Meeting Guide Divisi 2012 & Optical Materials May 20-24, 2012|Hilton o n A nnual Meetin nnual S t. L ouis atthe Ballpark| www .ceramics.org/gomd2012 S t. g L ouis, MO Welcome Letter Welcome to the 2012 Glass & Optical Materials Division Meeting! We have a record-setting number of talks and posters this year presented by leading glass science researchers from industry, governmental laboratories, and academic institutions from around the world. Divided into four broad symposia: Glass Science, Optical Materials and Devices, Cross-Cutting Topics, and a Festschrift to the Glass Research Career of Prof. Delbert E. Day sponsored by Mo-Sci and Missouri S&T, you will find talks covering the latest advances in glass science, the technology of optical materials, and a focused examination of the nature and properties of the amorphous state. Several special activities have been planned in addition to the outstanding technical program: • Renew acquaintances and get to know new faces within the GOMD community during the Welcome Reception held on Sunday from 5 to 7 pm. • Students will not want to miss the “Careers in Glass and Optical Materials: Panel Discussion for Students” event planned for Monday during lunchtime. • Special Award Lectures: The Stookey Lecture of Discovery Award (Monday morning), the George W. Morey Award (Tuesday morning), and the Norbert J. Kreidl Award for Young Scholars (Tuesday at noon) feature exceptional lectures by the honorees. • Continue your learning experience by attending the Poster Session on Monday evening, with detailed technical presentations and top materials science students competing in the student poster contest. • GOMD attendees are invited to be our guests and continue networking with their colleagues during the conference dinner on Tuesday evening. Prior to the conference, get a primer on glass science by attending the “Fundamentals of Glass Science and Technology” short course taught by Dr. Arun Varshneya of Saxon Glass Technologies. A separate registration fee is required to attend this course. Special thanks go to our sponsors including PPG Industries, Inc. for sponsoring the George W. Morey Award, Coe College and Corning Incorporated for sponsoring the Stookey Lecture of Discovery Award, SCHOTT North America for sponsoring lunch for the Norbert J. Kreidl Award for Young Scholars, and Corning Incorporated for the Student Poster Contest. We also thank Mo-Sci Corporation and Missouri S&T, Journal of Non-Crystalline Solids, the International Journal of Applied Glass Science, AdValue Technology and American Elements for their generous support. The Hilton St. Louis at the Ballpark is just steps away from Busch Stadium—home of the St. Louis Cardinals, the Gateway Arch, Edward Jones Dome—home of the St. Louis Rams, the riverfront, restaurants and all of St. Louis’ major attractions. Be sure to schedule some time for a visit to the Cathedral Basilica St. Louis which has the world’s largest collection of mosaic art. Other major attractions include Forest Park, one of the largest ur- ban parks in the country, approximately 500 acres larger than New York City’s Central Park. Forest Park is home to the Art Museum, Science Center, Zoo, Jewel Box greenhouse, History Museum, The Muny theatre, 7.5-mile biking, jogging and skating path, skating rink and lakes, all with free admission. The American Ceramic Society and the Glass & Optical Materials Division thank you for participating in this year’s meeting.

The 2012 Organizing Committee:

Juejun (JJ) Hu J. David Musgraves University of Delaware Clemson University Table of Contents Schedule-at-a-Glance ...... 2 Hotel Floorplan ...... 3 Award Lectures ...... 4 Careers in Glass and Optical Materials: Panel Discussion for Students ...... 6 Presenting Author List ...... 9–10

Final Program Monday Morning ...... 11–12 Monday Afternoon ...... 12–15 Tuesday Morning ...... 15–16 Tuesday Afternoon ...... 17–19 Wednesday Morning ...... 19–21 Wednesday Afternoon ...... 21–23 Thursday Morning ...... 23–24 Abstracts ...... 25 Author Index ...... 69

Glass & Optical Materials Division Officers

Chair Vice Chair John Ballato Shibin Jiang Clemson Research Park AMRL AdValue Technology, LLC

Chair-Elect Secretary Kelly Simmons-Potter Steve Feller University of Arizona Coe College

2012 Glass & Optical Materials Division Annual Meeting 1 Schedule At A Glance

Sunday – May 20, 2012 *Fundamentals of Glass Science & Technology Short Course 9:30 a.m. – 5 p.m. Gateway III Registration 3 p.m. – 7 p.m. Arch View Foyer Welcome Reception 5 p.m. – 7 p.m. Arch View Ballroom

Monday – May 21, 2012 Registration 7:30 a.m. – 5:30 p.m. Arch View Foyer Stookey Lecture of Discovery 8 a.m. – 9 a.m. Salons C&D Coffee Break 9 a.m. – 9:20 a.m. Arch View Foyer Concurrent Technical Sessions 9:20 a.m. – Noon Salons A-G, Grand Suites II & III Lunch On Your Own Noon – 1:20 p.m. Student Lunch Event Noon – 1:00 p.m. Lindbergh Concurrent Technical Sessions 1:20 p.m. – 5:20 p.m. Salons A-G, Grand Suites II & III *Fundamentals of Glass Science & Technology Short Course 1:30 p.m. – 5:00 p.m. Gateway III Coffee Break 3 p.m. – 3:20 p.m. Arch View Foyer Poster Setup 3 p.m. – 5 p.m. Arch View Ballroom GOMD General Business Meeting 5:45 p.m. – 6:30 p.m. Grand Suites II & III Poster Session 6:30 p.m. – 9 p.m. Arch View Ballroom

Tuesday – May 22, 2012 Registration 7:30 a.m. – 5 p.m. Arch View Foyer George W. Morey Award 8 a.m. – 9 a.m. Salons C&D Coffee Break 9 a.m. – 9:20 a.m. Arch View Foyer Concurrent Technical Sessions 9:20 a.m. – Noon Salons A-G, Grand Suites II & III Lunch On Your Own Noon – 1:20 p.m. Norbert J. Kreidl Award for Young Scholars Noon – 1:00 p.m. Salons C&D Concurrent Technical Sessions 1:20 p.m. – 6:00 p.m. Salons A-G, Grand Suites II & III Coffee Break 3 p.m. – 3:20 p.m. Arch View Foyer Conference Dinner 7 p.m. – 10 p.m. Arch View Ballroom

Wednesday – May 23, 2012 Registration 7:30 a.m. – 5 p.m. Arch View Foyer Concurrent Technical Sessions 8 a.m. – Noon Salons A-G, Grand Suites II & III Coffee Break 10 a.m. – 10:20 a.m. Arch View Foyer Lunch On Your Own Noon – 1:20 p.m. Concurrent Technical Sessions 1:20 p.m. – 6 p.m. Salons A-G, Grand Suites II & III Coffee Break 3 p.m. – 3:20 p.m. Arch View Foyer

Thursday – May 24, 2012 Registration 7:30 a.m. – Noon Arch View Foyer Concurrent Technical Sessions 8 a.m. – 12:20 p.m. Salons B, E-G, Grand Suites II & III Coffee Break 10 a.m. – 10:20 a.m. Arch View Foyer

*Fundamentals of Glass Science & Technology Short Course - pre-registration and an additional registration fee required.

2 2012 Glass & Optical Materials Division Annual Meeting Hilton St. Louis at the Ballpark Floor Plan

2012 Glass & Optical Materials Division Annual Meeting 3 Award Lectures

Monday, May 21 at 8 a.m. – Salons C & D

The Stookey Lecture of Discovery, named in honor of materials pioneer Dr. S. Donald Stookey, recognizes an individual's lifetime of innovative exploratory work or noteworthy contributions of outstanding research on new materials, phenomena, or processes involving glass, that have commercial significance or the potential for commercial impact.

Award Winner: John B. MacChesney, Bell Laboratories Fellow, retired Lecture Title: “ Development at Bell Laboratories” Sponsored by Corning Incorporated and Coe College

Tuesday, May 22 at 8 a.m. – Salons C & D

The George W. Morey Award recognizes new and original work in the field of glass science and technology. The criteria for winning the award is excellence in publication of work, either experimental or theoretical, done by an individual.

Award Winner: Edgar D. Zanotto, Professor, Vitreous Materials Laboratory, Federal University of São Carlos, Brazil Lecture Title: “Thirty-five Years of Glass Research – A tribute to my co-authors” Sponsored by PPG Industries Inc.

Tuesday, May 22 at 12 p.m. – Salons C & D

The Norbert J. Kreidl Award for Young Scholars recognizes excellence in research by graduate students in the fields of glass and optical materials. Dr. Kreidl’s lifelong mission was to enhance the education, achievement and advancement of young people.

Award Winner: Mathieu Bauchy, PhD Student, Université Pierre et Marie Curie Paris, France Lecture Title: “Topological Constraints and Rigidity of Network from Molecular Dynamics Simulations” Lunch* sponsored by SCHOTT North America Inc.

*Note: Lunch will be available at no cost on a first come, first served basis to attendees of the Kreidl Award Lecture.

4 2012 Glass & Optical Materials Division Annual Meeting Careers in Glass and Optical Materials: Panel Discussion for Students Monday, May 21th 12:00 p.m. – 1:00 p.m. A panel of speakers from the glass industry, start-up businesses, national laboratories, and academia will discuss their views on careers in glass science and technology. This is a chance for future glass researchers to hear about the opportu- nities open to them and to ask questions of experts in a wide range of research areas.

PANELISTS: Shibin Jiang, AdValue Technology Mark Davis, SCHOTT North America, Inc. Kathleen Richardson, Clemson University Jim Marra, Savannah River National Laboratory

Complimentary lunch courtesy of ACerS will be available on a first come, first served basis to students attending the panel discussion.

MEETING REGULATIONS The American Ceramic Society is a nonprofit scientific organization that facilitates whether in print, electronic or other media, including The American Ceramic Society’s the exchange of knowledge meetings and publication of papers for future reference. The website. By participating in the GOMD conference, you grant The American Ceramic Society owns and retains full right to control its publications and its meetings. The Society the right to use your name and photograph for such purposes. All postings Society has an obligation to protect its members and meetings from intrusion by others become the property of The American Ceramic Society. who may wish to use the meetings for their own private promotion purpose. Literature Registration Requirements: Attendance at any meeting of the Society shall be limited found not to be in agreement with the Society’s goals, in competition with Society services to duly registered persons. or of an offensive nature will not be displayed anywhere in the vicinity of the meeting. Disclaimer: Statements of fact and opinion are the responsibility of the authors alone Promotional literature of any kind may not be displayed without the Society’s permission and do not imply an opinion on the part of the officers, staff or members of The American and unless the Society provides tables for this purpose. Literature not conforming to this Ceramic Society. The American Ceramic Society assumes no responsibility for the policy or displayed in other than designated areas will be disposed. The Society will not statements and opinions advanced by the contributors to its publications or by the speakers permit unauthorized scheduling of activities during its meeting by any person or group at its programs; nor does The American Ceramic Society assume any liability for losses or when those activities are conducted at its meeting place in interference with its programs injuries suffered by attendees at its meetings. Registered names and trademarks, etc. used and scheduled activities. The Society does not object to appropriate activities by others in its publications, even without specific indications thereof, are not to be considered during its meetings if it is consulted with regard to time, place, and suitability. Any unprotected by the law. Mention of trade names of commercial products does not person or group wishing to conduct any activity at the time and location of the Society constitute endorsement or recommendations for use by the publishers, editors or authors. meeting must obtain permission from the Executive Director or Director of Meetings, Final determination of the suitability of any information, procedure or products for giving full details regarding desired time, place and nature of activity. use contemplated by any user, and the manner of that use, is the sole responsibility of the During oral sessions conducted during Society meetings, unauthorized photography, user. Expert advice should be obtained at all times when implementation is being videotaping and audio recording is prohibited. Failure to comply may result in the considered, particularly where hazardous materials or processes are encountered. removal of the offender from the session or from the remainder of the meeting. The American Ceramic Society plans to take photographs and video at the GOMD conference and reproduce them in GOMD educational, news or promotional materials, Copyright © 2012. The American Ceramic Society (www.ceramics.org). All rights reserved.

2012 Glass & Optical Materials Division Annual Meeting 5 Special Thanks to Our Sponsors For Their Generosity

Award Sponsors

Welcome Reception Sponsor Poster Session Sponsor

Endorsing Society

6 2012 Glass & Optical Materials Division Annual Meeting Save $125 when you register by June 15, 2012.

Sponsors: th International Congress on Ceramics 4 including 3rd Ceramic Leadership Summit Track

Shaping the Future of Ceramics ICC4 features these premier keynote and plenary speakers: – Maxine Savitz, General Manager (Retired), – Delbert Day, Founder, Mo-Sci Corp.; Honeywell Inc., and Vice President, Curators’ Professor Emeritus of Materials National Academy of Engineering Science and Engineering and Senior – Gary S. Calabrese, Senior Vice Investigator of the Graduate Center for President and Director, Photovoltaic Glass Materials Research, Missouri University Technologies, Corning Inc. of Science and Technology – Chi-Joon Choi, President and CEO, LCR – Mike Murray, Global Technical Director, Division, Samsung Electro-Mechanics Co. Engineered Materials Division, Morgan – John Tracy, Chief Technology Offi cer, Crucible Co. plc Boeing Co. – Yukio Sakabe, Senior Vice President – Athanasios Konstandopoulos, Chairman (Retired), Murata Manufacturing Co. of the Board, Centre for Research & Technology Hellas, and Director, Chemical – David S. Bem, Global R&D Director, Process Engineering Research Institute Dow Chemical Co. – Michael Holman, Research Director, Lux Research www.ceramics.org/icc4 July 15-19, 2012 | Sheraton Chicago Hotel & Towers | Chicago, Illinois, USA

The American Ceramic Society is pleased to host and organize ICC4. The International Ceramic Federation convenes the ICC every two years in cooperation with ACerS, the European Ceramic Society, the Ceramic Society of Japan and other ICF Member Societies. 'LASS/PTICAL-ATERIALS$IVISION!NNUAL-EETINGAT TH0ACIlC2IM#ONFERENCEON#ERAMIC rld of Scie o nc W e AND'LASS4ECHNOLOGY A *UNEn s(OTEL$EL#ORONADO 3AN$IEGO #! 53! PACRIM

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Name Date Time Room Page Number Name Date Time Room Page Number A Hoeland, W. 22-May 2:20PM Salon C 18 Abouraddy, A.F. 22-May 4:00PM Salon B 18 Holland, D. 23-May 1:20PM Grand Suites II & III 22 Affatigato, M. 21-May 11:20AM Salon A 11 Hoppe, U. 21-May 10:20AM Salon C 12 Agarwal, A.M. 22-May 9:20AM Salon B 16 Hosono, H. 21-May 9:20AM Grand Suites II & III 11 Ahmed, I. 22-May 2:40PM Salon C 19 Hsu, J. 21-May 4:40PM Grand Suites II & III 13 Aitken, B. 23-May 2:20PM Salons E, F, & G 21 Huang, L. 22-May 10:20AM Salons E, F, & G 15 Alvarez, C. 23-May 5:20PM Salon C 23 Hubert, M. 23-May 4:00PM Salon C 22 Anheier, N. 22-May 10:00AM Salon B 16 Hupa, L. 22-May 3:20PM Salon C 19 Arai, Y. 23-May 4:20PM Salon B 22 Arnold, C.B. 21-May 1:40PM Salon B 13 I Arnold, C.B. 22-May 10:40AM Salon B 16 Icenhower, J. 23-May 9:20AM Salon B 20 Inaba, S. 21-May 3:40PM Salons E, F, & G 12 B Inoue, H. 22-May 3:40PM Salons E, F, & G 17 Baker, B. 21-May 11:40AM Salons E, F, & G 11 Ballato, J. 22-May 2:20PM Salon B 18 J Ballato, J. 22-May 2:40PM Salon B 18 Jain, H. 22-May 4:00PM Salon C 19 Ballato, J. 22-May 4:40PM Salon B 18 Jain, H. 23-May 9:20AM Salon A 19 Ballato, J. 22-May 5:00PM Salon B 18 Jensen, K.F. 21-May 1:20PM Grand Suites II & III 13 Baltisberger, J.H. 24-May 8:00AM Grand Suites II & III 23 Jensen, K.F. 23-May 4:00PM Salon B 22 Barta, B. 23-May 4:40PM Salon C 23 Jiang, S. 24-May 8:40AM Salon B 23 Bauchy, M. 23-May 11:20AM Salon C 20 Johnson, J. 23-May 10:40AM Salons E, F, & G 19 Bauchy, Mathieu 22-May 12:00PM Salon C 16 Jung, S.B. 22-May 2:00PM Salon C 18 Benmore, C.J. 21-May 1:20PM Salons E, F, & G 12 Bischoff, C. 21-May 11:00AM Salons E, F, & G 11 K Bischoff, C. 23-May 5:20PM Salons E, F, & G 21 Kamitsos, E.I. 22-May 11:20AM Grand Suites II & III 16 Böhmer, R. 23-May 3:20PM Grand Suites II & III 22 Kana Kana, J. 21-May 2:00PM Grand Suites II & III 13 Bond, K. 21-May 4:00PM Grand Suites II & III 13 Karabulut, M. 22-May 5:00PM Salons E, F, & G 17 Boolchand, P. 23-May 9:00AM Salons E, F, & G 19 Kaseman, D.C. 21-May 4:20PM Salon C 14 Bornstein, K. 21-May 2:40PM Salons E, F, & G 12 Kelton, K.F. 24-May 9:00AM Salons E, F, & G 24 Busch, R. 23-May 8:40AM Salon A 19 Kieffer, J. 24-May 10:40AM Salon B 23 Kim, Y. 23-May 11:40AM Salons E, F, & G 19 C King, E.A. 23-May 2:40PM Salon A 21 Chakraborty, S. 21-May 9:20AM Salons E, F, & G 11 Kob, W. 22-May 1:20PM Salon A 17 Champagnon, B. 22-May 5:20PM Salon B 18 Koch, R.J. 21-May 10:20AM Salons E, F, & G 11 Champagnon, B. 22-May 9:20AM Salons E, F, & G 15 Komatsu, T. 21-May 11:00AM Salon A 11 Chen, G. 21-May 2:00PM Salons E, F, & G 12 Koontz, E. 23-May 3:40PM Salon A 21 Christensen, R. 21-May 10:20AM Grand Suites II & III 11 Koudelka, L. 24-May 11:00AM Salons E, F, & G 24 Christensen, R. 22-May 4:20PM Salons E, F, & G 17 Kovalskyy, A. 23-May 2:00PM Salons E, F, & G 21 Clark, A.N. 22-May 10:40AM Salons E, F, & G 15 Kozmidis-Petrovic, A.F. 22-May 5:00PM Salon A 17 Conradt, R. 22-May 5:20PM Salons E, F, & G 17 Kreski, P.K. 22-May 10:00AM Salon A 16 Cormier, L. 22-May 1:40PM Salons E, F, & G 17 Kroeker, S. 24-May 8:40AM Grand Suites II & III 23 Crawford, C.L. 23-May 1:40PM Salon B 21 Krol, D.M. 21-May 4:40PM Salon C 14 Krümpelmann, J. 22-May 2:20PM Grand Suites II & III 18 D Dash, P. 22-May 4:40PM Salons E, F, & G 17 L Davis, M.J. 23-May 9:40AM Salon C 20 Le Coq, D. 21-May 10:20AM Salon A 11 Dianov, E. 24-May 11:00AM Salon B 23 Le Roux, S. 22-May 2:00PM Salon A 17 Dongol, R. 21-May 4:40PM Salons E, F, & G 13 Le Roux, S. 22-May 2:40PM Salon A 17 Du, J. 21-May 10:40AM Salon C 12 Le Roux, S. 23-May 4:40PM Salons E, F, & G 21 Lee, S. 22-May 11:20AM Salons E, F, & G 16 E Lepry, W. 21-May 11:00AM Salon B 12 Ebert, W. 23-May 9:00AM Salon B 20 Li, C. 22-May 3:20PM Salons E, F, & G 17 Eckert, H. 22-May 10:40AM Grand Suites II & III 16 Li, W. 23-May 8:40AM Grand Suites II & III 20 Eckert, H. 23-May 11:00AM Grand Suites II & III 21 Lin, H. 22-May 11:00AM Salon B 16 Eckert, H. 23-May 3:20PM Salon C 22 Lin, P. 22-May 11:20AM Salon B 16 Erdmann, R.G. 23-May 2:00PM Salon A 21 Lin, P. 24-May 9:00AM Salon B 23 Lionel, M. 21-May 3:20PM Salon C 14 F Lotarev, S. 21-May 11:40AM Salon A 11 Feller, S. 24-May 11:00AM Grand Suites II & III 23 Lotarev, S. 24-May 10:20AM Salon B 23 Ferrand, K. 23-May 2:20PM Salon B 21 Loy, D.A. 21-May 11:20AM Salon B 12 Ferraro, P.A. 23-May 4:20PM Salon C 22 Lu, C. 21-May 2:40PM Salon A 13 Fortner, J.A. 23-May 2:00PM Salon B 21 Lucas, P. 23-May 3:20PM Salons E, F, & G 21 Fu, Q. 24-May 11:20AM Salons E, F, & G 24 Lumeau, J. 23-May 8:00AM Salon C 20 G M Galbraith, J. 23-May 5:00PM Salons E, F, & G 21 Maass, P. 22-May 10:00AM Grand Suites II & III 16 Gaudio, S.J. 23-May 11:40AM Salon A 19 MacChesney, John B. 21-May 8:00AM Salon C 11 George, J. 23-May 4:40PM Salon B 22 Mao, A. 21-May 10:40AM Salons E, F, & G 11 Gin, S. 23-May 8:00AM Grand Suites II & III 20 Marra, J. 21-May 5:00PM Grand Suites II & III 13 Gin, S. 23-May 9:40AM Salon B 20 Martin, S.W. 22-May 4:00PM Grand Suites II & III 18 Goel, A. 21-May 11:00AM Grand Suites II & III 12 Martin, S.W. 23-May 11:00AM Salon A 19 Goel, A. 21-May 4:20PM Grand Suites II & III 13 Massera, J. 24-May 10:40AM Salons E, F, & G 24 Goel, A. 22-May 4:20PM Salon C 19 Massiot, D. 23-May 2:00PM Grand Suites II & III 22 Golovchak, R. 23-May 11:00AM Salon C 20 Masuno, A. 21-May 11:20AM Grand Suites II & III 12 Gonzalo, J. 24-May 9:40AM Salon B 23 Matyas, J. 21-May 10:20AM Salon B 12 Greaves, N. 23-May 8:00AM Salon A 19 Mauro, J.C. 23-May 10:20AM Salon C 20 Guerette, M. 22-May 10:00AM Salons E, F, & G 15 McCloy, J. 21-May 10:00AM Salons E, F, & G 11 Guery, G. 21-May 9:40AM Salons E, F, & G 11 Micoulaut, M. 22-May 4:20PM Salon A 17 Gunasekera, K. 23-May 9:40AM Salons E, F, & G 19 Micoulaut, M. 23-May 8:00AM Salons E, F, & G 19 Guo, X. 23-May 3:20PM Salon A 21 Mogus-Milankovic, A. 21-May 11:00AM Salon C 12 Molières, E. 23-May 2:40PM Salon B 22 H Monteiro, A. 24-May 11:40AM Salons E, F, & G 24 Habasaki, J. 22-May 1:20PM Grand Suites II & III 18 Moore, L. 21-May 10:00AM Salon A 11 Han, K. 23-May 5:00PM Salon B 22 Mountjoy, G. 22-May 11:20AM Salon A 16 Harrison, M. 23-May 5:20PM Salon B 22 Mountjoy, G. 22-May 3:20PM Salon A 17 Hill, R.G. 22-May 1:20PM Salon C 18 Mueller, K. 23-May 10:20AM Salon B 20 Hill, R.G. 24-May 10:20AM Salons E, F, & G 24 Mugoni, C. 22-May 2:00PM Grand Suites II & III 18

2012 Glass & Optical Materials Division Annual Meeting 9 Presenting Author List

Name Date Time Room Page Number Name Date Time Room Page Number Munhollon, T. 23-May 4:00PM Salon A 21 Solis, J. 21-May 1:20PM Salon A 13 Murphy, K. 23-May 11:00AM Salon B 20 Stebbins, J.F. 23-May 4:40PM Grand Suites II & III 22 Musgraves, J. 23-May 4:00PM Salons E, F, & G 21 Stone, A. 21-May 2:00PM Salon A 13 Strachan, D. 23-May 9:00AM Grand Suites II & III 20 N Su, X. 21-May 10:00AM Grand Suites II & III 11 Neeway, J.J. 23-May 1:20PM Salon B 21 Swarnakar, A.K. 22-May 4:40PM Grand Suites II & III 18 Swarnakar, A.K. 23-May 5:20PM Grand Suites II & III 22 O Ohkubo, T. 21-May 3:40PM Grand Suites II & III 13 T Takada, A. 22-May 2:20PM Salon A 17 P Tandia, A. 22-May 9:20AM Salon A 16 Pandey, A.K. 21-May 2:20PM Salon B 13 Tang, Z. 22-May 4:00PM Salons E, F, & G 17 Pandey, P.C. 21-May 2:40PM Salon B 13 Tao, G. 22-May 2:00PM Salon B 18 Pavlacka, R.J. 23-May 5:40PM Salon C 23 Teki, R. 23-May 3:40PM Salon B 22 Pierce, E. 23-May 8:00AM Salon B 19 Terashima, T. 21-May 11:20AM Salon C 12 Ponader, C.W. 21-May 11:20AM Salons E, F, & G 11 Thompson, L.M. 23-May 11:40AM Grand Suites II & III 21 Pradel, A. 23-May 10:20AM Grand Suites II & III 20 Tomozawa, M. 22-May 3:20PM Grand Suites II & III 18 Prakash, A. 22-May 4:40PM Salon C 19 Trachenko, K. 23-May 4:20PM Salon A 21 Prokhorenko, O.A. 21-May 10:40AM Grand Suites II & III 12 Trott, C.R. 22-May 10:40AM Salon A 16 Prokhorenko, O.A. 22-May 5:20PM Salon A 17 Troy, N. 21-May 2:20PM Salon A 13 R V Rani, N. 23-May 3:20PM Salon B 22 Vanhoutte, M. 24-May 9:20AM Salon B 23 Ray, C.S. 24-May 8:20AM Salons E, F, & G 24 Vienna, J. 21-May 3:20PM Grand Suites II & III 13 Reis, R.M. 24-May 9:40AM Salons E, F, & G 24 Vignarooban, K. 22-May 2:00PM Salons E, F, & G 17 Rekhson, S.M. 23-May 10:20AM Salon A 19 Vigouroux, H. 23-May 5:00PM Salon C 23 Riley, B.J. 21-May 10:00AM Salon B 12 Vlcek, M. 23-May 1:20PM Salons E, F, & G 21 Rouxel, T. 23-May 10:20AM Salons E, F, & G 19 Vogel, M. 23-May 4:00PM Grand Suites II & III 22 Rouxel, T. 23-May 1:20PM Salon A 21 Rufflé, B. 21-May 4:20PM Salons E, F, & G 12 W Rufflé, B. 23-May 2:00PM Salon C 22 Weber, R. 21-May 3:20PM Salons E, F, & G 12 Rufflé, B. 23-May 9:00AM Salon C 20 Widgeon, S. 23-May 11:20AM Salons E, F, & G 19 Ryan, J. 23-May 11:20AM Salon B 20 Wondraczek, L. 23-May 1:20PM Salon C 22 Rygel, J.L. 21-May 5:00PM Salon C 14 Wright, A.C. 21-May 2:20PM Salons E, F, & G 12 Wright, A.C. 21-May 9:40AM Salon C 12 S Saiyasombat, C. 23-May 8:40AM Salon C 20 X Sanghera, J.S. 22-May 1:20PM Salon B 18 Xiang, Y. 22-May 4:00PM Salon A 17 Sanghera, J.S. 24-May 8:00AM Salon B 23 Scherer, C. 22-May 4:40PM Salon A 17 Y Schreiber, D.K. 23-May 11:40AM Salon B 20 Youngman, R. 21-May 4:00PM Salon C 14 Sebeck, K. 22-May 11:00AM Salon A 16 Youngman, R. 24-May 10:20AM Grand Suites II & III 23 Sen, S. 22-May 2:40PM Salons E, F, & G 17 Yuan, F. 22-May 11:40AM Salon A 16 Sen, S. 23-May 8:40AM Salons E, F, & G 19 Yuhas, B.D. 21-May 9:20AM Salon B 12 Sen, S. 24-May 10:20AM Grand Suites II & III 23 Serbena, F.C. 22-May 1:20PM Salons E, F, & G 17 Z Shelby, J.E. 22-May 9:20AM Grand Suites II & III 16 Zanotto, E.D. 24-May 8:00AM Salons E, F, & G 24 Shoulders, T. 23-May 4:20PM Salons E, F, & G 21 Zanotto, Edgar D. 22-May 8:00AM Salon C 15 Sidebottom, D.L. 22-May 5:00PM Grand Suites II & III 18 Zapol, P. 23-May 8:40AM Salon B 20 Singh, V. 22-May 10:20AM Salon B 16 Zhang, T. 21-May 11:40AM Grand Suites II & III 12 Skinner, L.B. 22-May 2:20PM Salons E, F, & G 17 Zhou, Z. 22-May 10:20AM Salon A 16 Smedskjaer, M.M. 22-May 11:00AM Salons E, F, & G 16 Zou, Y. 21-May 1:20PM Salon B 13 Smedskjaer, M.M. 23-May 9:20AM Salon C 20 Zou, Y. 21-May 2:20PM Grand Suites II & III 13 Smektala, F. 22-May 3:20PM Salon B 18 Zwanziger, J. 24-May 9:20AM Grand Suites II & III 23 Smelser, C.W. 21-May 9:20AM Salon A 11 Zwanziger, J. W. 21-May 4:00PM Salons E, F, & G 12 Solis, J. 21-May 10:40AM Salon A 11

Poster Presenters Name Date Time Room Page Number Name Date Time Room Page Number Bagga, R. 21-May 6:30PM Arch View Ballroom 15 Maeda, T. 21-May 6:30PM Arch View Ballroom 15 Bradt, R.C. 21-May 6:30PM Arch View Ballroom 14 Marasinghe, K. 21-May 6:30PM Arch View Ballroom 15 Bragatto, C.B. 21-May 6:30PM Arch View Ballroom 14 Mellott, N.P. 21-May 6:30PM Arch View Ballroom 15 Buchheit, E.M. 21-May 6:30PM Arch View Ballroom 14 Morin, E. 21-May 6:30PM Arch View Ballroom 14 Cabral, A.A. 21-May 6:30PM Arch View Ballroom 15 Mugoni, C. 21-May 6:30PM Arch View Ballroom 15 Cheng, X. 21-May 6:30PM Arch View Ballroom 14 Pan, Z. 21-May 6:30PM Arch View Ballroom 15 ChunTeng, L. 21-May 6:30PM Arch View Ballroom 15 Pérez, J. 21-May 6:30PM Arch View Ballroom 15 Faeghi nia, A. 21-May 6:30PM Arch View Ballroom 15 Pierce, D. 21-May 6:30PM Arch View Ballroom 15 Gallo, L. 21-May 6:30PM Arch View Ballroom 14 Pierce, E. 21-May 6:30PM Arch View Ballroom 15 George, J. 21-May 6:30PM Arch View Ballroom 14 Prasai, B. 21-May 6:30PM Arch View Ballroom 14 Ghussn, L. 21-May 6:30PM Arch View Ballroom 15 Prokhorenko, O.A. 21-May 6:30PM Arch View Ballroom 15 Gilbert, M. 21-May 6:30PM Arch View Ballroom 14 Reis, S.T. 21-May 6:30PM Arch View Ballroom 14 Goetschius, K. 21-May 6:30PM Arch View Ballroom 14 Saiyasombat, C. 21-May 6:30PM Arch View Ballroom 15 Gonzalo, J. 21-May 6:30PM Arch View Ballroom 15 Sanders, K.J. 21-May 6:30PM Arch View Ballroom 14 Gulbiten, O. 21-May 6:30PM Arch View Ballroom 14 Savytskyy, D. 21-May 6:30PM Arch View Ballroom 15 Harper, T.A. 21-May 6:30PM Arch View Ballroom 14 Schnell, S. 21-May 6:30PM Arch View Ballroom 14 Huang, P. 21-May 6:30PM Arch View Ballroom 14 Smith, C. 21-May 6:30PM Arch View Ballroom 14, 15 Knorr, B. 21-May 6:30PM Arch View Ballroom 15 Storek, M. 21-May 6:30PM Arch View Ballroom 15 Kolan, K. 21-May 6:30PM Arch View Ballroom 15 Tao, G. 21-May 6:30PM Arch View Ballroom 15 Korngruen, M. 21-May 6:30PM Arch View Ballroom 14 Velez, M. 21-May 6:30PM Arch View Ballroom 15 Kreski, P.K. 21-May 6:30PM Arch View Ballroom 14 Vieira, H. 21-May 6:30PM Arch View Ballroom 15 Lee, P. 21-May 6:30PM Arch View Ballroom 15 Vigouroux, H. 21-May 6:30PM Arch View Ballroom 14 Liu, S. 21-May 6:30PM Arch View Ballroom 15 Walder, B.J. 21-May 6:30PM Arch View Ballroom 14 Liu, X. 21-May 6:30PM Arch View Ballroom 14 Widgeon, S. 21-May 6:30PM Arch View Ballroom 14 Ma, L. 21-May 6:30PM Arch View Ballroom 14 Yu, T. 21-May 6:30PM Arch View Ballroom 14

10 2012 Glass & Optical Materials Division Annual Meeting Final Program Monday, May 21, 2012

Monday, May 21, 2012 Symposium II: Optical Materials & Devices Stookey Lecture of Discovery Award Session 2: Photosensitivity and Laser Room: Salon C Modification of Glasses I 8:00 AM Room: Salon A Optical Fiber Development at Bell Laboratories Session Chair: Denise Krol, University of California, Davis John B. MacChesney*, Bell Laboratories Fellow, retired 9:20 AM (GOMD-SII-008-2012) Temperature Stability Studies of Ultrafast Symposium I: Glass Science Infrared Laser Induced Index Change for Harsh Environment Fiber Based Sensors (Invited) C. W. Smelser*, D. Grobnic, R. B. Walker, S. J. Mihailov, Communications Research Centre, Session 1: Glass Structure and Properties I Canada Room: Salons E, F, & G 10:00 AM Session Chair: Randall Youngman, Corning Incorporated (GOMD-SII-009-2012) Effect of Composition and Process on the 9:20 AM Transient Absorption of ArF Excimer Laser-Exposed Silica (GOMD-SI-001-2012) Observation of three elastic phases in heavy L. Moore*, C. Smith, S. Schiefelbein, K. Hrdina, J. Moll, Corning Incorporated, USA metal oxide glasses 10:20 AM P. Boolchand, S. Chakraborty*, Univ of Cincinnati, USA; M. Malki, University of Orleans, France; M. Micoulaut, University of Paris 6, France (GOMD-SII-010-2012) Direct writing of waveguides by femtosecond laser filamentation 9:40 AM D. Le Coq*, O. Caulier, University of Littoral côte d’Opale, France; L. Calvez, University of (GOMD-SI-002-2012) New understanding in TeO2-based glass Rennes 1, France; E. Bychkov, P. Masselin, University of Littoral côte d’Opale, France structure by Hyper-Raman/Hyper-Rayleigh for the measure of 10:40 AM Raman gain G. Guery*, clemson university, USA; M. Dussauze, ISM, France; T. Cardinal, ICMCB, France; F. (GOMD-SII-011-2012) Refractive Index Modification Mechanisms Adamietz, V. Rodriguez, ISM, France; K. Richardson, clemson university, USA in a Doped Phosphate Glass Irradiated with Ultrashort Laser Pulses Analyzed by Micro-Photoluminescence 10:00 AM A. Ferrer, CSIC, Spain; D. Jaque, Facultad de Ciencias-UAM, Spain; J. Siegel, A. Ruiz de la (GOMD-SI-003-2012) Role of chloride in TeO2-PbO-XCl glass Cruz, J. Solis*, CSIC, Spain structure 11:00 AM J. McCloy*, B. J. Riley, C. Windisch, C. P. Rodriguez, J. Vienna, Pacific Northwest National Laboratory, USA (GOMD-SII-012-2012) Laser Patterning of Planar Crystals with High Orientation in Oxide Glass 10:20 AM T. Ko m a t s u *, F. Suzuki, K. Ogawa, T. Honma, Nagaoka University of Technology, Japan (GOMD-SI-004-2012) Structure-Terahertz Properties Relationship in Tellurite Glasses 11:20 AM A. A. Monteiro, UNESP-Univ. Estadual Paulista, Brazil; R. J. Koch*, Alfred University, USA; K. (GOMD-SII-013-2012) Laser Induced Modification in Borates and Yukimitu, UNESP-Univ. Estadual Paulista, Brazil; S. K. Sundaram, Alfred University, USA Vanadates M. Affatigato*, B. Franta, T. Ahline, S. Yosinski, R. Dongol, W. Lubberden, S. Feller, Coe 10:40 AM College, USA; F. Rocca, G. Dalba, R. Grisenti, Universita di Trento, Italy (GOMD-SI-005-2012) Synthesis and Structure of ternary chalcogenide glasses in the system BaSe-Ga2Se3-GeSe2 11:40 AM A. Mao*, S. Sen, University of California at Davis, USA; B. Aitken, Corning Incorporated, USA (GOMD-SII-014-2012) Laser-induced nanostructuring of nickel- doped alkali gallium silicogermanate glasses 11:00 AM S. Lotarev*, A. Lipatyev, N. Golubev, V. Sigaev, D. Mendeleyev University of Chemical (GOMD-SI-006-2012) NMR Investigation of Mixed Glass Former Technology of Russia, Russian Federation

Glasses in the Na2S+GeS2+P2S5 System C. Bischoff*, K. Schuller, S. W. Martin, Iowa State University, USA Symposium III: Cross-Cutting Topics 11:20 AM (GOMD-SI-007-2012) NMR and Raman Studies of Cesium Gallo- Session 1: Materials for Fuel Cells and Energy aluminate Glasses C. W. Ponader*, R. E. Youngman, L. K. Cornelius, A. J. Ellison, Corning Incorporated, USA Storage Room: Grand Suites II & III 11:40 AM Session Chairs: Barrett Potter, University of Arizona; Kelly Simmons- (GOMD-SI-008-2012) Structure and Property Studies of Alkali Potter, University of Arizona Borovanadate and Silicovanadate Glasses B. Baker*, B. Dahal, B. Pollpeter, William Jewell College, USA; J. North, J. Maldonis, C. Parrish, 9:20 AM M. Affatigato, S. Feller, Coe College, USA; S. Kroeker, V. Michaelis, University of Manitoba, Canada (GOMD-SIII-001-2012) An Electride Glass- a semiconducting calcium aluminate glass based on interstitial electron (Invited) H. Hosono*, Tokyo Institute of Technology, Japan 10:00 AM

(GOMD-SIII-002-2012) Characterization of BaTiO3 glass- ceramics/barium titanate composites for high energy storage capacitors X. Su*, D. B. Chrisey, M. Tomozawa, Rensselaer Polytechnic Institute, USA 10:20 AM (GOMD-SIII-003-2012) Glass and β” Alumina Ceramic Composites for the Sodium-Sulfur Battery R. Christensen*, Iowa State University, USA

*Denotes Presenter

2012 Glass & Optical Materials Division Annual Meeting 11 Final Program Monday, May 21, 2012

10:40 AM 10:20 AM (GOMD-SIII-004-2012) Lead-free Sealing Glass: Low Tflow & Low CTE (GOMD-SIV-014-2012) The structural behavior of Nb in Nb2O5- O. A. Prokhorenko*, Laboratory of Glass Properties, USA NaPO3 glasses by X-ray and neutron diffraction U. Hoppe*, Universität Rostock, Germany; L. Delevoye, L. Montagne, Université des Sciences 11:00 AM et Technologies de Lille, France; M. von Zimmermann, Deutsches Elektronen-Synchrotron (GOMD-SIII-005-2012) Rare-earth containing glass-ceramic DESY, Germany; A. Hannon, Rutherford Appleton Laboratory, United Kingdom sealants for solid oxide fuel cells 10:40 AM A. Goel*, Pacific Northwest National Laboratory, USA; J. M. Ferreira, University of Aveiro, Portugal (GOMD-SIV-015-2012) Structure of cerium aluminophosphate glasses: diffraction studies and molecular dynamics simulations 11:20 AM J. Du*, L. Kokou, University of North Texas, USA; J. Rygel, C. Pantano, the Penn State University, USA; L. Skinner, C. Benmore, Argonne National Laboratory, USA (GOMD-SIII-006-2012) Optical properties of La2O3-Nb2O5-MOx glasses prepared by containerless processing 11:00 AM A. Masuno*, The University of Tokyo, Japan; K. Yoshimoto, The University of Tokyo, Japan; H. Inoue, The University of Tokyo, Japan; Y. Watanabe, The University of Tokyo, Japan (GOMD-SIV-016-2012) Investigation of electrical properties of iron phosphate glasses in Croatia 11:40 AM A. Mogus-Milankovic*, A. Santic, L. Pavic, Ruder Boskovic Institute, Croatia (GOMD-SIII-007-2012) Development of Sealing Glass for Solid Oxide Fuel Cells- Chemical Stability of Sr-containing Crystalline 11:20 AM T. Zhang*, Q. Zou, D. Tang, Fuzhou University, China; H. Yang, National United University, (GOMD-SIV-017-2012) Water diffusion into phosphate glasses Taiwan T. Terashima*, M. Tomozawa, Rensselaer Polytechnic Institute, USA

Session 4: Liquid Synthesis and Sol-gel Derived Symposium I: Glass Science Materials I Room: Salon B Session 1: Glass Structure and Properties II Session Chairs: Brian Riley, Pacific Northwest National Laboratory; Room: Salons E, F, & G David Musgraves, Clemson University Session Chair: Sabyasachi Sen, University of California, Davis 9:20 AM 1:20 PM (GOMD-SIII-035-2012) Unique Opportunities in Chalcogels: Porous (GOMD-SI-009-2012) Characterizing Amorphous Synthetic and Semiconducting Metal-Chalcogenide Aerogels (Invited) Natural Spider Silk Fibers Using X-ray Diffraction (Invited) M. Kanatzidis, B. D. Yuhas*, S. Bag, Northwestern University, USA C. J. Benmore*, Argonne National Lab, USA; F. Teulé, Utah State University, USA; W. Weber, Arizona State University, USA; R. Lewis, Utah State University, USA; J. L. Yarger, Arizona State 10:00 AM University, USA (GOMD-SIII-036-2012) Chalcogen-based aerogels as sorbents for 2:00 PM radioiodine B. J. Riley*, W. C. Lepry, J. Chun, D. M. Strachan, Pacific Northwest National Laboratory, USA (GOMD-SI-010-2012) Mechanical Property of Nanoporous Glasses Characterized by X-ray Scattering 10:20 AM S. Dong, M. Sundararajan, G. Chen*, Ohio University, USA (GOMD-SIII-037-2012) -functionalized silica aerogels for 2:20 PM effective capture and safe storage of gaseous radioiodine (Invited) J. Matyas*, G. E. Fryxell, M. J. Robinson, PNNL, USA (GOMD-SI-011-2012) What can Neutron Scattering Techniques tell us about the Structure and Dynamics of Inorganic Glasses? 11:00 AM A. C. Wright*, University of Reading, United Kingdom (GOMD-SIII-038-2012) High-Halide Minerals as a Salt Waste Form 2:40 PM W. Lepry*, J. Crum, B. Riley, J. Matyas, Pacific Northwest National Laboratory, USA (GOMD-SI-012-2012) Formation of Ga-As colloids in Glasses 11:20 AM K. Bornstein*, S. K. Sundaram, Alfred University, USA (GOMD-SIII-039-2012) Sol-gel synthesis and processing of 3:00 PM polysilsesquioxane coatings using size exclusion and sintering (Invited) Break D. A. Loy*, The University of Arizona, USA 3:20 PM Symposium IV: Festschrift to the Glass (GOMD-SI-013-2012) Glassy and Amorphous Drugs R. Weber*, Materials Development, Inc., USA; C. J. Benmore, Argonne National Laboratory, Research Career of Prof. Delbert E. Day USA; A. N. Tailor, S. K. Tumber, Materials Development, Inc., USA; C. A. Rey, Charles Rey, Inc, USA; L. S. Taylor, S. R. Byrn, Purdue University, USA; J. L. Yarger, B. Cherry, Arizona State University, USA Session 2: Phosphate Glasses: Their Structures, Properties and Applications I 3:40 PM (GOMD-SI-014-2012) Structural study on anisotropic phosphate Room: Salon C glass by polarized Raman spectroscopy Session Chair: Richard Brow, Missouri S&T S. Inaba*, S. Ito, Tokyo Institute of Technology, Japan 9:20 AM 4:00 PM Opening remarks on Delbert Day’s contributions to phosphate (GOMD-SI-015-2012) Mixed alkali effect on the hardness and glass science and technology cracking of glass by Vickers indentation Richard K. Brow, Missouri S&T A. Mohajerani, J. W. Zwanziger*, Dalhousie University, Canada 9:40 AM 4:20 PM (GOMD-SIV-013-2012) The Atomic and Magnetic Structure and (GOMD-SI-017-2012) 3D μ-Brillouin mapping of a Vickers Dynamics of Iron Phosphate Glasses (Invited) indentation in a soda-lime silicate glass A. C. Wright*, University of Reading, United Kingdom H. Tran, University of Montpellier II, France; D. Vandembroucq, ESPCI/Paris 6/Paris 7, France; B. Rufflé*, University of Montpellier II, France

12 2012 Glass & Optical Materials Division Annual Meeting Final Program Monday, May 21, 2012

4:40 PM Session 1: Nuclear Waste Glass Chemistry and (GOMD-SI-018-2012) Crack Growth in Photomultiplier Tube Processing Glasses for Neutrino Detection R. Dongol*, S. K. Sundaram, Alfred University, USA; M. Diwan, Brookhaven National Room: Grand Suites II & III Laboratory, USA Session Chairs: James Marra, Savannah River National Laboratory; John Vienna, PNNL Symposium II: Optical Materials & Devices 3:20 PM (GOMD-SIII-011-2012) A Roadmap to High Level Waste Session 2: Photosensitivity and Laser in the U.S J. Vienna*, Pacific Northwest National Laboratory, USA; J. Marra, Savannah River National Modification of Glasses II Laboratory, USA Room: Salon A 3:40 PM Session Chair: Mario Affatigato, Coe College (GOMD-SIII-012-2012) Structural studies of nuclear waste form 1:20 PM glasses and glass ceramics by solid-state NMR and Raman (GOMD-SII-015-2012) Optimization of Energy Deposition in spectroscopies Femtosecond Laser Processing of Dielectrics Using Plasma T. Ohkubo*, Y. Iwadate, Chiba University, Japan Imaging Techniques (Invited) 4:00 PM J. Solis*, Instituto de Optica-CSIC, Spain (GOMD-SIII-013-2012) Sulfate Retention in Simulated Nuclear 2:00 PM Waste Glasses K. Bond*, S. Sundaram, Alfred University, USA; K. M. Fox, J. W. Amoroso, Savannah River (GOMD-SII-016-2012) Aberration correction and formation of National Laboratory, USA complex crystal geometries by spatial light modulation of femtosecond laser 4:20 PM A. Stone*, Lehigh University, USA; M. Sakakura, Y. Shimotsuma, K. Miura, Kyoto University, Japan; V. Dierolf, H. Jain, Lehigh University, USA (GOMD-SIII-014-2012) Rhenium solubility in borosilicate nuclear waste glasses 2:20 PM A. Goel*, B. J. Riley, M. Liezers, C. F. Windisch, J. S. McCloy, M. J. Schweiger, C. P. Rodriguez, P. Hrma, D. Kim, Pacific Northwest National Laboratory, USA (GOMD-SII-017-2012) Creating Optical Waveguides in Glass with Femtosecond Cylindrical Vector Beams 4:40 PM N. Troy*, University of California Davis, USA; H. Zhang, J. I. Dijkhuis, Utrecht University, Netherlands; D. M. Krol, University of California Davis, USA (GOMD-SIII-015-2012) The Corrosion of Inconel 690 and Inconel 693 in an Iron Phosphate Melt Containing 26 wt% of a Simulated 2:40 PM Low Activity Waste J. Hsu*, J. W. Newkirk, Missouri University of Science and Technology, USA; C. Kim, Mo-Sci (GOMD-SII-018-2012) A Phenomenological model on photo- Corporation, USA; C. S. Ray, R. K. Brow, M. E. Schlesinger, D. E. Day, Missouri University of induced surface structure in Arsenic Sulfide Science and Technology, USA C. Lu*, C. Arnold, Princeton University, USA 5:00 PM (GOMD-SIII-016-2012) Cold Crucible Induction Melter Technology as Symposium III: Cross-Cutting Topics a Tool to Increase Waste Loading for High Level Radioactive Wastes J. Marra*, Savannah River National Laboratory, USA Session 1: Solar Energy Materials Room: Grand Suites II & III Session 4: Liquid Synthesis and Sol-gel Derived Session Chairs: Barrett Potter, University of Arizona; Kelly Simmons- Potter, University of Arizona Materials II Room: Salon B 1:20 PM Session Chairs: Brian Riley, Pacific Northwest National Laboratory; (GOMD-SIII-008-2012) Material requirements for long-term stable David Musgraves, Clemson University Dye-sensitized Solar Modules (Invited) K. F. Jensen*, W. Veurman, H. Brandt, R. Loayza-Aguirre, K. Bialecka, A. Hinsch, Fraunhofer 1:20 PM Institute for Solar Energy Systems ISE, Germany (GOMD-SIII-040-2012) Physio-chemical properties of spin-coated 2:00 PM As2Se3 chalcogenide glass thin films Y. Z o u *, H. Lin, O. Ogbuu, University of Delaware, USA; S. Novak, Clemson University, USA; J. (GOMD-SIII-009-2012) Engineering CdTe-ZnO nanocomposites for Wilkinson, Clemson University, USA; J. Musgraves, Clemson University, USA; K. Richardson, photovoltaic device applications Clemson University, USA; J. Hu, University of Delaware, USA J. Kana Kana*, R. Beal, B. Potter, University of Arizona, USA 1:40 PM 2:20 PM (GOMD-SIII-041-2012) Materials properties and performance of (GOMD-SIII-010-2012) Optical Absorption Enhancement in Thin solution processed arsenic sulfide glass in optical and photonic Film Solar Cells Using High-index Glass Light Trapping Backside applications (Invited) Structures C. B. Arnold*, Princeton University, USA Y. Zou*, J. Hu, H. Lin, University of Delaware, USA 2:20 PM 2:40 PM (GOMD-SIII-042-2012) Investigation and electrocatalytic Break application of Prussian blue-Palladium nanocomposite P. C. Pandey, A. K. Pandey*, D. S. Chauhan, Institute of Technology, Banaras Hindu University, India

2:40 PM (GOMD-SIII-043-2012) Application of alkoxysilane-derived gold nanoparticles in sensitive determination of glucose P. C . P a n d e y *, D. S. Chauhan, Institute of Technology, Banaras Hindu University, India 3:00 PM Break

2012 Glass & Optical Materials Division Annual Meeting 13 Final Program Monday, May 21, 2012

Symposium IV: Festschrift to the Glass (GOMD-SP-P009-2012) Dynamic Light Scattering Studies on Structural Effects on the Dynamics of Potassium-modified Borate Research Career of Prof. Delbert E. Day Glass S. Schnell*, Creighton University, USA Session 2: Phosphate Glasses: Their Structures, (GOMD-SP-P010-2012) Synthesis and characterization of SnF2- Properties and Applications II SnO-P2O5 glasses doped with rare earth metals and organic dye Room: Salon C T. A. Harper*, A. Kovalskyy, C. Brennan, Austin Peay State University, USA Session Chair: Richard Brow, Missouri S&T (GOMD-SP-P011-2012) Effect of phosphate speciation on corrosion behavior of P O -doped sodium borosilicate glasses 3:20 PM 2 5 X. Cheng*, R. Brow, G. Chen, Missouri University of Science and Technology, USA (GOMD-SIV-018-2012) On the reticulation degree of phosphate glass networks : a solid-state NMR approach (Invited) (GOMD-SP-P012-2012) Calcium phosphate layer formation on bio- M. Lionel*, L. Delevoye, G. Tricot, F. Mear, J. Amoureux, J. Trebosc, P. Rajbandhari, T. Lemesle, active borate glass microspheres in aqueous phosphate solutions N. Forler, F. Vasconcelos, University of Lille, France J. George*, R. Brow, Missouri University of Science and Technology, USA 4:00 PM (GOMD-SP-P013-2012) The development of ‘ferrous blue’ silicate (GOMD-SIV-019-2012) Impact of P on Trivalent Network-Forming glasses E. M. Buchheit*, R. K. Brow, Missouri S&T, USA Cations R. Youngman*, B. Aitken, Corning Incorporated, USA (GOMD-SP-P014-2012) Aqueous Corrosion of Polyphosphate Glasses 4:20 PM C. Smith*, Missouri University of Science and Technology, USA; R. K. Brow, Missouri University (GOMD-SIV-020-2012) Quantification of structural disorder in zinc of Science and Technology, USA phosphate glasses: Results from 31P 2D Phase Adjusted Spinning (GOMD-SP-P015-2012) Dissolution behavior of alkali-alkaline earth Sideband (PASS) NMR borate glasses D. C. Kaseman*, S. Sen, University of California Davis, USA M. Gilbert*, K. Goetschius, R. Brow, Missouri University of Science and Technology, USA 4:40 PM (GOMD-SP-P016-2012) Experimental and Theoretical Studies of (GOMD-SIV-021-2012) Femtosecond laser writing of waveguides in Structural Properties of Ag doped Ge-Sb-Te Thin Films zinc phosphate glasses B. Prasai*, M. Kordesch, D. Drabold, G. Chen, Ohio University, USA L. B. Fletcher, N. Troy, University of California, Davis, USA; S. T. Reis, R. K. Brow, Missouri 29 University of Science and Technology, USA; D. M. Krol*, University of California, Davis, USA (GOMD-SP-P017-2012) Si natural abundance MAFCPMG NMR analysis of anionic species in BaSi2O5 glass 5:00 PM K. J. Sanders*, E. G. Keeler, The Ohio State University, USA; J. H. Baltisberger, Berea College, (GOMD-SIV-022-2012) Irradiation Induced Defects in Cerium USA; P. J. Grandinetti, The Ohio State University, USA Aluminophosphate Glasses (GOMD-SP-P018-2012) Enhancing Sensitivity of Slow MAS J. L. Rygel*, C. G. Pantano, The Pennsylvania State University, USA; J. Du, The University of North Texas, USA Correlation Experiments on K2Si4O9 glass using PIETA B. J. Walder*, E. G. Keeler, The Ohio State University, USA; J. H. Baltisberger, Berea College, USA; P. J. Grandinetti, The Ohio State University, USA Posters and Student Poster Competition (GOMD-SP-P020-2012) Multi-technique Investigation of Ion- Exchanged Silicate and Aluminosilicate Glasses Room: Arch View Ballroom P. K . K r e s k i *, A. Cormack, A. K. Varshneya, Alfred University, USA 6:30 PM (GOMD-SP-P021-2012) Effect of on the temperature dependence of photoconductivity in As2S3 films (GOMD-SP-P001-2012) Modulated DSC analysis of structure and W. R. Heffner, Lehigh University, USA; M. Korngruen*, Rowan University, USA; A. Kovalskyy, relaxation in arsenic selenide and germanium selenide glasses Austin Peay State University, USA; N. Ward, Oakwood University, USA O. Gulbiten*, P. Lucas, University of Arizona, USA (GOMD-SP-P037-2012) Multi Scale Studies of LiNbO3 Silicate (GOMD-SP-P002-2012) MgO-Al2O3-SiO2 glass-ceramics for Glass-Ceramic ballistic protection H. Vigouroux*, E. Fargin, ICMCB, France; B. Le Garrec, CEA, France; M. Dussauze, F. L. Gallo*, E. Zanotto, A. Rodrigues, Universidade Federal de São Carlos, Brazil Adamietz, V. Rodriguez, ISM, France (GOMD-SP-P003-2012) Structural Effects of Varying Quench Rates (GOMD-SI-P022-2012) Shattering (Exploding) Glass Cookware in Ba, Ca, La, Y Boroaluminosilicate Glasses: High Resolution 11B R. C. Bradt*, R. Martens, The University of Alabama, USA & 27Al MAS NMR (GOMD-SI-P023-2012) Synthesis of CaO-MgO-SiO2 glass-ceramic E. Morin*, J. Stebbins, J. Wu, Stanford University, USA powders by using a waste solution of Na2SiO3 as silica source C. Yamagata, O. Higa, A. D. Rodas, Nuclear and Energy Research Institute, Brazil; S. T. Reis*, (GOMD-SP-P005-2012) A thermodynamic interpretation to explain Saint-Gobain Innovative Materials, USA enhanced ionic conductivity due to AgI dissolution in AgPO3-AgI glasses (GOMD-SI-P024-2012) Elasticity of sodium disilicate glass at high C. B. Bragatto*, Universidade Federal de São Carlos, Brazil; J. Souquet, Institut National pressures and high temperatures Polytechnique de Grenoble, France; A. Rodrigues, Universidade Federal de São Carlos, Brazil T. Yu *, The University of Chicago, USA; Y. Kono, Carnegie Institution of Washington, USA; T. Sakamaki, Z. Jing, Y. Wang, The University of Chicago, USA; G. Shen, Carnegie Institution of (GOMD-SP-P006-2012) Conversion of Fine-Diameter Melt-Derived Washington, USA Fibers to Hydroxyapatite in a Simulated Body Fluid X. Liu*, Missouri University of Science and Technology, USA; M. N. Rahaman, Missouri (GOMD-SI-P025-2012) Fractal Structure of Silicon Oxycarbide University of Science and Technology, USA; D. E. Day, Missouri University of Science and Polymer Derived Ceramics Technology, USA S. Widgeon*, S. Sen, University of California, Davis, USA; G. Mera, Technische Universität Darmstadt, Germany; E. Stoyanov, University of California, Davis, USA; R. Riedel, Technische (GOMD-SP-P007-2012) Dissolution Behavior of Sodium-Iron- Universität Darmstadt, Germany; A. Navrotsky, University of California, Davis, USA Phosphate Glasses in Alkaline Aqueous Solutions L. Ma*, Missouri University of Science and Technology, USA; R. K. Brow, Missouri University of (GOMD-SI-P026-2012) Direct Atomic-Resolution Imaging of a Two- Science and Technology, USA; M. E. Schlesinger, Missouri University of Science and Dimensional Silica Glass Technology, USA P. Huang*, Cornell University, USA; S. Kurasch, University of Ulm, Germany; A. Srivastava, V. Skakalova, Max Planck Institute for Solid State Research, Germany; J. Kotakoski, A. (GOMD-SP-P008-2012) Glass forming behavior of borate melts Krasheninnikov, University of Helsinki, Finland; R. Hovden, Q. Mao, Cornell University, USA; J. based on thermal analyses and viscosity measurements Meyer, University of Vienna, Austria; U. Kaiser, University of Ulm, Germany; D. Muller, Cornell K. Goetschius*, L. Ghussn, R. K. Brow, Missouri S&T, USA University, USA

14 2012 Glass & Optical Materials Division Annual Meeting Final Program Tuesday, May 22, 2012

(GOMD-SI-P027-2012) Thermal Analysis of Waste Glass Feeds: (GOMD-SIV-P046-2012) A High-Energy X-Ray Diffraction Study of Modeling Kinetic Parameters Neodymium Doped Sodium Phosphate Glasses D. Pierce*, R. Pokorny, J. Chun, P. Hrma, Pacific National Northwest Laboratories, USA K. Marasinghe*, E. Gunapala, University of North Dakota, USA; R. Brow, Missouri University of Science & Technology, USA; L. Skinner, C. Benmore, Argonne National Laboratory, USA (GOMD-SI-P028-2012) Formation and corrosion behavior of mechanically alloyed Cu-Zr-Ti bulk metallic glasses (GOMD-SIV-P047-2012) The crystallization of lithium-iron- P. L e e *, National Taiwan Ocean University, Taiwan phosphate glasses with substitutes R. Yang, H. Liu, Y. Wang, H. Jiang, S. Liu*, University of Jinan, China (GOMD-SI-P004-2012) Corrosion behavior of P0798 type simulated HLW glass in the presence of magnesium ion (GOMD-SIV-P048-2012) Synthesis and structural characterization T. M a e d a *, H. Ohmori, S. Mitsui, T. Banba, Japan Atomic Energy Agency, Japan of copper based lithium phosphate glasses C. Mugoni*, M. Montorsi, C. Siligardi, H. Jain, University of Modena and Reggio Emilia, Italy (GOMD-SII-P029-2012) UV-Covert Glass Taggants M. Velez*, Y. He, Mo-Sci Corp., USA; M. Rupasinghe, V. A. Samaranayake, R. K. Brow, Missouri (GOMD-SIV-P049-2012) Anion Distributions of Polyphosphate University of Science & Technology, USA Glasses from the ZnO-Al2O3-P2O5 System C. Smith*, Missouri University of Science and Technology, USA; R. Christensen, Iowa State (GOMD-SII-P030-2012) Thermal stability and optical properties of University, USA; R. K. Brow, Missouri University of Science and Technology, USA rare earth doped oxyfluoride tellurite glasses R. Morea, CSIC, Spain; A. Miguel, Universidad del Pais Vasco, Spain; J. Gonzalo*, J. (GOMD-SIV-P050-2012) Effect of Crystal Nucleation Rates on DSC Fernandez-Navarro, CSIC, Spain; J. Fernandez, R. Balda, Universidad del Pais Vasco, Spain Crystallization Peaks A. A. Cabral*, A. M. Rodrigues, A. M. Carvalho, Federal Institute of Maranhao, Brazil (GOMD-SII-P031-2012) Laser fabrication of SbSI ferroelectric single crystals on the surface of Sb-S-I and Ge-Sb-S-I glasses (GOMD-SIV-P051-2012) Non-isothermal Crystallization Kinetics of D. Savytskyy*, P. Gupta, B. Knorr, V. Dierolf, H. Jain, Lehigh University, USA a Na-Fluorrichterite Glass-Ceramic Precursor J. Pérez*, R. Casasola, M. Romero, J. Rincón, CSIC, Spain (GOMD-SII-P032-2012) Raman Studies of Laser-Induced Crystallization in Oxide and Chalcogenide Glasses (GOMD-SIV-P052-2012) Crystallization of red mud-based glasses B. Knorr*, P. Gupta, A. Stone, H. Jain, V. Dierolf, Lehigh University, USA containing BaO, SrO, and ZrO2 H. Vieira*, Nuclear and Energy Research Institute, Brazil; R. K. Brow, Missouri University of (GOMD-SII-P033-2012) Optical Control and Full-Octave Science and Technology, USA; J. R. Martinelli, Nuclear and Energy Research Institute, Brazil Supercontinuum Generation in Robust Chalcogenide Glass Fibers and Tapers (GOMD-SIV-P053-2012) Bioactive Glass Implants for Bone Repair S. Shabahang, G. Tao*, A. F. Abouraddy, University of Central Florida, USA made by Selective Laser Sintering M. Velez, Mo-Sci Corp., USA; K. Kolan*, M. Leu, G. Hilmas, Missouri University of Science & (GOMD-SII-P034-2012) In Situ Optical Spectroscopic Study of Technology, USA; S. Jung, Mo-Sci Corp., USA; D. E. Day, Missouri University of Science & Annealing of Tin-doped Ruby Glass Technology, USA; T. G. Chu, Indiana University, USA C. McDonough, University of Dallas, USA; C. Saiyasombat*, H. Jain, Lehigh University, USA (GOMD-SII-P035-2012) Europium doped oxyfluoride transparent glass-ceramics and their luminescence property Tuesday, May 22, 2012 Z. Pan*, R. Akrobetu, R. Mu, S. Morgan, Fisk University, USA (GOMD-SII-P036-2012) Optical Properties Of lithium-aluminum George W. Morey Award Lecture silicate galss –ceramics containing Nano LaF3 using Tb/Gd Room: Salon C A. Faeghi nia*, M. Vafaei fard, ceramic division, Islamic Republic of Iran 8:00 AM (GOMD-SII-P038-2012) Tm/Dy ions co-doped zinc-aluminum Thirty-five Years of Glass Research – A tribute to my co-authors phosphate glasses for white LED Edgar D. Zanotto*, Federal University of Sao Carlos, Brazil L. ChunTeng*, L. JianShian, C. YeeShin, Y. Hsiwen, Z. Teng, National United University, Taiwan (GOMD-SII-P039-2012) Spectral investigation on Eu3+- doped oxyfluoride glass and nanocrystalline glass-ceramics Symposium I: Glass Science R. Bagga*, KMV, India; M. M. Falconieri, ENEA, Italy; V. Achanta, TIFR, India; A. Goyal, Pacific Northwest National Laboratory, USA; J. Ferreira, Department of Ceramics and Glass Session 1: Glass Structure and Properties III Engineering, Portugal; N. Singh, Punjab Technical University, India; G. Singh, Akal College of Pharmacy, India; D. Singh, Guru Nanak DevUniversity, India; V. Contini, ENEA, Italy; G. Room: Salons E, F, & G Sharma, KMV, India Session Chair: Sabyasachi Sen, University of California, Davis (GOMD-SIII-P040-2012) New Glasses: Higher Performance at 9:20 AM Lower Cost (GOMD-SI-019-2012) Densified silica glass : structure and O. A. Prokhorenko*, Laboratory of Glass Properties, USA; D. Laurent, Y. Houet, 3B Co, Belgium properties (Invited) B. Champagnon*, C. Sonneville, A. Kassir-Bodon, C. Martinet, T. Deschamps, D. de Ligny, (GOMD-SIII-P041-2012) NMR methods for studying the cation CNRS-University Lyon1, France; G. Kermouche, CNRS-ENISE, France; S. Le Floch, A. San Miguel, CNRS-University Lyon1, France; R. Lacroix, J. Teisseire, E. Barthel, CNRS-Saint- dynamics in solid electrolytes Gobain, France M. Storek*, M. Adjei-Acheamfour, R. Böhmer, TU Dortmund, Germany (GOMD-SIII-P042-2012) Sol-gel derived Ag-SiO2 Thin Films: Effect 10:00 AM of Al Addition on Structural, Chemical, and Bactericidal Properties (GOMD-SI-020-2012) In-situ Raman and Brillouin light scattering B. Akkopru Akgun, Middle Eastern Technical University, Turkey; N. P. Mellott*, Alfred University, studies of pressure-quenched glasses USA; C. Durucan, Middle Eastern Technical University, Turkey M. Guerette*, L. Huang, Rensselaer Polytechnic Institute, USA (GOMD-SIV-P043-2012) Effect of Tin and Gold Dopings on Sodium 10:20 AM Ion Movement in Silicate Glass P. Wanninkhof, University of Florida, USA; C. Saiyasombat*, H. Jain, Lehigh University, USA (GOMD-SI-021-2012) Experimental and Computational Studies of Glasses (GOMD-SIV-P044-2012) Color and oxygen diffusion in niobium Q. Zhao, M. Guerette, G. Scannell, L. Huang*, Rensselaer Polytechnic Institute, USA phosphate glass L. Ghussn*, R. K. Brow, Missouri University of Science & Technology, USA 10:40 AM (GOMD-SI-022-2012) Anomalous compressibility of vitreous silica (GOMD-SIV-P045-2012) Approach to Predict the Long-term illuminated: Polyamorphism and the effect of hydration Weathering of Iron Phosphate Glass for the Immobilization of A. N. Clark*, C. E. Lesher, S. Sen, University of California, Davis, USA; S. D. Jacobsen, Hanford Low-Activity Waste Northwestern University, USA; Y. Wang, Univeristy of Chicago, USA E. Pierce*, Oak Ridge National Laboratory, USA

2012 Glass & Optical Materials Division Annual Meeting 15 Final Program Tuesday, May 22, 2012

11:00 AM 10:00 AM (GOMD-SI-023-2012) Structure and Properties of Compressed (GOMD-SII-020-2012) A Mid-Infrared Integrated Chalcogenide Borate Glasses Nulling Interferometer for Extrasolar Planet Detection M. M. Smedskjaer*, Corning Inc., USA; U. Bauer, H. Behrens, Leibniz University Hannover, N. Anheier*, B. Bernacki, H. Qiao, Pacific Northwest National Lab, USA; L. Labadie, I. Germany; S. Striepe, J. Deubener, Clausthal University of Technology, Germany; R. E. Physikalisches Institut, Universität zu Köln, Germany Youngman, M. Potuzak, J. C. Mauro, Corning Inc., USA; Y. Yue, Aalborg University, Denmark 10:20 AM 11:20 AM (GOMD-SII-021-2012) Thermally evaporated chalcogenide thin (GOMD-SI-024-2012) Effect of Network Polymerization on the films for mid-infrared applications: materials analysis, device Pressure-Induced Structural Changes in Multi-component Silicate design, fabrication, and testing Glasses and Melts (Invited) V. Si n gh*, A. M. Agarwal, L. C. Kimerling, Massachussetts Institute of Technology, USA; J. Hu, S. Lee*, Seoul National University, Republic of Korea University of Delaware, USA; J. Wilkinson, Massachussetts Institute of Technology, USA; J. D. Musgraves, K. Richardson, J. Giammarco, I. Luzinov, Clemson University, USA; J. M. Hensley, K. M. Parameswaran, D. M. Scherer, B. D. F. Casse, Physical Sciences Inc., USA; C. S. Kim, W. W. Bewley, C. L. Canedy, I. Vurgaftman, J. Abell, J. R. Meyer, Naval Research Laboratory, USA; Session 3: Atomistic Simulation and Modeling of M. Kim, Sotera Defense Solutions, USA Glass I Room: Salon A 10:40 AM Session Chair: Jincheng Du, University of North Texas (GOMD-SII-022-2012) On-chip integration of mid-IR sources and detectors using planar and 3D chalcogenide glass structures 9:20 AM Y. Zha, M. Waldman, C. Lu, C. B. Arnold*, Princeton University, USA (GOMD-SI-053-2012) Molecular Dynamics Simulations of Network 11:00 AM Dilation Anomaly in Ion-Exchanged Glass (Invited) A. Tandia*, V. Deenamma, J. C. Mauro, Corning Incorporated, USA; A. K. Varshneya, Alfred (GOMD-SII-023-2012) Chalcogenie Glass 1-D Photonic Crystal University, USA Cavities for Single-molecule Mid-infrared Photothermal Spectroscopy: Theory and Design 10:00 AM H. Lin*, Y. Zou, J. Hu, University of Delaware, USA (GOMD-SI-054-2012) Investigation of Ion-Exchange ‘Stuffed’ Glass 11:20 AM Structures by Anisotropically-Bounded Molecular Dynamics Simulation (GOMD-SII-024-2012) Fabrication of Two-dimensional Photonic P. K . K r e s k i *, Alfred University, USA; A. K. Varshneya, Saxon Glass Technologies, Inc., USA; A. Crystals on Erbium Doped Tellurite Thin Films and its Anisotropic N. Cormack, Alfred University, USA Photoluminescence P. L i n *, M. Vanhoutte, MIT, USA; J. Hu, University of Delaware, USA; N. Patel, V. Singh, Y. Cai, 10:20 AM R. Camacho-Aguilera, J. Michel, L. Kimerling, A. Agarwal, MIT, USA; C. Dimas, Masdar Institute (GOMD-SI-055-2012) A Virtual Reality Tool for Studying the of Science and Technology, United Arab Emirates Microstructure and Ion Dynamics of Glassy Materials Z. Zhou*, Shanghai University, China; G. N. Greaves, E. Flikkema, Aberystwyth University, United Kingdom Symposium IV: Festschrift to the Glass 10:40 AM Research Career of Prof. Delbert E. Day (GOMD-SI-056-2012) A new force field for ion-conducting network Session 1: The Mixed Alkali Effect and Ion glasses with general composition wLi2O-xB2O3-ySi2O4-zP2O5 C. R. Trott*, Technische Universitaet Ilmenau, Germany; M. Schuch, P. Maass, Universitaet Conducting Glasses I Osnabrueck, Germany Room: Grand Suites II & III 11:00 AM Session Chair: David Sidebottom, Creighton University (GOMD-SI-057-2012) Effect of Second-Shell Neighbors on the IR 9:20 AM Vibrational Modes in Silicate Glasses via MD Simulations K. Sebeck*, X. Zhou, J. Kieffer, University of Michigan, USA (GOMD-SIV-001-2012) Day’s Studies of Internal Friction and Ionic Diffusion in Silicate Glasses (Invited) 11:20 AM J. E. Shelby*, Alfred University, USA (GOMD-SI-058-2012) Simulating the luminescence of Eu3+ ions in 10:00 AM silicate glasses and the effect of the distribution of Eu3+ ion sites G. Mountjoy*, Q. Ting, University of Kent, United Kingdom (GOMD-SIV-002-2012) Revisiting a prominent review: Do we understand the most striking features of the mixed alkali effect? 11:40 AM (Invited) (GOMD-SI-059-2012) Nanoindentation Study of Densified Silica P. Maass*, University of Osnabrück, Germany Glass by Molecular Dynamics Simulations F. Yu a n *, L. Huang, Rensselaer Polytechnic Institute, USA 10:40 AM (GOMD-SIV-003-2012) Structural Aspects of the Mixed Alkali Effect: A Solid State NMR Point of View (Invited) Symposium II: Optical Materials & Devices H. Eckert*, F. Behrends, S. Puls, J. Epping, S. Faske, WWU Münster, Germany 11:20 AM Session 3: Planar Glass Photonics (GOMD-SIV-004-2012) Structure and Dynamics of Mixed Alkali Room: Salon B Glasses Formed by Ion Exchange (Invited) Session Chairs: Norm Anheier, Pacific Northwest National Lab; Juejun E. I. Kamitsos*, National Hellenic Research Foundation, Greece Hu, University of Delaware 9:20 AM Norbert J. Kreidl Award Lecture (GOMD-SII-019-2012) Planar Mid Infrared Integrated Glass-on- Room: Salon C Silicon Microphotonics for Imaging and Sensing (Invited) 12:00 PM A. M. Agarwal*, MIT, USA Topological Constraints and Rigidity of Network Glasses from Molecular Dynamics Simulations Mathieu Bauchy*, Universite Pierre et Marie Curie, France

16 2012 Glass & Optical Materials Division Annual Meeting Final Program Tuesday, May 22, 2012

Symposium I: Glass Science 5:20 PM (GOMD-SI-109-2012) A Comparison of Viscosity Models in terms of Session 1: Glass Structure and Properties IV Numerical Precision and Prediction of High-T Values R. Conradt*, RWTH Aachen University, Germany Room: Salons E, F, & G Session Chair: Randall Youngman, Corning Incorporated Session 3: Atomistic Simulation and Modeling II 1:20 PM Room: Salon A (GOMD-SI-025-2012) Internal Residual Stresses in Lithium Session Chairs: Jincheng Du, University of North Texas; Liping Huang, Diborate Glass-Ceramics F. C. Serbena*, State University of Ponta Grossa, Brazil; L. Ghussn, R. M. Reis, E. D. Zanotto, Rensselaer Polytechnic Institute Federal University of São Carlos, Brazil 1:20 PM 1:40 PM (GOMD-SI-060-2012) Structural, dynamic and electronic properties (GOMD-SI-026-2012) Heterogeneities, phase separation and of sodium-silicate glasses and liquids from ab initio simulations nucleation in silicate glasses (Invited) L. Cormier*, O. Dargaud, N. Menguy, UPMC - CNRS, France; G. Patriarche, CNRS, Laboratoire W. Kob*, L. Pedesseau, S. Ispas, University Montpellier 2, France de Photonique et de Nanostructures, France 2:00 PM 2:00 PM (GOMD-SI-061-2012) Structural properties of liquid and amorphous

(GOMD-SI-027-2012) Evidence for self-organization in Borate Ge2Se3: first principles studies Glasses S. Le Roux*, C. Massobrio, Institut de Physique et Chimie des Matériaux de Strasbourg, P. Boolchand, K. Vignarooban*, University of Cincinnati, USA; M. Micoulaut, University of Paris France 6, France; M. Malki, University of Orleans, France; R. Kerner, University of Paris 6, France 2:20 PM 2:20 PM (GOMD-SI-062-2012) Molecular Dynamics Simulation of Sodium (GOMD-SI-028-2012) The structure of binary high alumina Al2O3- Borate Glasses SiO2 glass forming liquids A. Takada*, Asahi Glass Company, Japan; S. Feller, M. Affatigato, Coe College, USA L. B. Skinner*, Stony Brook University, USA; C. J. Benmore, Argonne National Lab, USA; R. Weber, Materials Development Inc., USA; J. B. Parise, Stony Brook University, USA 2:40 PM (GOMD-SI-063-2012) Three-dimensional structure of 2:40 PM multicomponent (Na2O)0.35 [(P2O5)1-x (B2 O3)x ]0.65 glasses by high- (GOMD-SI-029-2012) Silicate Glasses at the Ionic Limit: Alkaline- energy x-ray diffraction and constrained reverse Monte Carlo Earth Sub-Orthosilicates simulations N. Nasikas, Institute of Chemical Engineering and High Temperature Chemical Processes S. Le Roux*, Institut de Physique et Chimie des Matériaux de Strasbourg, France; V. Petkov, FORTH, Greece; T. Edwards, S. Sen*, University of California, Davis, USA; G. Papatheodorou, Central Michigan University, USA Institute of Chemical Engineering and High Temperature Chemical Processes FORTH, Greece 3:00 PM 3:00 PM Break Break

3:20 PM 3:20 PM (GOMD-SI-064-2012) Molecular dynamics modelling of iron and (GOMD-SI-030-2012) Fictive temperature measurement of silica other phosphate glasses (Invited) and doped-silica glasses using FTIR method: glass containing Si-H G. Mountjoy*, University of Kent, United Kingdom bonding and thick sample C. Li*, M. Tomozawa, Rensselaer Polytechnic Institute, USA 4:00 PM 3:40 PM (GOMD-SI-065-2012) The structural role of ZnO in strontium containing bioactive glass: molecular dynamics simulations (GOMD-SI-031-2012) Simulations of the Effect of the Addition of Y. Xiang*, J. Du, University of North Texas, USA Phosphate on Er-doped Silica Glasses H. Inoue*, The University of Tokyo, Japan; A. Masuno, The University of Tokyo, Japan; Y. Saito, 4:20 PM Sumitomo Electric Industries, Ltd, Japan (GOMD-SI-066-2012) Atom size effect and chemical bonding in 4:00 PM rigidity transitions M. Micoulaut*, M. Bauchy, UPMC, France (GOMD-SI-032-2012) Inert Failure Strain Measurements of Sodium Borate Glass Fibers 4:40 PM Z. Tang*, N. P. Lower, Missouri S&T, USA; C. R. Kurkjian, University of Southern Maine, USA; R. K. Brow, Missouri S&T, USA (GOMD-SI-067-2012) Glass structure with well defined thermal history and glassy dynamic 4:20 PM C. Scherer*, M. Letz, Schott AG, Germany; F. Schmid, Johannes-Gutenberg University, Germany (GOMD-SI-033-2012) Structure-Property Relationships of the Mixed Glass Former Glasses 0.2Na2O + 0.2[xBO3/2 +(1-x) SiO2] 5:00 PM R. Christensen*, Iowa State University, USA (GOMD-SI-068-2012) Glass stability parameters and glass forming 4:40 PM ability. Comparison and opportunities A. F. Kozmidis-Petrovic*, University of Novi Sad, Faculty of Technical Sciences, Serbia (GOMD-SI-034-2012) Space Charge Formation and High Field Properties of Low Alkali Glasses 5:20 PM P. D a s h *, M. T. Lanagan, C. G. Pantano, E. Furman, The Pennsylvania State University, USA (GOMD-SI-069-2012) Fiber Drawing: Basic Principals Model 5:00 PM O. A. Prokhorenko*, Laboratory of Glass Properties, USA (GOMD-SI-035-2012) Structure and Properties of Iron Borophosphate Glasses M. Karabulut*, G. Mamedov, H. Ertap, B. Yuce, O. Bozdogan, Kafkas University, Turkey

2012 Glass & Optical Materials Division Annual Meeting 17 Final Program Tuesday, May 22, 2012

Symposium II: Optical Materials & Devices Symposium IV: Festschrift to the Glass Research Career of Prof. Delbert E. Day Session 3: Optical Fibers Room: Salon B Session 1: The Mixed Alkali Effect and Ion Session Chairs: Norm Anheier, Pacific Northwest National Lab; Juejun Conducting Glasses II Hu, University of Delaware Room: Grand Suites II & III 1:20 PM Session Chair: Philipp Maass, University of Osnabrueck (GOMD-SII-025-2012) Recent Developments in IR Glass and Fiber Technology (Invited) 1:20 PM J. S. Sanghera*, Naval Research Lab, USA (GOMD-SIV-005-2012) A role of the heterogeneity of dynamics in the mixed alkali effect (Invited) 2:00 PM J. Habasaki*, Tokyo Institute of Technology, Japan; K. L. Ngai, University of Pisa, Italy (GOMD-SII-026-2012) One-step Multi-material Optical Fiber Preform Extrusion for Robust Chalcogenide Glass Optical Fibers 2:00 PM and Tapers (GOMD-SIV-007-2012) Ion transport in copper oxide containing G. Tao*, S. Shabahang, E. Banaei, J. J. Kaufman, A. F. Abouraddy, University of Central lithium phosphate glasses Florida, USA C. Mugoni*, G. Broglia, M. Montorsi, C. Siligardi, University of Modena and Reggio Emilia, Italy; H. Jain, Lehigh University, USA 2:20 PM (GOMD-SII-027-2012) Reactive molten core fabrication of silicon 2:20 PM optical fiber (Invited) (GOMD-SIV-008-2012) In-situ study of bias-induced particle growth J. Ballato*, S. Morris, T. Hawkins, P. Foy, Clemson University, USA; R. Rice, Dreamcatchers on a lithium-ion conductive glass ceramic (LIC-GC) (Invited) Consulting, USA; L. Zhu, R. Stolen, Clemson University, USA J. Krümpelmann*, C. Yada, Uni Marburg, Germany; F. Rosciano, Toyota Motor Europe, Belgium; B. Roling, Uni Marburg, Germany 2:40 PM (GOMD-SII-028-2012) The influence of core geometry on the 3:00 PM crystallography of silicon optical fiber Break J. Ballato*, S. Morris, T. Hawkins, C. McMillen, P. Foy, Clemson University, USA; R. Rice, Dreamcatchers Consulting, USA 3:20 PM 3:00 PM (GOMD-SIV-009-2012) Critical Ordering Temperature of Mixed Break Alkali Glasses (Invited) M. Tomozawa*, P. J. Lezzi, M. Yoshiyagawa, RPI, USA 3:20 PM 4:00 PM (GOMD-SII-029-2012) Tellurite and Chalcogenide Microstructured (GOMD-SIV-010-2012) New Studies of Ion Conduction in Optical Fibers for Broadband Sources in the Infrared (Invited) Phosphate-Based Mixed Glass Former Glasses (Invited) F. S m e k t a l a *, Universite de Bourgogne, France S. W. Martin*, Iowa State University, USA; R. B. Christensesn, Iowa State University, USA; G. Olson, Iowa State University, USA; P. Maass, University of Osnabruick, Germany; M. Schuch, 4:00 PM University of Osnabruick, Germany (GOMD-SII-030-2012) Multi-material Fibers: Current Progress and 4:40 PM Future Prospects (Invited) A. F. Abouraddy*, University of Central Florida, CREOL, USA (GOMD-SIV-011-2012) Internal friction of calcium alumino-silicate glasses substituted with Ba, Sr and Mg 4:40 PM A. K. Swarnakar*, Leuven University, Belgium; A. Stamboulis, University of Birmingham, United Kingdom; O. Van der Biest, Leuven University, Belgium (GOMD-SII-031-2012) Annealing of Silicon Optical Fibers J. Ballato*, N. Gupta, C. McMillen, R. Singh, R. Podila, A. Rao, T. Hawkins, P. Foy, S. Morris, Clemson University, USA; R. Rice, Dreamcatchers Consulting, USA; L. Zhu, Clemson 5:00 PM University, USA (GOMD-SIV-012-2012) Dynamic Light Scattering in Mixed Alkali Metaphosphate Glassforming Liquids 5:00 PM D. L. Sidebottom*, J. Changstrom, Creighton University, USA (GOMD-SII-032-2012) An acentric crystalline oxide core optical fiber J. Ballato*, C. McMillen, T. Hawkins, P. Foy, L. Zhu, Clemson University, USA; R. Rice, Session 4: Glasses for Bio-Medical Applications Dreamcatchers Consulting, USA; O. Stafsudd, UCLA, USA Room: Salon C 5:20 PM Session Chairs: Julian Jones, Imperial College; Matthew Hall, Alfred (GOMD-SII-033-2012) Surface Enhanced Raman Scattering of silica University matrixes containing noble metal nanoparticles for the improvement 1:20 PM of Raman Amplification in telecommunication optical fibers B. Champagnon*, E. Nardou, D. Vouagner, A. Jurdyc, A. Berthelot, O. Ben Amara, A. Pillonnet, (GOMD-SIV-032-2012) Composition Structure Property CNRS-University Lyon1, France; L. Bertry, O. Durupthy, C. Chanéac, Uninversity Pierre et Marie Relationships in Bioactive Glasses (Invited) Curie, France; A. Pastouret, E. Burov, Draka Comtek France, France R. G. Hill*, Queen Mary University of London, United Kingdom 2:00 PM (GOMD-SIV-033-2012) Treatment of Chronic Ulcers with Bioactive Borate Glass Nanofibers S. B. Jung*, T. Day, MO-SCI Corporation, USA; W. V. Stoecker, P. Taylor, Phelps County Regional Medical Center, USA; D. E. Day, Missouri University of Science and Technology, USA

2:20 PM (GOMD-SIV-034-2012) Glass-ceramics with high strength for dental application W. Hoeland*, C. Ritzberger, M. Schweiger, V. M. Rheinberger, Ivoclar Vivadent AG, Liechtenstein

18 2012 Glass & Optical Materials Division Annual Meeting Final Program Wednesday, May 23, 2012

2:40 PM 10:20 AM (GOMD-SIV-035-2012) Phosphate Based Glass Fibre Reinforced (GOMD-SI-041-2012) SiOC glass-diamond composites Composites for Bone Repair Applications T. Rouxel*, P. Sellappan, University Rennes 1, France; L. Toma, G. Miehe, TU Darmstadt, I. Ahmed*, A. J. Parsons, C. A. Scotchford, D. Grant, C. D. Rudd, University of Nottingham, Germany; F. Célarié, University Rennes 1, France; R. Riedel, TU Darmstadt, Germany United Kingdom 10:40 AM 3:00 PM (GOMD-SI-042-2012) Study of Europium Valence in ZBLAN Image Break Plates (Invited) J. Johnson*, C. Johnson, UTSI, USA; C. Passlick, Fraunhofer Center for Silicon Photovoltaics, Germany; S. Gray, UTSI, USA; R. Weber, Materials Development Inc., USA; S. Schweizer, 3:20 PM Fraunhofer Center for Silicon Photovoltaics, Germany (GOMD-SIV-036-2012) Effect of the Glass Composition on In Vivo 11:20 AM Behavior of Bioactive Glasses (Invited) L. Hupa*, Åbo Akademi University, Finland (GOMD-SI-043-2012) Nanostructure of Silicon Carbonitride and Silicon Boron Carbonitride Polymer-Derived Ceramics (PDCs) 4:00 PM using Solid State Nuclear Magnetic Resonance (SSNMR) S. Widgeon*, University of California, Davis, USA; Y. Gao, G. Mera, Technische Universität (GOMD-SIV-037-2012) In vitro and in vivo response of tailored Darmstadt, Germany; E. Stoyanov, S. Sen, A. Navrotsky, University of California, Davis, USA; R. amorphous multi porous (TAMP) bioscaffolds Riedel, Technische Universität Darmstadt, Germany M. Saad, M. Sabry, M. Marei, Alexandria University, Egypt; S. Wang, T. Kowal, J. Marzillier, M. Falk, H. Jain*, Lehigh University, USA 11:40 AM 4:20 PM (GOMD-SI-044-2012) Silicon Oxycarbide Glass as a Low Dielectric (GOMD-SIV-038-2012) Alkali-free bioactive glasses for bone tissue material Y. K i m *, Y. Lee, S. Kim, W. Kwon, Korea Institute of Ceramic Engineering and Technology, engineering Republic of Korea A. Goel*, Pacific Northwest National Laboratory, USA; J. M. Ferreira, University of Aveiro, Portugal

4:40 PM Session 4: Relaxation I (GOMD-SIV-039-2012) Effect of titanium oxide in the development Room: Salon A of an organically modified silicate based dopamine sensor Session Chair: Ulrich Fotheringham, SCHOTT AG P. C. Pandey, A. Prakash*, D. S. Chauhan, Institute of Technology, Banaras Hindu University, India 8:00 AM (GOMD-SI-070-2012) Relaxation, Polyamorphism and Perfect Glasses (Invited) Wednesday, May 23, 2012 N. Greaves*, University of Cambridge, United Kingdom; Z. Zhou, Shanghai University, China 8:40 AM Symposium I: Glass Science (GOMD-SI-071-2012) On the fragility and relaxation behavior of bulk metallic glass forming liquids (Invited) Session 2: Non-Oxide Glasses I R. Busch*, Chair for Metallic Materials, Germany Room: Salons E, F, & G 9:20 AM Session Chairs: Andriy Kovalskyy, Austin Peay State University; David (GOMD-SI-072-2012) Physical aging of chalcogenide glass Musgraves, Clemson University (Invited) R. Golovchak, Lehigh University, USA; A. Kozdras, Opole University of Technology, Poland; H. 8:00 AM Jain*, Lehigh University, USA (GOMD-SI-049-2012) Ab initio simulations of chalcogenides: size 10:00 AM effects, structure, rigidity and dynamics (Invited) M. Micoulaut*, UPMC, France Break 8:40 AM 10:20 AM (GOMD-SI-036-2012) Observation of polyamorphism in GeTe- Sb2Te3 Phase Change Materials (GOMD-SI-073-2012) Analysis of small volume changes at S. Sen*, University of California, Davis, USA; B. Kalkan, Advanced Light Source, Lawrence temperatures below the region (Invited) Berkeley Laboratory, USA; S. Clark, University of California, Berkeley, USA; B. Aitken, Corning S. M. Rekhson*, Cleveland State University, retired, USA Incorporated, USA 11:00 AM 9:00 AM (GOMD-SI-074-2012) Glass Transition Studies of Mechanically (GOMD-SI-037-2012) Meeting experimental challenges to physics Milled Amorphous Materials (Invited) of network glasses- assessing the role of sample homogeneity S. W. Martin*, Iowa State University, USA; M. Marple, Iowa State University, USA; C. Bischoff, (Invited) Iowa State University, USA P. Boolchand*, S. Bhosle, K. Gunasekera, P. Chen, Univ of Cincinnati, USA; M. Micoulaut, University of Paris 6, France; C. Massobrio, Institut de Physique et de Chimie des Materiaux de 11:40 AM Strasbourg,, France (GOMD-SI-075-2012) Relaxation in NaAlSi3O8 across the glass 9:40 AM transition interval at high pressure S. J. Gaudio*, C. E. Lesher, S. Sen, University of California, Davis, USA (GOMD-SI-039-2012) Glass formation and molecular structure in the SixGexTe100-2x ternary P. Boolchand, K. Gunasekera*, Univ of Cincinnati, USA; S. Mamedov, Horiba Jobin Yvon Inc, Session 5: Glass Corrosion and Surface Science I USA Room: Salon B 10:00 AM Session Chair: Nathan Mellott, Alfred University Break 8:00 AM (GOMD-SI-083-2012) Glass-Water Interfacial Reactions: Role of Experimentation and Modeling in Predicting Long-term Weathering (Invited) E. Pierce*, Oak Ridge National Laboratory, USA

2012 Glass & Optical Materials Division Annual Meeting 19 Final Program Wednesday, May 23, 2012

8:40 AM 9:40 AM (GOMD-SI-084-2012) First-Principles Study Of Barriers For (GOMD-SII-038-2012) Calorimetric Absorption Measurements of Dissolution Reactions In Silicate Minerals And Glasses Laser Glasses P. Zapol*, H. He, X. Tan, Argonne National Laboratory, USA M. J. Davis*, J. S. Hayden, SCHOTT North America, Inc., USA 9:00 AM 10:00 AM (GOMD-SI-085-2012) Distinguishing Chemical Reaction Affinity Break from Mass Transport in Silica-Saturated Solutions W. Ebert*, Argonne National Laboratory, USA 9:20 AM Symposium I: Glass Science (GOMD-SI-086-2012) Dissolution Kinetics of Borosilicate SON68 Glass Determined by Experiment: Effects of Al and Si Session 6: Topological Constraints and Rigidity: J. Icenhower*, C. Steefel, Lawrence Berkeley National Laboratory, USA Theory and Experiment I 9:40 AM Room: Salon C (GOMD-SI-087-2012) New insight into the composition-dependent Session Chair: Pierre Lucas, Univ of AZ-Harshbarger Rm 224B long-term alteration rate of glass S. Gin*, X. Beaudoux, C. Jegou, CEA, France 10:20 AM 10:00 AM (GOMD-SI-104-2012) Topological Principles of Chemistry (Invited) Break J. C. Mauro*, M. M. Smedskjaer, R. E. Youngman, C. L. Hogue, M. Potuzak, Corning Incorporated, USA; Y. Yue, Aalborg University, Denmark

10:20 AM 11:00 AM (GOMD-SI-088-2012) Studies of Glass Corrosion Combining (GOMD-SI-105-2012) On the criterion for identification of Analytical Spectroscopies and Computational Chemistry (Invited) intermediate phases in network glasses K. Mueller*, Pacific Northwest National Laboratory, USA; C. Pantano, Penn State University, R. Golovchak*, Lehigh University, USA USA 11:20 AM 11:00 AM (GOMD-SI-106-2012) Transport, intermediate phases and rigidity in (GOMD-SI-089-2012) Observed Structural Changes in Leached glass-forming liquids Nuclear Waste Glasses by Solid State NMR M. Micoulaut, M. Bauchy*, UPMC, France K. Murphy*, The Pennsylvania State University, USA; K. T. Mueller, Pacific Northwest National Laboratory, USA; C. G. Pantano, The Pennsylvania State University, USA; J. V. Ryan, N. M. Washton, Pacific Northwest National Laboratory, USA Symposium III: Cross-Cutting Topics 11:20 AM (GOMD-SI-090-2012) The Use of Isotopic Tracing to Determine Session 3: Archeological Glass Science and Elemental Diffusion Profiles Through an Established Alteration Technology Layer J. Ryan*, A. V. Mitroshkov, Z. Zhu, J. J. Neeway, D. A. Schreiber, Pacific Northwest National Room: Grand Suites II & III Laboratory, USA Session Chair: Denis Strachan, Pacific Northwest National Laboratory 11:40 AM 8:00 AM (GOMD-SI-091-2012) Atomic Profiles of Corrosion Layer Interface (GOMD-SIII-032-2012) An archaeological slag for probing by Atom Probe Tomography glass/iron interaction (Invited) D. K. Schreiber*, J. Ryan, Pacific Northwest National Laboratory, USA S. Gin*, A. Michelin, D. Neff, P. Dillmann, E. Burger, D. Rebiscoul, CEA, France 8:40 AM Symposium II: Optical Materials & Devices (GOMD-SIII-033-2012) The formation regularity of black-glazed tea bowls from the Jian kiln site of ancient China Session 4: Optical Absorption W. Li*, H. Luo, Shanghai Institute of Ceramics, China Room: Salon C 9:00 AM Session Chair: Mark Davis, SCHOTT North America, Inc. (GOMD-SIII-034-2012) Characterization of Roman Glasses as 8:00 AM Analogues for Nuclear Waste Glasses D. Strachan*, J. Ryan, J. Crum, D. Schreiber, Pacific Northwest National Laboratory, USA (GOMD-SII-034-2012) Photo-thermo-induced absorption in photo- thermo-refractive glass (Invited) 9:20 AM J. Lumeau*, L. Glebova, L. B. Glebov, University of Central Florida, USA Break 8:40 AM (GOMD-SII-035-2012) Formation and structure of Au nanoparticles in sodium trisilicate ruby glass by X-ray absorption and optical Session 2: NMR Studies of the Structure of spectroscopy C. Saiyasombat*, H. Jain, Lehigh University, USA Glass 1: Mixed Glass Former Systems Room: Grand Suites II & III 9:00 AM Session Chair: Steve Martin, Iowa State University (GOMD-SII-036-2012) Brillouin scattering from superpolished vitreous silica in the Urbach-tail region 10:20 AM B. Rufflé*, E. Courtens, M. Foret, University of Montpellier II, France (GOMD-SIII-017-2012) Mixed Glass Former Effect in alkali borophosphate glasses: Structural investigation by advanced 31P 9:20 AM and 11B NMR (Invited) (GOMD-SII-037-2012) Predicting the Photoelastic Response of A. Pradel*, B. Raguenet, Université Montpellier 2, France; G. Tricot, Université des Sciences et Silicate Glasses technologies de Lille, France; G. Silly, M. Ribes, Université Montpellier 2, France M. M. Smedskjaer*, J. C. Mauro, X. Guo, S. A. Saxton, A. J. Ellison, Corning Inc., USA

20 2012 Glass & Optical Materials Division Annual Meeting Final Program Wednesday, May 23, 2012

11:00 AM Session 4: Relaxation II (GOMD-SIII-018-2012) The Mixed Network Former Effect in Room: Salon A Glasses: Structure-Property Correlations in Phosphate-Based Session Chair: Tanguy Rouxel, University Rennes 1 Glass Systems (Invited) H. Eckert*, M. Rinke, D. Larink, F. Behrends, WWU Münster, Germany; S. Martin, WWU 1:20 PM Münster, Germany, WWU Münster, GermanyIowa State University, USA (GOMD-SI-076-2012) Thermodynamics of viscous flow and 11:40 AM elasticity of glass forming liquids in the Glass Transition Range (GOMD-SIII-019-2012) Increased Accuracy For Non-bridging (Invited) Oxygen Measurements in Silicate Glasses Using 17O NMR T. Rouxel*, University Rennes 1, France L. M. Thompson*, J. F. Stebbins, Stanford University, USA 2:00 PM (GOMD-SI-077-2012) Phenomenological Modeling of Structural Symposium I: Glass Science Relaxation with a Modified TNM Model (Invited) R. G. Erdmann*, P. Lucas, E. A. King, University of Arizona, USA Session 2: Non-Oxide Glasses II 2:40 PM Room: Salons E, F, & G (GOMD-SI-078-2012) Parametric Studies of Simulated Modulated Session Chairs: Andriy Kovalskyy, Austin Peay State University; David DSC with the TNM Model Musgraves, Clemson University E. A. King*, R. G. Erdmann, P. Lucas, University of Arizona, USA 1:20 PM 3:00 PM (GOMD-SI-045-2012) Chalcogenide glasses, materials for Break homeland security applications (Invited) M. Vlcek*, University of Pardubice, Czech Republic 3:20 PM 2:00 PM (GOMD-SI-079-2012) Insights into glass transition and relaxation (GOMD-SI-046-2012) Structural interpretation of spectral selectivity behavior using temperature-modulated differential scanning calorimetry of photoinduced effects in As2S3 thin films A. Kovalskyy*, Austin Peay State University, USA; M. Vlcek, University of Pardubice, Czech X. Guo*, J. C. Mauro, D. C. Allan, R. L. Stewart, Corning Inc., USA; Y. Yue, Aalborg University, Republic; J. Oelgoetz, Austin Peay State University, USA; H. Jain, Lehigh University, USA Denmark

2:20 PM 3:40 PM (GOMD-SI-047-2012) Structure and Properties of B-containing (GOMD-SI-080-2012) Prony series temporal spectra for structural GeAs Sulfide and Selenide Glasses (Invited) relaxation in optical glass B. Aitken*, S. Currie, R. Youngman, Corning Inc., USA E. Koontz*, V. Y. Blouin, Clemson University, USA 3:00 PM 4:00 PM Δ Break (GOMD-SI-081-2012) The Temperature Width, Tg, of the Glass Transition as a Function of Composition in Alkali Borate Glasses S. Feller, T. Munhollon*, K. Podhajsky, M. Affatigato, Coe College, USA 3:20 PM 4:20 PM (GOMD-SI-048-2012) Structure and properties of telluride glasses for sensing applications (Invited) (GOMD-SI-082-2012) Phonon theory of liquids and their glass P. L u c a s *, Z. Yang, A. Wilhelm, University of Arizona, USA; P. Jovari, RISSPO, Hungary; B. transition Bureau, University of Rennes, France K. Trachenko*, Queen Mary University of London, United Kingdom 4:00 PM (GOMD-SI-038-2012) Thermal Properties of Chalcogenide Glasses Session 5: Glass Corrosion and Surface Science J. Musgraves*, S. Danto, P. Wachtel, K. Richardson, Clemson University, USA II 4:20 PM Room: Salon B (GOMD-SI-040-2012) Thermal Poling Behavior and SHG Stability of Session Chair: Nathan Mellott, Alfred University Multicomponent Chalcogenide Glasses T. S h o u l d e r s *, University of Central Florida, USA; J. W. Novak, Clemson University, USA; M. 1:20 PM Dussauze, Université Bordeaux, France; K. Richardson, Clemson University, USA (GOMD-SI-092-2012) Effects of Alteration Product Precipitation on Glass Dissolution: Preliminary Results 4:40 PM D. M. Strachan, J. J. Neeway*, J. V. Ryan, Pacific Northwest National Laboratory, USA (GOMD-SI-050-2012) DFT studies of the atomic structure of disordered chalcogenides 1:40 PM S. Le Roux*, C. Massobrio, Institut de Physique et Chimie des Matériaux de Strasbourg, (GOMD-SI-093-2012) Measuring Long-Term Glass Dissolution France Rates in the Presence of Mineral Alteration Phases C. L. Crawford*, Savannah River National Laboratory, USA; W. L. Ebert, Argonne National 5:00 PM Laboratory, USA (GOMD-SI-051-2012) The stress-optic response of Ge-P-S glass: experimental results and comparison with models 2:00 PM J. Galbraith*, J. Zwanziger, Dalhousie University, Canada; B. Aitken, Corning Inc., USA (GOMD-SI-094-2012) Coupled Waste Glass Dissolution and Mineral Alteration Phase Precipitation 5:20 PM J. A. Fortner*, W. L. Ebert, Argonne National Lab, USA (GOMD-SI-052-2012) Effects of Structure on the Distribution of 2:20 PM Activation Energy Model in the Na2S+GeS2+P2S5 Glass System C. Bischoff*, K. Schuller, S. P. Beckman, S. W. Martin, Iowa State University, USA (GOMD-SI-095-2012) Nuclear glass dissolution at high pH K. Ferrand*, K. Lemmens, SCK-CEN, Belgium

2012 Glass & Optical Materials Division Annual Meeting 21 Final Program Wednesday, May 23, 2012

2:40 PM Session 2: NMR Studies of Structure of Glass 3: (GOMD-SI-096-2012) Structural evolution under aqueous corrosion Structure and Dynamics of borosilicate glasses containing rare earths E. Molières*, F. Angeli, P. Jollivet, CEA - Marcoule, France; D. de Ligny, G. Panczer, LPCML, Room: Grand Suites II & III France; T. Charpentier, A. Soleilhavoup, O. Spalla, CEA - Saclay, France; S. Gin, CEA - Session Chair: Steve Martin, Iowa State University Marcoule, France; P. Barboux, LCMCP-ENSCP, France 3:20 PM 3:00 PM (GOMD-SIII-022-2012) Nuclear magnetic resonance studies of Break mixing effects in ion conducting glasses (Invited) M. Storek, M. Adjei-Acheamfour, R. Böhmer*, TU Dortmund, Germany; R. Christensen, G. Olson, S. Martin, D. Larink, Iowa State University, USA; H. Eckert, Westfälische Wilhelms- 3:20 PM Universität, Germany (GOMD-SI-097-2012) Alteration mechanism of obsidian for its suitability as nuclear waste glass 4:00 PM N. Rani*, J. P. Shrivastava, University of Delhi, India; R. K. Bajpai, BARC, India (GOMD-SIII-023-2012) NMR Studies of Ion Transport in Solid and Polymer Electrolytes (Invited) 3:40 PM M. Vogel*, Institute of Condensed Matter Physics, TU Darmstadt, Germany (GOMD-SI-098-2012) Understanding polishing-induced surface defectivity on EUV masks 4:40 PM R. Teki*, A. Kadaksham, J. Harris-Jones, E. Stinzianni, F. Goodwin, SEMATECH, USA (GOMD-SIII-024-2012) Network cation coordination and oxygen speciation in oxide glasses and melts: a view from NMR 4:00 PM spectroscopy (Invited) (GOMD-SI-099-2012) Study on glass frit corrosion influenced by J. F. Stebbins*, J. Wu, L. Thompson, stanford university, USA - - composition and water content in I3 /I redox electrolyte K. F. Jensen*, A. Hinsch, W. Veurman, Fraunhofer Institute for Solar Energy Systems ISE, 5:20 PM Germany; S. Sarker, H. Son, J. Kim, Konkuk University, Republic of Korea; C. Im, Konkuk University- Fraunhofer Next generation Solar cell research Center, Republic of Korea; J. Wilde, (GOMD-SIII-025-2012) Estimating the E-modulus of glasses from University of Freiburg, Germany; J. Lee, Konkuk University- Fraunhofer Next generation Solar NMR structural data cell research Center, Republic of Korea A. K. Swarnakar*, Leuven University, Belgium; A. Stamboulis, University of Birmingham, United Kingdom; O. Van der Biest, Leuven University, Belgium 4:20 PM (GOMD-SI-100-2012) Atomic Layer Deposition (ALD) Coating on Soda-lime-silicate Glass for Strength Improvement Symposium I: Glass Science Y. A r a i *, C. G. Pantano, Pennsylvania State University, USA Session 6: Topological Constraints and Rigidity: 4:40 PM Theory and Experiment II (GOMD-SI-101-2012) Dissolution kinetics of bio-active borate glasses in aqueous solutions Room: Salon C J. George*, R. Brow, Missouri University of Science and Technology, USA Session Chair: Pierre Lucas, Univ of AZ-Harshbarger Rm 224B 5:00 PM 1:20 PM (GOMD-SI-102-2012) Enhanced Dissolution Rate of Densified (GOMD-SI-107-2012) Towards ultra-strong glasses (Invited) Glass: a Probe for Densification under Nanoindentations L. Wondraczek*, University of Erlangen, Germany J. Guin, CNRS-INSIS, France; K. Han*, Université de Rennes 1, France 2:00 PM 5:20 PM (GOMD-SI-108-2012) Anomalous elastic behavior of vitreous silica (GOMD-SI-103-2012) The Effect on Product Quality of Varying the under high pressure and high temperature Oxide to Magnox Ratio in High Incorporation UK Blend HLW Glass S. Ayrinhac, M. Foret, H. Tran, R. Vacher, C. Weigel, B. Rufflé*, Montpellier University, France M. Harrison*, R. Short, N. Gribble, C. Steele, Sellafield Ltd, United Kingdom Symposium II: Optical Materials & Devices Symposium III: Cross-Cutting Topics Session 6: Optical Ceramics and Glass Session 2: NMR Studies of the Structure of Ceramics Glass 2: Chemical Order and Disorder Effects Room: Salon C Room: Grand Suites II & III Session Chair: Robert Pavlacka, US Army Research Laboratory Session Chair: Josef Zwanziger, Dalhousie University 3:20 PM 1:20 PM (GOMD-SII-039-2012) Structural Characterization of Luminescent (GOMD-SIII-020-2012) Recent developments in the understanding Glasses and Ceramics Using Solid State NMR (Invited) of the structure of glasses containing lone-pair cations (Invited) H. Eckert*, H. Deters, WWU Münster, Germany; A. de Camargo, C. Magon, F. de Lima, WWU D. Holland*, O. Alderman, N. Laorodphan, R. Dupree, Warwick University, United Kingdom; E. Münster, Germany, WWU Münster, GermanyIFSC, USP, Brazil Barney, Nottingham University, United Kingdom; A. Hannon, Rutherford Appleton laboratory, United Kingdom 4:00 PM (GOMD-SII-040-2012) A new synthesis way for the production of 2:00 PM bulk chalcogenide glasses and glass-ceramics by mechanical (GOMD-SIII-021-2012) Order and disorder in glasses : chemical alloying and Spark Plasma Sintering and geometrical contributions at different scales (Invited) M. Hubert*, Université de Rennes 1, France; G. Delaizir, Groupe d’Etudes des Matériaux D. Massiot*, M. Deschamps, F. Fayon, V. Montouillout, N. Pellerin, P. Florian, D. Neuville, S. Hétérogènes (GEMH), Centre Européen de la Céramique, France; X. Zhang, L. Calvez, Cadars, L. Martel, J. Hiet, CEMHTI-CNRS, France Université de Rennes 1, France

2:40 PM 4:20 PM Break (GOMD-SII-041-2012) The Benefits of Polyalkylene Carbonate Binders (QPAC®) for Low Temperature Glass Frit or Powdered Glass in Low Temperature Thick Film Applications P. A. Ferraro*, S. Hanggodo, Empower Materials, USA

22 2012 Glass & Optical Materials Division Annual Meeting Final Program Thursday, May 24, 2012

4:40 PM 10:20 AM (GOMD-SII-042-2012) Glass-Ceramic Nanocomposite Scintillators (GOMD-SII-006-2012) Borogermanate glasses with high rare earth for Gamma-ray Spectroscopy oxide content: from optical quality to nanostructuring B. Barta*, Georgia Institute of Technology, USA; J. H. Nadler, Z. Kang, B. Wagner, R. Rosson, V. Sigaev, V. Savinkov, N. Golubev, S. Lotarev*, E. Lopatina, D. Mendeleyev University of B. Kahn, Georgia Tech Research Institute, USA Chemical Technology of Russia, Russian Federation

5:00 PM 10:40 AM (GOMD-SII-043-2012) Crystallization and optical properties in (GOMD-SII-007-2012) A Non-Equilibrium Processing Route for La2O-B2O3-GeO2 Glasses Active Optical Waveguides H. Vigouroux*, E. Fargin, ICMCB, France; B. Le Garrec, CEA, France; M. Dussauze, V. G. Bernard, W. Wu, J. Padalis, J. Kieffer*, Univ Michigan, USA Rodriguez, F. Adamietz, ISM, France; J. Ravaux, R. Podor, ICSM, France; S. Lotarev, V. Sigaev, Mendeleyev University of Chemical Technology, Russian Federation; D. Vouagner, D. De Ligny, 11:00 AM B. Champagnon, LPCML, France (GOMD-SII-046-2012) Bismuth-doped glass optical fibers: a 5:20 PM challenging active optical material for near IR region E. Dianov*, Fiber Optis Research Center, Russian Federation (GOMD-SII-044-2012) Crystallization studies of ZBLAN glasses by DSC and in situ TEM L. Leonard, C. Foerster, UTSI, USA; C. Alvarez*, Northwestern University, USA; R. Weber, Materials Development Inc., USA; A. Petford-Long, Argonne National Laboratory, USA; J. Symposium III: Cross-Cutting Topics Johnson, UTSI, USA; S. Schweizer, Fraunhofer Center for Silicon Photovoltaics, Germany

5:40 PM Session 2: NMR Studies of the Structure of (GOMD-SII-045-2012) Novel Synthesis of Transparent Rare Earth Glass 4 Doped Aluminum Oxide Room: Grand Suites II & III R. J. Pavlacka*, C. Cooper, T. Sanamyan, M. Dubinskiy, G. Gilde, U.S. Army Research Session Chair: Hellmut Eckert, WWU Münster Laboratory, USA 8:00 AM (GOMD-SIII-026-2012) Q3 site variations in a mixed Thursday, May 24, 2012 potassium/magnesium glass using Magic-Angle Flipping (MAF) NMR (Invited) J. H. Baltisberger*, Berea College, USA; E. G. Keeler, D. C. Kaseman, K. J. Sanders, P. J. Symposium II: Optical Materials and Devices Grandinetti, The Ohio State University, USA Session 1: Active Optical Materials 8:40 AM (GOMD-SIII-027-2012) NMR Studies of Nuclear Waste Materials: Room: Salon B Cutting Through Compositional and Morphological Complexity Session Chair: Shibin Jiang, AdValue Photonics Inc (Invited) S. Kroeker*, University of Manitoba, Canada 8:00 AM (GOMD-SII-001-2012) Ceramic Laser Technology: History and 9:20 AM Status (Invited) (GOMD-SIII-028-2012) Structural basis of durability in a transition J. S. Sanghera*, W. Kim, G. Villalobos, L. B. Shaw, C. Baker, Naval Research Lab, USA; M. Hunt, URF, USA; B. Sadowski, R. Miklos, Sotera Defense Solutions, USA; J. Frantz, Naval metal phosphate glass (Invited) S. Chenu, U. Werner-Zwanziger, C. Calahoo, J. Zwanziger , Dalhousie University, Canada Research Lab, USA; I. D. Aggarwal, Sotera Defense Solutions, USA *

8:40 AM 10:00 AM (GOMD-SII-002-2012) Rare-earth Doped Glasses and Fibers for 2 Break Micron Laser S. Jiang*, AdValue Photonics Inc, USA 9:00 AM Session 2: NMR Studies of the Structure of (GOMD-SII-003-2012) Two-dimensional Photonic Crystals on Glass 5 Hybrid Quantum Dots/ Chalcogenide Thin Films and their Emission Room: Grand Suites II & III Properties Session Chair: Annie Pradel, Université Montpellier 2 P. L i n *, N. Patel, V. Singh, L. Kimerling, A. Agarwal, J. Scherer, M. Bawendi, MIT, USA; J. Musgraves, K. Richardson, Clemson University, USA; C. Dimas, Masdar Institute of Science 10:20 AM and Technology, United Arab Emirates (GOMD-SIII-029-2012) Structure of Chalcogenide glasses by 9:20 AM Multinuclear NMR spectroscopy (Invited) (GOMD-SII-004-2012) GeSbS waveguides on Er-TeO2 for optical S. Sen*, University of California, Davis, USA amplication 11:00 AM M. Vanhoutte*, MIT, USA; H. Lin, University of Delaware, USA; V. Singh, P. Lin, MIT, USA; J. Hu, University of Delaware, USA; A. Agarwal, L. C. Kimerling, MIT, USA (GOMD-SIII-030-2012) A Comparison of 10B, 11B NMR and NQR in Borates (Invited) 9:40 AM S. Feller*, D. Crist, V. Khristenko, K. Tholen, N. Barnes, E. Troendle, M. Affatigato, Coe College, (GOMD-SII-005-2012) Structure and nonlinear optical properties of USA; D. Holland, T. Kemp, M. E. Smith, University of Warwick, United Kingdom tellurite thin film glasses 10:20 AM R. Morea, D. Munoz-Martin, J. Gonzalo*, J. Fernandez-Navarro, J. Solis, CSIC, Spain; G. Jose, A. Jha, University of Leeds, United Kingdom; C. Domingo, CSIC, Spain (GOMD-SIII-031-2012) NMR and Industrial Glass Research (Invited) 10:00 AM R. Youngman*, Corning Incorporated, USA Break

2012 Glass & Optical Materials Division Annual Meeting 23 Final Program Thursday, May 24, 2012

Symposium IV: Festschrift to the Glass 10:20 AM (GOMD-SIV-027-2012) Characterisation of the Crystallisation Research Career of Prof. Delbert E. Day Behaviour of Bioactive Glasses with view to Preventing Crystallisation Using Non Isothermal DTA/DSC Methods Session 3: DTA and DSC Methods for Glass R. G. Hill*, A. Al-Noaman, Queen Mary University of London, United Kingdom Crystallization Study 10:40 AM Room: Salons E, F, & G (GOMD-SIV-028-2012) Crystallization behavior of bioactive glasses Session Chair: Edgar Zanotto, UFSCar using differential thermal analysis J. Massera*, S. Fagerlund, L. Hupa, M. Hupa, Åbo Akademi, Finland 8:00 AM (GOMD-SIV-023-2012) On DTA and DSC methods for glass 11:00 AM crystallization study (GOMD-SIV-029-2012) Crystallization of phosphate glasses doped E. D. Zanotto*, UFSCar, Brazil by heavy metal oxides studied by thermoanalytical and 8:20 AM spectroscopic methods L. Koudelka*, I. Rösslerova, Z. Cernosek, P. Mosner, University of Pardubice, Czech Republic (GOMD-SIV-024-2012) DTA/DSC Methods for Studying Glass Formation and crystallization Behavior of Melts and Glasses 11:20 AM (Invited) (GOMD-SIV-030-2012) Crystallization Kinetics of Lithium C. S. Ray*, Missouri S&T, USA Aluinosilicate (LAS) glasses Q. Fu*, R. L. Stewart, J. T. Kohli, Corning Incorporated, USA 9:00 AM (GOMD-SIV-025-2012) Analysis of Crystallization Kinetics (Invited) 11:40 AM K. F. Kelton*, Washington University, USA (GOMD-SIV-031-2012) Chemical reactivity during HLW glass 9:40 AM synthesis:impact of Al2O3, MoO3 A. Monteiro*, S. Schuller, M. Toplis, R. Podor, J. Ravaux, N. Clavier, T. Charpentier, CEA, France (GOMD-SIV-026-2012) Crystal growth rates in glasses determined by a single differential scanning calorimetry run R. M. Reis*, Federal University of Sao Carlos, Brazil; V. M. Fokin, S.I. Vavilov’s State Optical Institute, Russian Federation; E. D. Zanotto, Federal University of Sao Carlos, Brazil

10:00 AM Break

24 2012 Glass & Optical Materials Division Annual Meeting Abstracts

Monday, May 21, 2012 waste cations and the presence of chloride causes repolymerization of the network relative to comparable compositions containing only oxy- gen as the anion. The mechanism of repolymerization is thought to in- Symposium I: Glass Science volve some chloride scavenging and compensating excess alkali thus preventing network modification. Session 1: Glass Structure and Properties I 10:20 AM Room: Salons E, F, & G (GOMD-SI-004-2012) Structure-Terahertz Properties Relationship Session Chair: Randall Youngman, Corning Incorporated in Tellurite Glasses A. A. Monteiro, UNESP-Univ. Estadual Paulista, Brazil; R. J. Koch*, Alfred 9:20 AM University, USA; K. Yukimitu, UNESP-Univ. Estadual Paulista, Brazil; S. K. (GOMD-SI-001-2012) Observation of three elastic phases in heavy Sundaram, Alfred University, USA metal oxide glasses P. Boolchand, S. Chakraborty*, Univ of Cincinnati, USA; M. Malki, University of Tellurite glasses are well known for their linear and nonlinear optical Orleans, France; M. Micoulaut, University of Paris 6, France properties, but their terahertz (THz) properties are not yet fully ex- plored. We have studied the THz properties of glasses in the 80TeO2- Ternary (B2O3)5(TeO2)95-x(V2O5)x glasses are examined in Raman (20-x)-Li O-xWO system for x = 5, 10, 15 and 20% mol and 80TeO - scattering, IR reflectance, mDSC and AC conductivity experiments as a 2 3 2 (20-x)-WO3-xBi2O3 system for x = 2 and 5% mol. Additionally, limited function of composition in the 18% < x < 35% range. Tg(x) are found substitution of Li with Na has also been studied to explore mixed-alkali to decrease as x increases, but the non-reversing enthalpy at Tg, shows a effect in this family of glasses. The glass samples were prepared by reversibility window (RW) in the 23.5% < x < 27.0% range. We identify batching, melting, quenching, and annealing, and characterized using the RW as the rigid but unstressed elastic phase with compositions x < time-domain terahertz spectroscopy (TDS-THz) over a frequency range 23.5% being stressed-rigid, while those at x > 27.0% flexible.125Te and of 0.2– 4 THz. We have also used IR, Raman, and UV-Vis absorption 51V NMR data of Sakida et al, [JPCM 12,2579 (2000)] show isostatic spectroscopic techniques. The refractive index of the glasses was meas- (TeO3 pyramidal , VO4 tetrahedra) units to grow at the expense of ured using an interferometric method. The refractive index generally in- stressed-rigid (TeO4 tbp, and VO5 tbp) ones as x increases to 35%, low- creases with increasing WO3 concentration. We present our THz results ering the count of bonding constraints per atom. Electronic conductiv- along with a preliminary structure-THz properties relationship in this ity is found to increase with x displaying a plateau like behavior in the family of glasses. RW and a logarithmic increase in the flexible phase. The assignment of three elastic phases suggested by the mDSC measurements is confirmed 10:40 AM by NMR and conductivity data (GOMD-SI-005-2012) Synthesis and Structure of ternary chalcogenide glasses in the system BaSe-Ga2Se3-GeSe2 9:40 AM A. Mao*, S. Sen, University of California at Davis, USA; B. Aitken, Corning (GOMD-SI-002-2012) New understanding in TeO2-based glass Incorporated, USA structure by Hyper-Raman/Hyper-Rayleigh for the measure of Raman gain Structure-property relationships in covalent network chalcogenide G. Guery*, clemson university, USA; M. Dussauze, ISM, France; T. Cardinal, glasses in the Ge-As-S/Se/Te systems have been extensively studied over ICMCB, France; F. Adamietz, V. Rodriguez, ISM, France; K. Richardson, clemson the last decades. However, little is known for chalcogenide glasses with university, USA modified networks containing modifier cations such as alkalis or alka- line-earths and glass-forming intermediates such as Ga or In. We have Tellurite based oxide glasses were fabricated and tested as promising synthesized glasses in the BaSe-Ga2Se3-GeSe2 system with a wide range materials for Raman gain applications. Relation between glass structure of BaSe:Ga2Se3 ratios. The structures of these glasses have been investi- and vibrational response is not always an easy task. For development of gated using Raman and multinuclear (77Se and 71Ga) NMR spec- Raman amplifier, understanding of the relation between, glass composi- troscopy. The results indicate that their structures are based on corner tion, glass structure and Raman spectra in multicomponent glasses is an and edge-sharing of GeSe4 and GaSe4 tetrahedra and are characterized important issue. The structural evolution of (100-x)TeO2-xTaO5/2, was by a small concentration of metal-metal bonds between Ga and Ge. The investigated using Raman, Hyper-Raman and Hyper-Rayleigh spectro- concentration of these bonds decreases with increasing BaSe content. scopies. Combination of those vibrational techniques allows evaluating The implications of these structural characteristics in understanding the the structural units responsible for the Raman response. Key informa- compositional variation of Tg and volumetric properties of these glasses tions for understanding relation between optical polarisability and hy- will be discussed. perpolarisability and Raman Response have been evidenced. The results obtained using vibrational spectroscopies show that the Raman cross 11:00 AM sections in the tellurite matrix are not only dependent on the glass com- (GOMD-SI-006-2012) NMR Investigation of Mixed Glass Former position but also on the nature and surroundings of the structural units. Glasses in the Na2S+GeS2+P2S5 System 10:00 AM C. Bischoff*, K. Schuller, S. W. Martin, Iowa State University, USA (GOMD-SI-003-2012) Role of chloride in TeO2-PbO-XCl glass A non-linear and non-additive composition dependent change in ionic structure conductivity is known as the Mixed Glass Former Effect (MGFE). Alkali J. McCloy*, B. J. Riley, C. Windisch, C. P. Rodriguez, J. Vienna, Pacific Northwest ion conducting glasses are of particular interest for use in ion conduc- National Laboratory, USA tive batteries. Sulfide amorphous materials show promise as solid-state electrolytes due to their significantly large alkali ion conductivities as A series of TeO2-PbO glasses were fabricated with a nonradioactive compared to their oxide counterparts. Impedance spectroscopy meas- mixed alkali/alkaline earth/lanthanide chloride waste intended to simu- urements of the yNa2S + (1-y)[xGeS2 + (1-x)PS5/2] glass system exhibit late the waste stream from the electrochemical process used in repro- the MGFE. 31P NMR techniques are used to identify short and interme- cessing of nuclear fuel. The structure of these potential advanced nu- diate range order in these glasses. A structural model based on these re- clear waste glasses was studied with Raman spectroscopy and X-ray sults will be discussed. diffraction. As the waste fraction is increased, the medium-range order in the glass decreased and the tellurite network was depolymerized. At the highest waste loadings, the glass became phase-separated, resulting in a Te-rich phase, a Pb-alkali-chloride-rich phase, and some chloride- containing. Glass network-breaking was caused by the additions of the

2012 Glass & Optical Materials Division Annual Meeting 25 Abstracts

11:20 AM 10:00 AM (GOMD-SI-007-2012) NMR and Raman Studies of Cesium Gallo- (GOMD-SII-009-2012) Effect of Composition and Process on the aluminate Glasses Transient Absorption of ArF Excimer Laser-Exposed Silica C. W. Ponader*, R. E. Youngman, L. K. Cornelius, A. J. Ellison, Corning L. Moore*, C. Smith, S. Schiefelbein, K. Hrdina, J. Moll, Corning Incorporated, Incorporated, USA USA Glasses containing ~30 mol% Cs2O can be made across a range of Transient absorption is photo-induced absorption which changes when Ga/Al ratios. We used NMR to study all three cations in these glasses. Ga the exposing radiation changes intensity. The effects of composition and and Al occupy primarily tetrahedral sites. A small amount of Al(V) is process variables on the transient absorption of high purity fused silica present for charge compensation. Average Al coordination increases as exposed to 193nm excimer laser radiation have been investigated. An Cs content decreases. Cs environment appears insensitive to changes in ArF excimer laser system capable of measuring 193nm absorption dur- the Ga/Al ratio although the chemical shift of Cs decreases with decreas- ing exposure was used to monitor changes in the materials’ absorption ing Cs2O. The Raman spectra give information about medium range as a function of laser fluence. The initial change in absorption and the order. The strongest feature in the spectra can be fit with three bands steady-state absorption as a function of fluence were found to be di- that are assigned to oxygen motions in Ga-O-Ga, Al-O-Al and Ga-O-Al rectly related to the initial OH concentration of the silica, the hydrogen linkages. Intensity variations of these bands with composition suggest concentration, and the temperature at which the hydrogen was loaded that Ga and Al may cluster. The glass properties are most strongly af- into the glass. The trends are explained in terms of the initial silicon hy- fected by the Ga/Al ratio. Refractive index and density both increase dride concentration in the glass which is set by composition and pro- with increasing Ga. Tg decreases with increasing Ga. Cs concentration cessing conditions. Laser darkening-resistant silica is a key material used does not appear to strongly affect the glass properties although the lim- in deep UV optical elements such as microlithography lens systems. ited concentration range explored may mask small effects. 10:20 AM 11:40 AM (GOMD-SII-010-2012) Direct writing of chalcogenide glass (GOMD-SI-008-2012) Structure and Property Studies of Alkali waveguides by femtosecond laser filamentation Borovanadate and Silicovanadate Glasses D. Le Coq*, O. Caulier, University of Littoral côte d’Opale, France; L. Calvez, B. Baker*, B. Dahal, B. Pollpeter, William Jewell College, USA; J. North, J. University of Rennes 1, France; E. Bychkov, P. Masselin, University of Littoral Maldonis, C. Parrish, M. Affatigato, S. Feller, Coe College, USA; S. Kroeker, V. côte d’Opale, France Michaelis, University of Manitoba, Canada Femtosecond laser filamentation in chalcogenide glasses can induce The density and the glass transition of a large number of lithium and ce- permanent refractive index variation (Δn). Spatially resolved measure- sium borovanadate and silicovanadate glasses were investigated. In ad- ments of the resulting Δn are presented. The role of the repetition rate is dition, ESR and NMR (51V, 29Si, 133Cs,and 7Li) studies of these glasses emphasised. It is shown that at high repetition rate the structure is com- were conducted to understand the manner in which the glass formers plex with positive and negative part while at lower one the negative part were modified as well as the way the electronic structure evolved as a disappeared leaving only a smooth structure. The differences are attrib- function of composition. This was complimented by Raman spectro- uted to the free carrier accumulation due to the long plasma lifetime. scopic studies of these systems as well. A resulting structure property The resulting structural modifications after laser writing are studied model is proposed. This work supported by NSF DMR-0904615 and using micro-Raman spectroscopy. By translating the sample in condi- NSF PHY-REU 1004860. tions of moderate repetition rate, homogeneous waveguide can be writ- ten on a centimetre length scale. An analysis of pulse intensity depend- ence on the various repetition rate demonstrates that the magnitude of Symposium II: Optical Materials & Devices Δn can easily be controlled. Session 2: Photosensitivity and Laser Modification 10:40 AM (GOMD-SII-011-2012) Refractive Index Modification Mechanisms of Glasses I in a Doped Phosphate Glass Irradiated with Ultrashort Laser Pulses Room: Salon A Analyzed by Micro-Photoluminescence Session Chair: Denise Krol, University of California, Davis A. Ferrer, CSIC, Spain; D. Jaque, Facultad de Ciencias-UAM, Spain; J. Siegel, A. Ruiz de la Cruz, J. Solis*, CSIC, Spain 9:20 AM (GOMD-SII-008-2012) Temperature Stability Studies of Ultrafast We have analyzed the refractive index changes induced in an Er:Yb- Infrared Laser Induced Index Change for Harsh Environment Fiber doped phosphate glass upon fs-laser irradiation. For such a purpose we Based Sensors (Invited) have studied the spatial distribution of the photoluminescence (PL) fea- C. W. Smelser*, D. Grobnic, R. B. Walker, S. J. Mihailov, Communications tures of Er and Yb in fs-laser written waveguides using a confocal fluo- Research Centre, Canada rescence microscope. The system allows us scanning the sample surface and recording a full PL spectrum for each point of the scanned area. Fiber based sensors, and perhaps most significantly, fiber Bragg gratings Consistent relations among local PL features (intensity and spectral (FBG), are employed in a wide variety of sensing applications. One very peak position), sign of density changes, and local modifications of the common application is temperature sensing. Originally, the fabrication refractive index have been established. The spatially resolved spectral of FBG’s relied on the Ultraviolet (UV) photosensitization mechanism features show that the Er ion emission at 553 nm is more affected by discovered in germanium doped silica by K. O. Hill in 1978. Unfortu- matrix expansion, while the emission of the Yb ion at 976 nm is more nately, Type I UV induced FBG sensors do not survive at temperatures sensitive to the compression of the matrix. The results globally show in excess of 300-500 degrees C and are not suitable for applications that that RE-ions can be used as suitable local probes of the material density require elevated temperatures (500-100 degrees C). Recently, it has been in laser-irradiated glasses. demonstrated that ultrafast Infrared laser induced FBG’s possess tem- perature stability up to 1000 degress C. In this presentation we will dis- cuss our most recent measurements of high temperature stable index change in silica based fibers. We will compare the stability of the various types of induced index change and investigate the upper temperature limit of devices in silica based fiber.

26 2012 Glass & Optical Materials Division Annual Meeting Abstracts

11:00 AM Symposium III: Cross-Cutting Topics (GOMD-SII-012-2012) Laser Patterning of Planar Crystals with High Orientation in Oxide Glass T. Komatsu*, F. Suzuki, K. Ogawa, T. Honma, Nagaoka University of Technology, Session 1: Materials for Fuel Cells and Energy Japan Storage Two-dimensional planar β-BaB2O4 crystals are patterned on the sur- Room: Grand Suites II & III face of Sm2O3-BaO-B2O3 glass by laser irradiation. By scanning Session Chairs: Barrett Potter, University of Arizona; Kelly Simmons- Yb:YVO4 fiber lasers (wavelength: 1080 nm) continuously with a small Potter, University of Arizona step (0.5 μm) between laser irradiated areas, planar crystals having a 9:20 AM smooth surface are patterned, and a preferential growth orientation of crystals is confirmed from linearly polarized micro-Raman scattering (GOMD-SIII-001-2012) An Electride Glass- a semiconducting spectrum and second harmonic intensity measurements. The crystal calcium aluminate glass based on interstitial electron (Invited) growth direction is perpendicular to the laser scanning direction, and H. Hosono*, Tokyo Institute of Technology, Japan this relation is different from the behavior in discrete crystal line pat- An electride is a crystal in which an electrons serves as an anion. We re- terning. The crystal orientation mechanism is discussed from two-di- ported thermally and chemical stable electrides in 2003 employing mensional micro-Raman scattering spectrum measurements in the 12CaO•7Al2O3 (C12A7) composed of 3D-connected sub-nanometer- overlapped region of lasers. The present study proposes that laser-in- sized crystallographic cages. The resulting C12A7 electride shows metal- duced crystallization is applied not only for crystalline dots or lines but lic conduction with (300K)=~1,500Scm-1. We measured electrical con- also for two-dimensional planar crystals with high orientation in oxide duction in C12A7 electride melt in PO2 =10_-24 atm, fining that glasses. metallic conduction occurs in a whole temperature range 2-1600K. Sub- 11:20 AM sequently, the melt was rapidly quenched by a twin-roller to obtain a glass. The resulting glass looks a block colored and exhibited a variable (GOMD-SII-013-2012) Laser Induced Modification in Borates and range hopping type conduction obeying log∝T-1/4 at temperatures Vanadates below ~700K. The present result indicates that C12A7 electide glass is a M. Affatigato*, B. Franta, T. Ahline, S. Yosinski, R. Dongol, W. Lubberden, S. novel class of amorphous semiconductors based on interstitial electrons Feller, Coe College, USA; F. Rocca, G. Dalba, R. Grisenti, Universita di Trento, in the insulating amorphous matrix. C12A7 electride glass has a low Italy workfunction(3.2eV )but chemically inert. We compare the mechanisms responsible for the modification of the 10:00 AM surface and structure of borate and vanadate glasses. In particular, we used both 785 nm and 532 nm lasers to alter the surface morphology, (GOMD-SIII-002-2012) Characterization of BaTiO3 glass- induce crystallization, and, at higher powers, ablate material and drive ceramics/barium titanate composites for high energy storage off water in the alkali borates. The rearrangement of V-O-V bonds is capacitors compared to changes in the borate structure, which is more insulated by X. Su*, D. B. Chrisey, M. Tomozawa, Rensselaer Polytechnic Institute, USA its lack of absorption and by the presence of energy-absorbing water. In High energy storage capacitors require their dielectric layer to possess our work we report on the effect of the laser irradiation in the form of both high dielectric constant and high breakdown strength. Glass/ce- single spots and longer linear regions, and on the effect of preirradia- ramic composites have higher breakdown strength than that of sintered tion. Also, preliminary micro EXAFS measurement will be presented. ceramics alone because glass displaces air-filled voids. However, based This work was supported by the National Science Foundation, grant No. on the dielectric mixing rule, the dielectric constant of mixture is lim- DMR 0904615, and Coe College. ited by the low permittivity of glass phase. In this work, we use BaO- TiO -SiO -Al O glass as the glass phase that crystallizes to BaTiO 11:40 AM 2 2 2 3 3 glass-ceramics by controlled heat treatments, after which the dielectric (GOMD-SII-014-2012) Laser-induced nanostructuring of nickel- constant of the mixture is significantly improved while maintaining doped alkali gallium silicogermanate glasses breakdown strength. Results show that the dielectric constant of this S. Lotarev*, A. Lipatyev, N. Golubev, V. Sigaev, D. Mendeleyev University of glass-ceramics alone after heat treatments (1050oC for 2 h) is around Chemical Technology of Russia, Russian Federation 200, over 10 times that of glass. Ni2+-doped alkali gallium silicogermanate glasses nanocrystallized by 10:20 AM heat treatment have been recently shown to be an efficient optical media β for broadband NIR luminescence. In the present study, 7.5Li2O- (GOMD-SIII-003-2012) Glass and ” Alumina Ceramic Composites 2.5Na2O 20Ga2O3-35SiO2-35GeO2 glass doped with NiO (0.1-1 for the Sodium-Sulfur Battery mol.%) were heated up to 400-600 Celsius degree and irradiated with R. Christensen*, Iowa State University, USA the focused beam of the pulsed copper vapor laser (511 nm and 578 The sodium-sulfur battery is one of many possible solutions to inter- nm) and the continuous wave Nd:YAG laser (1064 nm). For both lasers, mittent renewable energy sources like solar and wind energies. However, glass areas irradiated at certain conditions remained transparent but it has a major drawback of an operating temperature of 300oC. In addi- drastically changed their color. The laser-induced modification mecha- tion, the most likely cause of cell failure is mechanical fracture of the nism of the glass is shown to be similar to the earlier reported bulk solid state electrolyte, β” Alumina. We have focused on the improve- nanocrystallization migration of Ni2+ ions into the precipitating ment of the mechanical properties of β” Alumina electrolyte through nanocrystals. The nanostructured waveguides fabricated by laser irradi- the creation of β” Alumina Glassy composites while maintaining or im- ation near the glass surface are promising media for elaboration of NIR- proving the ionic conduction capabilities at ambient temperature. Pre- range short laser amplifiers for integrated . vious studies of β” Alumina/Glass composites, in the literature, have struggled to create a dense, low porosity sample with ionic conductivity comparable to that of unmodified β” alumina. The effects of Hot Isotac- tic Pressing of mixed glass and alumina pellets and surface penetration of cold pressed alumina pellets by glass have been investigated in order to create a dense and therefore more conductive material than can be achieved by cold pressing.

2012 Glass & Optical Materials Division Annual Meeting 27 Abstracts

10:40 AM model was also employed to verify the good chemical stability of these (GOMD-SIII-004-2012) Lead-free Sealing Glass: Low Tflow & Low Sr-containing crystalline. CTE O. A. Prokhorenko*, Laboratory of Glass Properties, USA Session 4: Liquid Synthesis and Sol-gel Derived There are known lead-containing glasses for making glass-to-metal seals Materials I with quite favorable combination of low temperature of flat flow Room: Salon B (Tflow) and low CTE. Environmental regulations require excluding lead Session Chairs: Brian Riley, Pacific Northwest National Laboratory; from glass and other materials. The companies has begun to replace David Musgraves, Clemson University PbO2 by other, non-toxic oxides, such as P2O5, Bi2O3, SnO2, etc. Ob- taining lead-free sealing materials with CTE ranging from 70*10^-7 to 9:20 AM 95*10^-7, and flow temperature less than 500oC, however, was only (GOMD-SIII-035-2012) Unique Opportunities in Chalcogels: Porous possible by adding so-called fillers to low-melting glasses having CTE Semiconducting Metal-Chalcogenide Aerogels (Invited) above 100*10^-7. The present paper describes new lead-free seal glass M. Kanatzidis, B. D. Yuhas*, S. Bag, Northwestern University, USA system, which is characterized by combination of low CTE and low Tflow. Some glass-to-glass and glass- to-metal seals obtained by using Chalcogels are a novel class of porous aerogel materials possessing high new glass-sealants are described as well. internal surface area. Their open polymeric random frameworks are constructed by chalcogenide building units linked with transition as 11:00 AM well as main group metal ions. Gels are obtained using a slow metathe- (GOMD-SIII-005-2012) Rare-earth containing glass-ceramic sealants sis reaction and are transformed to aerogels after supercritical drying for solid oxide fuel cells with liquid carbon dioxide. These low density sponge like materials can A. Goel*, Pacific Northwest National Laboratory, USA; J. M. Ferreira, University absorb conjugated organic molecules, mercury ions and can preferen- of Aveiro, Portugal tially adsorb CO2 over H2, which illustrates their high potential as gas separation media. Additionally, chalcogels can be synthesized with bio- The sintering behavior of rare-earth containing alkaline-earth alumi- mimetic transition metal clusters such as [Fe4S4] or [Mo2Fe6S8] inte- nosilicate glass-ceramics has been studied for sealing application in grated seamlessly into the chalcogenide semiconducting matrix. These solid oxide fuel cells (SOFC). The in situ follow up of sintering behavior materials have narrow energy-gaps in the range of 0.2-2.0 eV depending of glass powders has been done by high temperature - environmental on the building units, and promise unique opportunities in optoelec- scanning electron microscope (HT-ESEM) and hot-stage microscope tronic, sensing, photosynthetic and photocatalytic applications. (HSM) while the crystalline phase evolution and assemblage has been analyzed by x-ray diffraction (XRD) and scanning electron microscopy 10:00 AM (SEM). The increase in lanthanide content in glasses suppressed their (GOMD-SIII-036-2012) Chalcogen-based aerogels as sorbents for tendency towards devitrification, thus, resulting in glass-ceramics with radioiodine high amount of residual glassy phase (50 - 96 wt.%) which is expected B. J. Riley*, W. C. Lepry, J. Chun, D. M. Strachan, Pacific Northwest National to facilitate their self-healing behavior during SOFC operation. The Laboratory, USA long term thermal stability of glass-ceramic seals and their chemical in- teractions with SOF components will be discussed. In the past, silica-based aerogels have been researched for nuclear waste capture and immobilization. However, only recently, a new type of aero- 11:20 AM gel has been brought into this arena, a chalcogen-based aerogel termed a chalcogel. These types of aerogels are produced with a sol-gel technique (GOMD-SIII-006-2012) Optical properties of La2O3-Nb2O5-MOx glasses prepared by containerless processing combining separate solutions containing ionic forms of the precursors, A. Masuno*, The University of Tokyo, Japan; K. Yoshimoto, The University of letting them gel (up to a month), removing the byproducts through Tokyo, Japan; H. Inoue, The University of Tokyo, Japan; Y. Watanabe, The rinsing, and then supercritically drying to preserve the pore structure. University of Tokyo, Japan These aerogels are generally sulfide-based and have specific surface areas of > 400 m2/g and are made with heavier elements such as Ge, Sn, Mo, La2O3-Nb2O5-MOx glasses were fabricated by containerless processing and W. In early tests at PNNL, we showed that these materials could be (M = Al, Ta, Ti). The glasses were colorless and transparent in the visible used as sorbents for iodine gas. Thus, they are currently being evaluated to infrared region. The refractive indices ranged from 2.0 to 2.35. The as potential sorbents for radioactive iodine that is evolved from nuclear Abbe number increased from 20 to 40 by adding MOx to La2O3-Nb2O5 fuel reprocessing. A summary of the on-going work in this area will be binary glasses. The effect of the addition of MOx were investigated by presented. using optical parameters obtained from the Drude–Voigt relationship.

These results demonstrated that the La2O3-Nb2O5-MOx ternary glasses 10:20 AM would be key materials to produce innovative optical components. (GOMD-SIII-037-2012) Silver-functionalized silica aerogels for effective capture and safe storage of gaseous radioiodine (Invited) 11:40 AM J. Matyas*, G. E. Fryxell, M. J. Robinson, PNNL, USA (GOMD-SIII-007-2012) Development of Sealing Glass for Solid Oxide Fuel Cells- Chemical Stability of Sr-containing Crystalline To support the future expansion of nuclear energy, various materials T. Zhang*, Q. Zou, D. Tang, Fuzhou University, China; H. Yang, National United have been investigated to capture and immobilize radiological iodine- University, Taiwan 129 form reprocessing off-gas. In most cases, however, the materials that are effective for capturing iodine cannot subsequently be sintered/den- Many Glass-ceramics have been developed for solid oxide fuel cell sified to create a stable composite that could be a viable waste form. In (SOFC) sealing application. However, the chemical stability of glasses in contrast, the functionalized silica aerogels can be effective for capturing the operational temperature range of solid oxide fuel cells (SOFCs) still radioiodine and, once laden with iodine, these materials can be consoli- remains challenging. In this paper, the nanoscale SrO-SiO2 glass was dated into a durable silica glass. Our silver-functionalized silica aerogels prepared by sol-gel method. Some Sr-containing crystalline phases, e.g., exhibit decontamination factors in excess of 10000 in off-gas streams SrSiO3 and Sr2SiO4, can be formed from the glass matrix via different containing 4.2 ppm of iodine and have a maximum iodine sorption ca- heat treatment routines. The chemical stability of these crystalline pacity of 47.6 mass% which is more than 2 times higher than the state- phases in the operational temperature range of SOFCs was evaluated by of-the-art silver reduced mordenite. In addition, more than 92 mass% the reaction between glass-ceramics and Cr2O3 powders. The results of the iodine was retained in densified aerogels after thermal sintering showed that the chemical stability of glass-ceramics can be dramatically with pressure assistance at 1200°C for 30 min. improved with increasing crystalline content. The thermodynamic

28 2012 Glass & Optical Materials Division Annual Meeting Abstracts

11:00 AM 10:20 AM

(GOMD-SIII-038-2012) High-Halide Minerals as a Salt Waste Form (GOMD-SIV-014-2012) The structural behavior of Nb in Nb2O5- W. Lepry*, J. Crum, B. Riley, J. Matyas, Pacific Northwest National Laboratory, NaPO3 glasses by X-ray and neutron diffraction USA U. Hoppe*, Universität Rostock, Germany; L. Delevoye, L. Montagne, Université des Sciences et Technologies de Lille, France; M. von Zimmermann, Deutsches In order to maximize the efficiency of nuclear power production, used Elektronen-Synchrotron DESY, Germany; A. Hannon, Rutherford Appleton nuclear fuel will likely be reprocessed to recover fuel value. One of the Laboratory, United Kingdom proposed reprocessing techniques is an electrochemical separations 31 17 process that produces a spent mixed-chloride salt as a waste stream. A The structure of Nb2O5-NaPO3 glasses was already studied by P, O, commonly studied waste form for immobilizing this salt waste is a zeo- 93Nb NMR and Raman spectroscopy. Several glass properties such as lite that, when pressed and fired, forms the environmentally-stable so- mass density or glass transition temperature change linearly with the dalite structure. A glass binder is then added to this sodalite (~25 Nb2O5 content. Recently, these glasses have been discussed as candidates mass%) and the mixture is fired at temperatures above 900°C. Here, we for Raman gain applications. Here, the behavior of the Nb-O and Nb- demonstrate an alternative method, a room-temperature sol-gel Nb distances is analyzed by results from X-ray and neutron diffraction method, to produce a sodalite. Since the particles achieved with the sol- experiments. The Nb-O coordination number is six throughout all glass gel process are small (~1–5 μm), we have demonstrated that even small compositions. Three different Nb-O distances are resolved which do not additions of a glass binder (1–5 mass%) allow for a significant decrease change for glasses of small Nb2O5 content. The Nb-O and Nb-Nb dis- in the porosity in fired pellets. This method increases the overall waste- tances characteristic of Nb-O-Nb bridges become significant in the dif- loading over the baseline approach. Here, we discuss results from a fraction results for glasses with Nb2O5 content greater than 20 mol%. A study on a series of glass binders to improve densification. model of the structural evolution of the network formed of NbO6 and PO4 groups is discussed which is based on the results from NMR, 11:20 AM Raman spectroscopy, diffraction, and the comparison with related crys- (GOMD-SIII-039-2012) Sol-gel synthesis and processing of tal structures. polysilsesquioxane coatings using size exclusion and sintering (Invited) 10:40 AM D. A. Loy*, The University of Arizona, USA (GOMD-SIV-015-2012) Structure of cerium aluminophosphate glasses: diffraction studies and molecular dynamics simulations Sol-gel processed polysilsesquioxanes provide the opportunity to pre- J. Du*, L. Kokou, University of North Texas, USA; J. Rygel, C. Pantano, the Penn pare asymmetric membranes with tailored separation layers for gas and State University, USA; L. Skinner, C. Benmore, Argonne National Laboratory, chemical separations or even for barrier coatings. However, sol-gel dep- USA osition of the top coating on such membranes is often accompanied by infiltration of the colloidal particles into the porous ceramic supports Rare earth aluminophosphate glasses find wide technological applica- making determination of final membrane thickness difficult. We have tions. Cerium containing aluminophosphate glasses in particular are side-stepped the problem by preparing and depositing pre-formed par- known to provide improved radiation resistance for glasses in solar en- ticles of polysilsesquioxanes with diameters larger than the pores in the ergy and space applications. Understanding the atomic structure of support. The particles can then be thermally sintered into a glassy, de- these glasses are critical to the understanding the optical and radiation fect free coating at relatively mild temperatures (<300 °C) without infil- resistance properties of these glasses. In this paper, the structure of a se- tration. Furthermore, we have prepared fluorescent particles that allow ries of cerium aluminophosphate glasses has been studied by combining us to confirm the formation of a thin coating without infiltration and X-ray and neutron diffractions and using MD simulations for systems obtain accurate membrane thicknesses using fluorescence microscopy. of about 13,000 atoms to investigate aluminum and cerium ions envi- ronment and their distribution. The simulation results were compared with the diffraction data and to interpret the experimental results. It was Symposium IV: Festschrift to the Glass found that cerium ions were preferentially surrounded by phosphorus Research Career of Prof. Delbert E. Day oxygen tetrahedra in the second coordination shell. Variation of alu- minum coordination as a function of composition has also been investi- Session 2: Phosphate Glasses: Their Structures, gated. Properties and Applications I 11:00 AM Room: Salon C (GOMD-SIV-016-2012) Investigation of electrical properties of iron Session Chair: Richard Brow, Missouri S&T phosphate glasses in Croatia A. Mogus-Milankovic*, A. Santic, L. Pavic, Ruder Boskovic Institute, Croatia 9:40 AM Electrical properties of iron phosphate glasses have been investigated in (GOMD-SIV-013-2012) The Atomic and Magnetic Structure and Croatia for more than one decade. Polaronic conduction in these glasses Dynamics of Iron Phosphate Glasses (Invited) takes place by electron hopping from Fe(II) to Fe(III) ions. However, by A. C. Wright*, University of Reading, United Kingdom altering composition (addition of MoO3, Cr2O3, Bi2O3, PbO, Na2O) the Neutron scattering techniques have been employed to investigate the electrical conductivity of iron phosphate based glasses may vary for atomic and magnetic structure and dynamics of four iron phosphate many orders of magnitude. Recently, the influence of nanocrystalliza- glasses with nominal compositions between 30 and 44 mol. % Fe2O3. tion on the electronic conductivity of iron phosphate glasses has been Neutron diffraction data show that the atomic structure includes iron in studied. The analysis shows a drop in electrical conductivity for two or- at least three charge/co-ordination states, viz. tetrahedral Fe3+, octahe- ders of magnitude in an early stage of nanocrystallization. At higher dral Fe3+ and 6-fold co-ordinated (trigonal-prismatic and/or octahe- concentration of nanocrystallites the continuous interfaces are created dral) Fe2+. At low temperatures, neutron magnetic diffraction experi- which enhances the electrical conductivity. This presentation will give ments confirm the presence of speromagnetic ordering. The data are an overview of our recent studies of electronic and ionic transport in compared to two structural models, the first based on crystalline FePO4, iron phosphate glasses and its crystallized counterparts. with alternating FeO4 and PO4 tetrahedra, and the second including (Fe3O12)16- clusters as found in crystalline Fe3(P2O7)2, and it is con- cluded that the structure is much more complex than either of these simple models would suggest.

2012 Glass & Optical Materials Division Annual Meeting 29 Abstracts

11:20 AM vastly improved, mainly due to the development of high-flux neutron (GOMD-SIV-017-2012) Water diffusion into phosphate glasses sources, and as the result of improvements in both neutron detectors T. Terashima*, M. Tomozawa, Rensselaer Polytechnic Institute, USA and their associated electronics and data storage. The present paper re- views the role of modern neutron scattering techniques in the study of Shear modulus of glasses are known to be related to the activation en- the structure and dynamics of inorganic glasses and other amorphous ergy of molecular diffusion into glasses. In this study, water diffusion solids. The subjects include neutron diffraction (structure), magnetic into phosphate glasses with various MgO contents from 45mol% to diffraction (magnetic ordering), inelastic scattering (vibrational density 55mol% was investigated at low temperature from 175°C to 250°C using of states), quasi-elastic scattering (molecular rotation) and small-angle FTIR to reveal the relationship between the activation energy of water neutron scattering (longer-range fluctuations). The information that diffusion and shear modulus. The effective diffusion coefficient was cal- can be extracted using the various neutron scattering techniques is illus- culated from the time dependence of the water uptake. The effective dif- trated with examples taken from recent papers by the author and his co- fusion coefficient in magnesium metaphosphate glass at 200°C was workers. found to be 2.6×10-10 cm2/s and its activation energy of water diffusion was 87kJ/mol. The activation energy of water diffusion increased with 2:40 PM increasing MgO contents, i.e. as shear modulus increases. The effect of (GOMD-SI-012-2012) Formation of Ga-As colloids in Glasses Al2O3, Cr2O3 and SiO2 addition will also be discussed. K. Bornstein*, S. K. Sundaram, Alfred University, USA Alkali galliosilicate glasses were used to study reduction of Ga-As in a Symposium I: Glass Science glass matrix. The colloids were formed by heat treatment in a hydrogen- deutrium atmosphere. The heat-treatment temperature, duration, and Session 1: Glass Structure and Properties II H2-D2 ratio were varied in optimizing the nucleation and growth processes. X-ray diffraction, differential thermal analysis, low frequency Room: Salons E, F, & G Raman scattering, UV-Vis-NIR, and FTIR spectroscopies were used to Session Chair: Sabyasachi Sen, University of California, Davis study the processes. Hydroxyl formation in these glasses will be corre- 1:20 PM lated to the formation of Ga-As colloids. These processes can be de- scribed using well-established models. (GOMD-SI-009-2012) Characterizing Amorphous Synthetic and Natural Spider Silk Fibers Using X-ray Diffraction (Invited) 3:20 PM C. J. Benmore*, Argonne National Lab, USA; F. Teulé, Utah State University, (GOMD-SI-013-2012) Glassy and Amorphous Drugs USA; W. Weber, Arizona State University, USA; R. Lewis, Utah State University, R. Weber*, Materials Development, Inc., USA; C. J. Benmore, Argonne National USA; J. L. Yarger, Arizona State University, USA Laboratory, USA; A. N. Tailor, S. K. Tumber, Materials Development, Inc., USA; Potential applications of amorphous spider silk include ligament re- C. A. Rey, Charles Rey, Inc, USA; L. S. Taylor, S. R. Byrn, Purdue University, USA; placement and tendon repair materials. Here we have performed high J. L. Yarger, B. Cherry, Arizona State University, USA energy x-ray scattering measurements on naturally amorphous Nephila Efficient absorption of a drug is critical to delivering it to body tissue. Clavipes, Argiope Aurantia and Black Widow spider silks, as a basis for Glassy and amorphous forms of pharmaceuticals often exhibit signifi- biopolymer design. The low absorption and negligible radiation dam- cantly increased solubility, faster dissolution rates and higher bioavail- age associated with high energy x-rays (>100 keV) make the pair distri- ability compared to their crystalline counterparts. We used containerless bution function technique an ideal probe of short and intermediate processing by acoustic levitation to investigate the amorphization and range order in biomaterials. Similarities and differences in the x-ray vitrification of low molecular weight pharmaceutical compounds. Satu- data between different species are compared to varying silk properties. rated solutions and supercooled liquids were investigated. Measure- The results of x-ray fiber diffraction from natural silk fibers are also ments were made on the bench and in-situ using high energy x-ray dif- compared to those obtained from synthetic spider silk-like fibers. fraction. Work is in progress to study the processed materials using 2:00 PM NMR and neutron diffraction. This talk will outline the methods, pres- ent results and discuss ongoing activities to optimize development of (GOMD-SI-010-2012) Mechanical Property of Nanoporous Glasses amorphous pharmaceutical materials using containerless processing. Characterized by X-ray Scattering S. Dong, M. Sundararajan, G. Chen*, Ohio University, USA 3:40 PM Nanoporous glasses derived from the so-gel method are an important (GOMD-SI-014-2012) Structural study on anisotropic phosphate class of materials due to their interesting properties such as large surface glass by polarized Raman spectroscopy area and controllable pore morphology. In this talk, we report develop- S. Inaba*, S. Ito, Tokyo Institute of Technology, Japan ment of a new method for characterizing the mechanical property of Alkali meta-phosphate glass fibers prepared with a fiber elongating nanoporous glasses by X-ray scattering. This method is based on capil- method, showed anisotropic structural alterations which were caused by lary condensation where water spontaneously enters or retreats from mechanical history, as compared with the corresponding isotropic the pores as water partial pressure changes. Because of the nanosized glasses. Composition dependence of birefringence caused by the pores, extremely large capillary pressure exerts on the amorphous pore anisotropic structure was predominantly affected by the kind of net- walls, causing mechanical deformation of the materials. By measuring work modifier. Structural studies of the anisotropic were per- the capillary-pressure-induced strain as a function of relative humidity, formed by the polarized Raman spectroscopy. The polarization depend- we were able to derive the Yong’s moduli of the nanoporous materials. It ence of Raman scattering intensities was obtained by varying the is found that the Yong’s moduli of the porous materials depend strongly polarization direction of incident radiation. From the comparison of on the porosity, pore morphology and pore wall structure. Our study the polarized Raman spectra of KPO3 crystal which has a uniaxial ori- demonstrates a new method for characterizing the mechanical property ented structure, we revealed that the anisotropic glass fiber was made up of nanoporous materials. by long chains of PO4 tetrahedra, and the axes of these chains had a 2:20 PM strong preference for lying along the fiber axis direction and the out of chain PO2 units were oriented to the perpendicular to the fiber axis di- (GOMD-SI-011-2012) What can Neutron Scattering Techniques tell rection us about the Structure and Dynamics of Inorganic Glasses? A. C. Wright*, University of Reading, United Kingdom Since their first application to the vitreous state during the 1960s, the quality of the data obtained from neutron scattering experiments has

30 2012 Glass & Optical Materials Division Annual Meeting Abstracts

4:00 PM Symposium II: Optical Materials & Devices (GOMD-SI-015-2012) Mixed alkali effect on the hardness and cracking of glass by Vickers indentation A. Mohajerani*, J. W. Zwanziger, Dalhousie University, Canada Session 2: Photosensitivity and Laser Modification of Glasses II Three series of mixed alkali glasses (Na/Li) were studied to investigate mixed alkali effect on the Vickers indentation of glass. Hardness was Room: Salon A measured as the ratio of load to dent area on the planes of indentation. Session Chair: Mario Affatigato, Coe College Cracking was investigated by measuring the length of cracks extending 1:20 PM in radial direction outward the dents. All the glass series exhibited nega- tive deviations of hardness and crack length from additivity. This mixed (GOMD-SII-015-2012) Optimization of Energy Deposition in alkali effect on hardness and cracking was attributed to the reduced Femtosecond Laser Processing of Dielectrics Using Plasma Imaging plastic flow of mixed alkali glasses, and the combined effect of fracture Techniques (Invited) toughness and residual stresses, respectively. Fracture toughness and J. Solis*, Instituto de Optica-CSIC, Spain residual stresses were calculated using a semi-empirical model. Residual The presentation will provide an overview of our recent work regarding stresses did not correlate with crack lengths, and exhibited linear varia- the use of fs-resolved microscopy for the assessment of the interaction tions from one single alkali glass to the other. Fracture toughness how- of ultrashort laser pulses with glasses and other dielectrics. This tech- ever showed positive deviation from additivity, suggesting the presence nique can be adapted in order to reach experimental conditions equiva- of mixed alkali effect on the fracture toughness of glass. lent to those used during fs-laser processing for the production of pho- tonic components. Its use has enabled to unveil a number of complex 4:20 PM interaction mechanisms including non-linear self-focusing, multiple μ (GOMD-SI-017-2012) 3D -Brillouin mapping of a Vickers beam filamentation, and pre-focal energy depletion that act as impor- indentation in a soda-lime silicate glass tant energy loss channels that deteriorate the spatial distribution of the H. Tran, University of Montpellier II, France; D. Vandembroucq, ESPCI/Paris deposited laser energy. Detailed studies performed with this technique 6/Paris 7, France; B. Rufflé*, University of Montpellier II, France show how these undesirable effects can be minimized by adjusting the As brittle materials, glasses experience plasticity under high-stress con- processing parameters. As a consequence, the energy can be deposited ditions at small scale. The plastic flow is then accompanied by an irre- much more efficiently and confined in the linear focal volume region, versible densification. This “micro-ductile” behavior remains ill under- leading to structures with highly optimized performance. stood. Data obtained through Instrumented indentation tests are 2:00 PM unfortunately far too limited to characterize unambiguously the me- chanical response of the glass. It is thus highly desirable to develop in- (GOMD-SII-016-2012) Aberration correction and formation of novative μ-mechanics experiments which could image the stress state of complex crystal geometries by spatial light modulation of the glass surface after an indentation. The comparison to the output of a femtosecond laser finite element simulation would give then a much more severe criterion A. Stone*, Lehigh University, USA; M. Sakakura, Y. Shimotsuma, K. Miura, for a constitutive law validation. We show in this paper that Brillouin μ- Kyoto University, Japan; V. Dierolf, H. Jain, Lehigh University, USA spectroscopy can provide such new information. 3D iso-density maps of Femtosecond (fs) lasers can induce crystallization of optically active the area beneath a Vickers micro-indentation have been obtained in a phases inside glass in 3D, a powerful application of nonlinear optics in soda-lime silicate glass, demonstrating the potential of the technique. materials processing. By relying on multiphoton absorption for modifi- Residual stress is also discussed as well as new in situ high-pressure Bril- cation at the focal point, power loss due to conventional absorption of louin data. the unfocused beam is negligible regardless of focal depth. However, spherical aberration due to refractive index mismatch still distorts the 4:40 PM beam profile, causing the size and shape of crystals to vary as focal depth (GOMD-SI-018-2012) Crack Growth in Photomultiplier Tube is increased. We have used spatial light modulation (SLM) to correct for Glasses for Neutrino Detection aberration during fs laser crystallization, reducing variation of the crys- R. Dongol*, S. K. Sundaram, Alfred University, USA; M. Diwan, Brookhaven tal cross-section. SLM was also utilized to crystallize at multiple and National Laboratory, USA moving focal points in order to produce complex crystal geometries like It is well documented fact that glass materials in the influence of mois- curved lines, junctions (e.g. interferometer), and planar crystals. Despite ture and constant state of stress are susceptible to subcritical crack some limitations, SLM provides substantially increased versatility in fs growth. The crack size increases until the stress intensity at the crack tip laser crystallization. exceeds the fracture toughness or critical stress intensity factor and fail- 2:20 PM ure occurs. This phenomenon is known as stress corrosion and is a form of static fatigue. We are studying the static fatigue testing of Photomul- (GOMD-SII-017-2012) Creating Optical Waveguides in Glass with tiplier Tube (PMT) glass composition, primarily borosilicate glass com- Femtosecond Cylindrical Vector Beams positions, using various indentation techniques. Our objective is to un- N. Troy*, University of California Davis, USA; H. Zhang, J. I. Dijkhuis, Utrecht derstand the crack growth behavior under high moisture environment. University, Netherlands; D. M. Krol, University of California Davis, USA It is essential that the crack growth is minimized to achieve effective fail- We have investigated the use of cylindrical vector beams for femtosec- ure prediction. We will present our preliminary crack growth results. ond laser waveguide writing in glass. When focused, cylindrical vector The research is supported by Brookhaven National Laboratory under beams can produce torus-shaped focal spots with cylindrically symmet- the Long Baseline Neutrino Experiment (LBNE). The strength and life- ric polarization. We have fabricated waveguides with these beams in time prediction of the PMT glass are crucial to the success of the exper- fused silica and IOG-1, a commercial phosphate glass from Schott, Inc. iment. These two glasses represent different types of fs-laser modification be- havior. When using standard Gaussian beam focusing with linearly po- larized light, fused silica exhibits a positive change in its index of refrac- tion in the modified region, whereas in IOG-1 a negative change in the index of refraction occurs. In this talk we will provide a background on cylindrical vector beams and their focusing properties as well as experi- mental results of waveguide fabrication with these beams. The struc-

2012 Glass & Optical Materials Division Annual Meeting 31 Abstracts tural changes in these glasses have also been investigated using fluores- 2:20 PM cence and Raman spectroscopy. (GOMD-SIII-010-2012) Optical Absorption Enhancement in Thin Film Solar Cells Using High-index Glass Light Trapping Backside 2:40 PM Structures (GOMD-SII-018-2012) A Phenomenological model on photo- Y. Zou*, J. Hu, H. Lin, University of Delaware, USA induced surface structure in Arsenic Sulfide C. Lu*, C. Arnold, Princeton University, USA Light trapping (LT) designs are essential for thin film cells due to the low absorption of near infrared light. In this work, we theoretically ana- Chalcogenide materials, such as Arsenic Sulfide (As2S3), are well- lyzed and numerically designed novel LT grating structures which pro- known for their sensitivities to external stimuli, especially illumination. vides LT enhancement well exceeding the Lambertian limit, by breaking Among various photo-induced phenomena, this paper focused on mass the structural symmetry in conventional grating designs to maximize transport issues. Thin films of As2S3 respond to non-uniform illumina- the guided mode contribution to optical absorption. We choose chalco- tion by changing their surface morphologies. The volume expansion genide glasses (ChGs) as the grating material to leverage their unique can be as large as 0.05% with appropriate illumination. However, there optical and structural properties, such as high refractive indices, trans- is still much debate on the mechanism for this process. We present a new parency in the near-IR, and amorphous structure amenable to low cost model describing the surface structural modification by employing the imprint patterning. The LT enhancement in Si solar cells was numeri- incompressible fluid equation, driven by a photo-induced pressure. This cally studied by optimizing the grating parameters. The results showed equation, derived without any consumption of the microstructure of that the optimized 1-D gratings lead to 30% increase in optical path As2S3, is shown to be sufficient and effective in predicting many aspects length, which represents 42% relative improvement compared to the of photo-induced surface relief formation. path length enhancement factor using conventional LT structures. Symposium III: Cross-Cutting Topics Session 1: Nuclear Waste Glass Chemistry and Processing Session 1: Solar Energy Materials Room: Grand Suites II & III Room: Grand Suites II & III Session Chairs: James Marra, Savannah River National Laboratory; Session Chairs: Barrett Potter, University of Arizona; Kelly Simmons- John Vienna, PNNL Potter, University of Arizona 3:20 PM 1:20 PM (GOMD-SIII-011-2012) A Roadmap to High Level Waste (GOMD-SIII-008-2012) Material requirements for long-term stable Vitrification in the U.S Dye-sensitized Solar Modules (Invited) J. Vienna*, Pacific Northwest National Laboratory, USA; J. Marra, Savannah K. F. Jensen*, W. Veurman, H. Brandt, R. Loayza-Aguirre, K. Bialecka, A. Hinsch, River National Laboratory, USA Fraunhofer Institute for Solar Energy Systems ISE, Germany Nuclear power plays a key role in maintaining current worldwide energy In 2011 the transfer of the Dye-sensitized Solar cell (DSC) from lab to growth while minimizing the greenhouse gas emissions. A disposition large area module production was demonstrated by Fraunhofer ISE. path for used nuclear fuel (UNF) must be found for this technology to The first functioning 60cmx100cm internally interconnected DSC achieve its promise. One likely option is to reprocess UNF and immobi- module on one glass substrate was shown, which raises great hope for lize the high-level waste (HLW) by vitrification. Vitrification is the tech- the near future commercialization of DSC modules. The DSC is aimed nology of choice for immobilizing HLW from defense and commercial for the building integrated photovoltaic market, offering aesthetical de- fuel reprocessing around the world. Recent advances in both recycling sign freedom and multipurpose functions of shading, light filtering and technology and vitrification show great promise in closing the U.S. nu- electricity generation. Our presentation will comprise the working prin- clear fuel cycle in an efficient fashion. This presentation summarizes the ciple of the DSC, the fabrication steps and a microscopic material analy- recent trends, developments, and future options in waste vitrification sis. Focus is placed specifically on the Transparent Conductive Oxide for both defense waste cleanup and closing the nuclear fuel cycle in the (TCO) and the glass frit used as internal cell insulator and outer seal for United States. separating the liquid electrolyte from ambient environment. The re- moval of defects as well as specific TCO is crucial for further production 3:40 PM processes with screen printing of active layers and the sealing material. (GOMD-SIII-012-2012) Structural studies of nuclear waste form glasses and glass ceramics by solid-state NMR and Raman 2:00 PM spectroscopies (GOMD-SIII-009-2012) Engineering CdTe-ZnO nanocomposites for T. Ohkubo*, Y. Iwadate, Chiba University, Japan photovoltaic device applications We investigate the network structure of simplified nuclear waste form J. Kana Kana*, R. Beal, B. Potter, University of Arizona, USA glasses, which have varying a series of mole ration La2O3/B2O3 (series Nanoscale composite materials are of significant interest in the develop- 1) and Na2O/B2O3, by multi nuclear magin-angle spinning (MAS) nu- ment of new options for next-generation photovoltaic(PV) devices.The clear magnetic resonance (NMR) and Raman spectroscopy. The struc- present work focuses on recent developments in the design, fabrication tural properties of such glasses are showon to depend on the fraction of- and characterization of CdTe-ZnO and CdTe-ZnMgO thin film four-coordinated boron atoms and on the fraction of silicate tetrahedra nanocomposites produced using sequential RF sputtering. The deposi- connecting structure. tion technique enables close control of the semiconductor nanophase spatial distribution within the oxide matrix and thus allows the 4:00 PM nanocomposite spectral absorption and long-range charge transport (GOMD-SIII-013-2012) Sulfate Retention in Simulated Nuclear behavior,both critical factors to PV energy conversion,to be engi- Waste Glasses neered.External quantum efficiency spectra from thin film PV devices K. Bond*, S. Sundaram, Alfred University, USA; K. M. Fox, J. W. Amoroso, in which these materials are introduced as heterojunction elements, Savannah River National Laboratory, USA highlight the impact of nanocomposite structure on the spectral charac- Sulfate present in nuclear wastes limits the amount of waste that can be teristics of the energy conversion process.The interplay between the spa- immobilized (waste loading) in the glass waste form. This study has tial distribution of the semiconductor nanophase relative to the hetero- been undertaken to determine the potential impact of glass frit additives junction plane appears to play a key role in the response observed. in enhancing the retention of sulfate in glass. The baseline borosilicate

32 2012 Glass & Optical Materials Division Annual Meeting Abstracts glass system and the simulated nuclear waste components are based on a variety of simulated Savannah River Site HLW feeds have been suc- developments at the Savanna River National Laboratory (SRNL). Sulfur cessfully completed over the past few years. These campaigns provided will be introduced into these glasses in the form of sodium sulfate, demonstration of the potential of the CCIM to increase waste loading which will be normalized into the glass network to target sulfur levels of and, thus, increase waste throughput. 0.8 and 1.0 weight percent. To increase sulfate solubility, additions of barium, lead, and vanadium will be introduced into the predetermined Session 4: Liquid Synthesis and Sol-gel Derived glass matrix. The sulfate solubility of these glasses will be determined initially by visual methods, then by Inductively Coupled Plasma Atomic Materials II Emission Spectroscopy (ICP-AES) at Alfred University. SRNL will be Room: Salon B conducting chemical durability tests to estimate the performance of the Session Chairs: Brian Riley, Pacific Northwest National Laboratory; glasses in practical application. David Musgraves, Clemson University 4:20 PM 1:20 PM (GOMD-SIII-014-2012) Rhenium solubility in borosilicate nuclear (GOMD-SIII-040-2012) Physio-chemical properties of spin-coated waste glasses As2Se3 chalcogenide glass thin films A. Goel*, B. J. Riley, M. Liezers, C. F. Windisch, J. S. McCloy, M. J. Schweiger, C. Y. Zou*, H. Lin, O. Ogbuu, University of Delaware, USA; S. Novak, Clemson P. Rodriguez, P. Hrma, D. Kim, Pacific Northwest National Laboratory, USA University, USA; J. Wilkinson, Clemson University, USA; J. Musgraves, Clemson The present study is an attempt to gain an insight into the solubility/re- University, USA; K. Richardson, Clemson University, USA; J. Hu, University of tention of 99Tc species in low activity waste glass. Since, 99Tc is ra- Delaware, USA dioactive in nature; therefore, Re has been used as simulant for Tc due Thin film selenide glasses have emerged as an important material for to their similar chemistry, ionic size and other chemical aspects. The photonic applications due to its high refractive index, transparency in concentration of Re in glasses varied between 0 ppm – 10000 ppm (by the near-IR and high non-linear optical properties. However, one of the wt.) and all the glasses have been melted in a vacuum sealed quartz cru- challenges is developing low-cost methods to deposit glassy films while cible in order to avoid any Re loss due to volatilization. An array of char- retaining glass stoichiometry and high optical quality. In this paper, acterization techniques including MAS-NMR, Raman spectroscopy, As2Se3 amorphous thin films were prepared by standard spin-coating XRD, SEM-EDS, ICP-OES, LA-ICP-MS and EPMA has been employed techniques from their organic amine solution with glass loading con- to study the structure, crystalline phase assemblage, Re solubility and centrations as high as 0.6 g/ml. The prepared films were stabilized at el- distribution in glasses. The results obtained from this study are expected evated temperatures. Physio-chemical properties of the spin-coated to lay a strong foundation for the future experiments involving the im- films were studied and compared with thermal evaporated As2Se3 thin mobilization of radioactive 99Tc in nuclear waste glasses. film. Fabrication of low loss waveguides from spin-coated As2Se3 thin films was also demonstrated. 4:40 PM (GOMD-SIII-015-2012) The Corrosion of Inconel 690 and Inconel 1:40 PM 693 in an Iron Phosphate Melt Containing 26 wt% of a Simulated (GOMD-SIII-041-2012) Materials properties and performance of Low Activity Waste solution processed arsenic sulfide glass in optical and photonic J. Hsu*, J. W. Newkirk, Missouri University of Science and Technology, USA; C. applications (Invited) Kim, Mo-Sci Corporation, USA; C. S. Ray, R. K. Brow, M. E. Schlesinger, D. E. C. B. Arnold*, Princeton University, USA Day, Missouri University of Science and Technology, USA Solution derived non-oxide glasses opens the door to many novel Iron phosphate (FeP) glass is a candidate fixation medium for storage of processes and methods for producing optical and photonic devices in , based on the high waste loading, low processing tem- the near and mid infrared regions. In this presentation, we discuss the peratures, and outstanding chemical durability. The U.S. Department of materials properties of solution processed chalcogenide films used in Energy supported a program to assess the viability of using FeP glass for spin-coating and soft-lithographic patterning and their stability in the vitrifying low activity waste in a Joule Heated Melter(JHM). In this solution phase. Solutions and films are characterized for their physical study, the isothermal corrosion behavior of Inconel 690 and 693, poten- structure, chemical stability and optical properties. We find the solution tial electrode materials for the JHM, was investigated. Inconel coupons phase to be stable to atmospheric conditions, including the presence of were immersed in a FeP containing 26 wt% simulated low activity waste water, and demonstrate that it is possible to produce films from aged so- at 1030-1050 °C. After submersion at 1050 °C for seven days, there is al- lutions that show similar properties to those produced from fresh mix- most no dimensional change and the internal penetration is <250 μm tures. In addition, we focus on the properties of these films and com- for both Inconel 690 and 693. The corrosion is slightly higher when a ment on specific anomalous effects that occur in their photoresponsive voltage is applied to the electrode, but the results indicate that Inconel behavior and their non-linear properties. 690 and 693 should have an acceptable corrosion resistance in an Iron Phosphate melt. 2:20 PM (GOMD-SIII-042-2012) Investigation and electrocatalytic 5:00 PM application of Prussian blue-Palladium nanocomposite (GOMD-SIII-016-2012) Cold Crucible Induction Melter Technology P. C. Pandey, A. K. Pandey*, D. S. Chauhan, Institute of Technology, Banaras as a Tool to Increase Waste Loading for High Level Radioactive Hindu University, India Wastes J. Marra*, Savannah River National Laboratory, USA The present work is focused on the fabrication of an efficient hydrogen peroxide sensor prepared from Prussian blue/Palladium (PB/Pd) The Cold Crucible Induction Melter (CCIM) melts glass inductively by nanocomposite. PB was synthesized following facile chemical method creating an eddy current inside the glass pool using a water-cooled, by the addition of an aqueous solution of ferrous sulphate to an high-frequency electrical coil that surrounds the outer walls of the equimolar solution of potassium ferricyanide. Palladium chloride was CCIM. Due to a steep temperature gradient that exists near the walls, a reduced with 3-Glycidoxypropyltrimethoxysilane following high tem- frozen glass layer forms along the inside walls of the CCIM preventing perature treatment. The electrochemical behavior of PB was tremen- corrosion. The CCIM design is relatively insensitive to glass chemistry dously enhanced by the incorporation of palladium metal resulting in allowing for feeds with more diversified chemistry, lessening the burden the formation of PB/Pd nanocomposite. The obtained nanocomposite put on the pretreatment or melter feed preparation processes. The was utilized to modify the carbon paste electrode (CPE), leading to the CCIM can also run at higher temperatures allowing for higher waste development of an electrochemical sensor for hydrogen peroxide. The loading and tolerance to crystalline phases. Several melter campaigns on results of hydrogen peroxide reduction indicate excellent sensitivity and

2012 Glass & Optical Materials Division Annual Meeting 33 Abstracts limit of detection. The results on the effect of pH suggested that lower- structure, with examples from both oxide and non-oxide glasses. Much ing of pH lead to improvement in the kinetics of hydrogen peroxide re- of our effort has been directed at understanding the impact of P on duction. other network-forming cations. Fully networked glasses display inter- esting structural responses to the introduction of P, with substantial 2:40 PM changes in B, Al or Ga coordination, suggesting the association of P and (GOMD-SIII-043-2012) Application of alkoxysilane-derived gold these cations as next-nearest neighbors. The presence of P has been nanoparticles in sensitive determination of glucose shown to stabilize B, Al and Ga in tetrahedral coordination, with signif- P. C. Pandey*, D. S. Chauhan, Institute of Technology, Banaras Hindu icant impact on glass properties, including increased Tg and chemical University, India durability. The present work reports the synthesis of Gold nanoparticles (AuNp) 4:20 PM using alkoxysilane precursors and application of same in composite for- (GOMD-SIV-020-2012) Quantification of structural disorder in zinc mation. For this purpose, Prussian blue (PB) was chosen as a model sys- phosphate glasses: Results from 31P 2D Phase Adjusted Spinning tem. The AuNp were mixed with chemically synthesized PB and were Sideband (PASS) NMR utilized for the modification of carbon paste electrodes (CPE). The re- D. C. Kaseman*, S. Sen, University of California Davis, USA sulting CPE, due to the presence of alkoxysilanes, showed the stability comparable to carbon ceramic electrodes. The CPE were used for the The Q speciation and the degree of structural disorder associated with determination of hydrogen peroxide at potential close to 0.0 V. Further, the geometry of the corresponding PO4 tetrahedra are investigated in in order to investigate the biocompatibility of the CPE, glucose oxidase glasses of composition 60ZnO*40P2O5 with different fictive tempera- (GOD) was incorporated into the CPE matrix. The sensing of glucose tures using 31P 2D PASS NMR spectroscopy. The 2D PASS experiment was performed using cyclic voltammetry and amperometric monitoring correlates a pure isotropic shift dimension and a pure anisotropic di- of hydrogen peroxide released as a byproduct of glucose oxidation. The mension; a distinct advantage over typical Magic Angle Spinning NMR, results show that the modified electrodes proved to be an efficient ma- in which spectra are difficult to interpret due to overlapping spinning trix for biomolecule immobilization leading to generation of electrocat- sidebands. The isotropic dimension contained three distinct chemical alytic sites. shifts corresponding to the Q(2), Q(1) and Q(0) species. The 31P chem- ical shift anisotropy (CSA) parameters and their distributions were also quantified for the constituent Q-species and were found to be sensitive Symposium IV: Festschrift to the Glass to the thermal history of the glass. The CSA distributions and their fic- Research Career of Prof. Delbert E. Day tive temperature dependence are shown to be related to the frozen-in configurational entropy in these glasses. Session 2: Phosphate Glasses: Their Structures, 4:40 PM Properties and Applications II (GOMD-SIV-021-2012) Femtosecond laser writing of waveguides in zinc phosphate glasses L. B. Fletcher, N. Troy, University of California, Davis, USA; S. T. Reis, R. K. Brow, Missouri University of Science and Technology, USA; D. M. Krol*, Room: Salon C University of California, Davis, USA Session Chair: Richard Brow, Missouri S&T We have studied ultrafast (femtosecond) laser fabrication of photonic 3:20 PM structures in a wide range of zinc phosphate glasses. Our research fo- (GOMD-SIV-018-2012) On the reticulation degree of phosphate cused on the relationship between the initial glass composition and the glass networks : a solid-state NMR approach (Invited) laser-induced structural changes in the material. Waveguides were writ- M. Lionel*, L. Delevoye, G. Tricot, F. Mear, J. Amoureux, J. Trebosc, P. ten in Er-Yb doped and undoped zinc phosphate glasses. White light Rajbandhari, T. Lemesle, N. Forler, F. Vasconcelos, University of Lille, France microscopy and waveguide experiments were used together with Raman and fluorescence spectroscopy to characterize the structural changes in It is well known that the development of phosphate glasses with accept- the glass. The results show that the exact glass composition plays a key able chemical durability for applications to the vitrification of nuclear role in determining both waveguide quality and the structural modifica- wastes or antioxidation coatings is based on the enhancement of the tion of the glass. In this talk, we will discuss the response to femtosecond reticulation of the phosphate network with elements like aluminium, laser exposure in the context of glass structure and composition. We will iron, boron or niobium. We use multi-nuclear solid-state NMR as a tool also briefly highlight the performance of the laser-fabricated devices. to probe this reticulation effect from two angles: one is how the reticu- lating elements (27Al, 93Nb, 11B) are connected to phosphate groups, 5:00 PM the second concerns the oxygens that are involved in the connectivities, (GOMD-SIV-022-2012) Irradiation Induced Defects in Cerium using 17O NMR. We will present how this approach can help in under- Aluminophosphate Glasses standing the mechanism of phosphate glass alteration with the aim of J. L. Rygel*, C. G. Pantano, The Pennsylvania State University, USA; J. Du, The developing optimized glass compositions for nuclear waste vitrification. University of North Texas, USA We use a combination of advanced NMR methods and hardware (high- Cerium is known for radiation damage resistance, limiting the forma- field spectrometer, high performance probes), completed by ab-initio tion of deleterious color centers during high-energy irradiation. Phos- calculations. phate glasses provide a unique opportunity for studying this effect due 4:00 PM to their high rare-earth solubility, ~25 mol%. Irradiation-induced de- (GOMD-SIV-019-2012) Impact of P on Trivalent Network-Forming fects were identified by EPR in a series of cerium aluminophosphate Cations glasses. P1 and P2 defects sites were found in the low cerium composi- R. Youngman*, B. Aitken, Corning Incorporated, USA tions, while no irradiation-induced defects were detected in the high cerium glasses. Additionally, no POHC’s, a near ubiquitous defect in ir- Phosphate glasses have captured the attention of glass scientists for radiated phosphate glasses, were detected in any of the irradiated com- many years. In addition to our increased ability to understand struc- positions. The presence, or absence, of irradiation-induced defects has ture/property relations, certain P-containing glasses have been studied been correlated to the structure of these glasses. Finally, first principles for a variety of commercial applications, including sealing materials, Density Functional Theory calculations were performed to determine photonic devices and consumer products. We describe several studies in the hole- and electron-trapping behaviors of intrinsic defect sites, in- which NMR spectroscopy was used to investigate short-range atomic

34 2012 Glass & Optical Materials Division Annual Meeting Abstracts cluding P1, P2 and POHC, with or without the presence of cerium ions (GOMD-SP-P005-2012) A thermodynamic interpretation to explain in the vicinity of the defects. enhanced ionic conductivity due to AgI dissolution in AgPO3-AgI glasses Poster Session and Student Poster Competition C. B. Bragatto*, Universidade Federal de São Carlos, Brazil; J. Souquet, Institut National Polytechnique de Grenoble, France; A. Rodrigues, Universidade Room: Arch View Ballroom Federal de São Carlos, Brazil (GOMD-SP-P001-2012) Modulated DSC analysis of structure and In the xAgI(1-x)AgPO3 system (0≤x≤0.5), room temperature ionic con- relaxation in arsenic selenide and germanium selenide glasses ductivity increases by many orders of magnitude with x, although the O. Gulbiten*, P. Lucas, University of Arizona, USA concentration of silver remains constant.The conductivity of silver ions, Due to their low glass transition temperatures, chalcogenide glasses un- σ, is expressed as σ=n+eμ+, where n+ is the effective concentration of dergo large structural relaxation even at room temperature. The param- charge carriers, e is their positive charge, and μ+ is their electrical mo- eters describing these relaxation processes need to be determined since bility. Previous studies involving Hall effect measurements or the inter- they can have a significant impact on technological applications. In this pretation of discontinuity in the mechanism of ion transport between study, temperature modulated differential scanning the glassy and supercooled liquid phases have shown that μ+ is inde- calorimetry(MDSC) is used to probe slow structural processes. MDSC pendent of the glass composition. Hence, the dependence of ionic con- is an enhanced calorimetric technique that superimposes the sinusoidal ductivity on the AgI content is attributable only to an increase in n+. temperature modulations on the linear temperature ramp. Decomposi- Considering AgI AgPO3 glasses as weak electrolytes, the concentration tion of complex heat capacity into imaginary and real components al- in charge carriers would depend on the partial free energy of AgI. This lows detailed analysis of relaxation processes which can be directly cor- thermodynamic characteristic is determined by potentiometric meas- related to the glass structure. Heat capacity spectroscopy is performed urements and is correlated to the variation in ionic conductivity. on arsenic and germanium selenide glass systems in a wide range of av- (GOMD-SP-P006-2012) Conversion of Fine-Diameter Melt-Derived erage coordination numbers (2.1≤〈r〉≤2.6) to demonstrate the distinct Bioactive Glass Fibers to Hydroxyapatite in a Simulated Body Fluid and complex responses of different structural motives. X. Liu*, Missouri University of Science and Technology, USA; M. N. Rahaman, (GOMD-SP-P002-2012) MgO-Al2O3-SiO2 glass-ceramics for Missouri University of Science and Technology, USA; D. E. Day, Missouri ballistic protection University of Science and Technology, USA L. Gallo*, E. Zanotto, A. Rodrigues, Universidade Federal de São Carlos, Brazil Fibrous scaffolds of bioactive glass with micron to submicron fiber di- Two glasses - H2R5 and L2R4 - of the MgO-Al2O3-SiO2 system with ameters are showing exciting promise for the regeneration of bone and widely different minor components have been formulated and melted. the healing of soft tissue wounds. In this work, the bioactivity of melt- After differential scanning calorimetry analysis, thermal treatments derived bioactive glass fibers was evaluated in vitro from their conver- were performed to crystallize the precursor glasses. Hardness and in- sion to hydroxyapatite (HA) in a simulated body fluid (SBF) at 37C. dentation fracture toughness (IFT) were measured using a Vickers hard- Fibers of three bioactive glasses were studied: silicate 45S5 (Na2O-CaO- ness equipment. After single-stage heat treatments, the hardness of the P2O5-SiO2) borate 13-93B3 (Na2O-K2O-MgO-CaO-P2O5-B2O3) and H2R5 samples varied from 6.0±0.4 to 6.8±0.1GPa, whereas the IFT in- borate 13-93B3 doped with trace amounts of Fe, Sr, Cu, and Zn. The creased about 60% on partial crystallization. In the case of L2R4 sam- structure and composition of the conversion products were analyzed by ples, the hardness varied from 6.6±0.1 to 9.9±0.2GPa, with an increase XRD, SEM, TEM, and FTIR. The ion concentration of the solution was of about 70% in the IFT. After double-stage heat treatments, transparent measured by ICP-AES. Results showed rapid conversion of the bioactive GCs were obtained from the L2R4 glass, with hardness up to glass fibers to HA as well as rapid release of ions from the glass fibers 9.5±0.1GPa and an increase in IFT of about 35%. X-ray diffraction ex- into the SBF. These characteristics may account for the exciting results periments showed Sapphirine (7MgO.9Al2O3.3SiO2) and three other already observed in the use of these fibrous bioactive glass scaffolds in phases in the GCs crystallized above 1270 K. These are promissing, vivo. transparent, low density armor materials. (GOMD-SP-P007-2012) Dissolution Behavior of Sodium-Iron- (GOMD-SP-P003-2012) Structural Effects of Varying Quench Rates Phosphate Glasses in Alkaline Aqueous Solutions in Ba, Ca, La, Y Boroaluminosilicate Glasses: High Resolution 11B & L. Ma*, Missouri University of Science and Technology, USA; R. K. Brow, 27Al MAS NMR Missouri University of Science and Technology, USA; M. E. Schlesinger, E. Morin*, J. Stebbins, J. Wu, Stanford University, USA Missouri University of Science and Technology, USA Although the “intermediate” cations yttrium and lanthanum are incor- Iron phosphate glasses are being considered for use in vitrification of porated in technologically important glasses, there has been little struc- nuclear waste because they can be processed at low temperatures, can tural exploration of multi-component rare earth glasses. The influence have large waste-loadings, and possess excellent chemical durability. of cation on structure- Ba, Ca, La, Y- is being explored. In industrial Several series of Na2O-Fe2O3-P2O5 glasses were prepared with compo- , the degree of “fictive temperature reset,” the atomic re- sitions in the meta- to polyphosphate range (O/P=3.0~3.5). Dissolution laxation of glass during reheating, must be controlled. Using 11B and rates of the glasses in alkaline aqueous solutions were determined from 27Al NMR spectroscopy, we are examining the effect of different weight loss measurements, ion concentration in solution, and pH shift. quench rates on glass structure. The fictive temperatures have been de- The effects of experimental conditions on dissolution rate are investi- termined using differential scanning calorimetry. Slower cooling rates gated, including solution temperature and pH value. The effect of glass produce glass with a slight increase in four-coordinate boron ([4]B). structure on the dissolution behavior will be discussed. Preliminary results suggest slower cooling rates result in more [5,6]Al (GOMD-SP-P008-2012) Glass forming behavior of borate melts relative to [4]Al. For each cation, as the boron to silicon ratio in the glass based on thermal analyses and viscosity measurements is increased, the fraction of [4]B increases. Higher cation field strength K. Goetschius*, L. Ghussn, R. K. Brow, Missouri S&T, USA results in a lower fraction of [4]B. Compositions near the edge of the glass forming region from the system Na2O-CaO-B2O3 , (0-35 mole % Na2O, 0-40 mole % CaO and 50-65 mole% B2O3) were studied in order to relate the glass forming ability to the viscosity of melt at the temperature and to the melt fragility parameter (m). Viscosity measurements were made using rotational and parallel plate viscometers and the data was fit using the Corning model, which was used to determine ‘m’. Liquidus temperatures were deter-

2012 Glass & Optical Materials Division Annual Meeting 35 Abstracts mined using a new DTA technique and were confirmed using the gradi- °C. Analytical SEM was used to monitor the formation of a calcium ent furnace method. Glass stability parameters, such as the Hruby and phosphate layer surrounding the glass particle. Additionally, the layer Weinburg parameters, were also determined using DTA and related to was characterized by x-ray diffraction and micro-Raman spectroscopy. glass forming ability. In general, melts with either a higher viscosity at The role of internal and external phosphate sources in hydroxyapatite the liquidus temperature or those with lower viscosity but a larger formation will be discussed. fragility parameter had a greater ability to form glasses upon quenching. (GOMD-SP-P013-2012) The development of ‘ferrous blue’ silicate (GOMD-SP-P009-2012) Dynamic Light Scattering Studies on glasses Structural Effects on the Dynamics of Potassium-modified Borate E. M. Buchheit*, R. K. Brow, Missouri S&T, USA Glass The purpose of this undergraduate research project was to develop a S. Schnell*, Creighton University, USA glass composition that transmits in the near ultraviolet region (~350 Studies on the effects of modifying network chains of covalent bonds in nm) but absorbs in the near infrared (~1050 nm). Ferrous ions in sili- glassforming oxides have been a topic of much research. Alkali oxides cate glasses provide the desired near-IR absorption, and if the ferric ion are known network modifiers; effectively raising or lowering the average concentration can be minimized, then the desired near-UV trans- bond density and modifying the viscoelastic properties of the corre- parency can be obtained. Experiments were done to determine how sponding liquid. Recently our research group investigated borate glass combinations of Fe2O3, SnO, and graphite affected the UV/VIS/NIR modified with potassium oxide using dynamic light scattering. The re- spectra of a 12.5 Li2O 12.5 Na2O 75 SiO2 mol% base glass. Desirable sult of this study indicates a rising fragility with the inclusion of potas- blue colors were obtained, but the base glass composition had to be sium oxide which contradicts our prediction of a decreasing fragility modified in order to blue-shift the UV-edge into the desired range. The with corresponding increase in covalent bond density. However our effects of glass composition on the fraction of ferrous and ferric ions measurements agree with measurements in a similar study. I intend here were estimated from the optical spectra. to discuss the technique and results of this DLS study, and how they will impact further research. (GOMD-SP-P014-2012) Aqueous Corrosion of Polyphosphate Glasses (GOMD-SP-P010-2012) Synthesis and characterization of SnF2- C. Smith*, Missouri University of Science and Technology, USA; R. K. Brow, SnO-P2O5 glasses doped with rare earth metals and organic dye Missouri University of Science and Technology, USA T. A. Harper*, A. Kovalskyy, C. Brennan, Austin Peay State University, USA Zinc polyphosphate glasses are candidates for a variety of optical appli- Low melting point glasses have gotten recent attention as a successful cations but phosphate glasses in general are known to have poor chemi- host matrix to rare earth metals and organic elements to be used in en- cal durability. In this study, Zn-Mg- and Zn-Al-polyphosphate glasses ergy conversions. It is known that these glasses usually have low envi- with a range of phosphate anions, determined from their O/P ratios, ronmental durability. Tin phosphate glasses have been shown through have been prepared and their dissolution behavior in aqueous solutions recent studies that they have both the property of being a host matrix determined. Sample weight losses are related to ion-release rates as de- while still having high durability. A set of SnF2-SnO-P2O5 glasses of termined from ICP analyses of solutions as a function of time and tem- different composition have been synthesized. The structural data for the perature. Changes in solution pH are related to changes in solution obtained glass were evaluated using a combination of RAMAN laser chemistry and the phosphate anion distributions in solution were deter- spectroscopy and high-resolution X-ray photoelectronic spectroscopy mined using high pressure liquid chromatography. In general, the (XPS) methods. The received optical quality glass samples have been glasses dissolve congruently and those with shorter average phosphate separately doped with a rare earth metal (Er) and organic dye chain lengths (greater O/P ratios), and with greater field strength (coumarin). RAMAN spectroscopy, XPS, and fluorescence data have cations (Al3+ vs. Zn2+), have lower dissolution rates. been analyzed for the doped samples. (GOMD-SP-P015-2012) Dissolution behavior of alkali-alkaline earth (GOMD-SP-P011-2012) Effect of phosphate speciation on corrosion borate glasses behavior of P2O5-doped sodium borosilicate glasses M. Gilbert*, K. Goetschius, R. Brow, Missouri University of Science and X. Cheng*, R. Brow, G. Chen, Missouri University of Science and Technology, Technology, USA USA The dissolution behavior of alkali-alkaline earth borates (10 R2O-10 Three series of P O -doped, sodium borosilicate glasses were studied: R’O-80 B O , where R= Na, K, or Li and R’=Ca, Mg, or Sr) were studied 2 5 2 3 μ xP2O5•(1-x)(30Na2O•30B2O3•40SiO2), xP2O5•(1-x) in this undergraduate research project. The glass particles, 75-150 m in (10Na2O•30B2O3•60SiO2), and xP2O5•(1-x)(40Na2O•20B2O3•40SiO2) diameter, were reacted in DI water, inside mesh bags, using a shaking (mol%). Solid state NMR reveal that phosphate is incorporated into the water bath at a temperature of 37°C. The solutions were analyzed using glass structure in three different ways, as isolated orthophosphate units, induction coupled plasma optical emission spectroscopy (ICP-OES) to pyrophosphate units and in borophosphate sites. The corrosion determine the ion release rates over a period of two days. All glass com- processes of glasses from each of these three series were analyzed in a positions were found to dissolve congruently. In the series with different pH=7 buffer solution and in a calcium-containing, pH=12 solution. In alkali, the K2O containing glasses were found to dissolve fastest, while the latter solution, the release of phosphate anions leads to the forma- Li2O glasses had the lowest dissolution rate. In the series with different tion of a calcium phosphate layer on the surface that inhibits further re- alkaline earths, MgO glasses had the highest dissolution rates, and the action. The dissolution kinetics were studied using ion release rates de- CaO glasses had the lowest. termined by ICP-OES and HPLC, and the corrosion layers were analyzed by SEM and micro-Raman spectrometry. The effects of glass (GOMD-SP-P016-2012) Experimental and Theoretical Studies of structure, particularly the nature of the incorporated phosphate units, Structural Properties of Ag doped Ge-Sb-Te Thin Films on the corrosion kinetics will be discussed. B. Prasai*, M. Kordesch, D. Drabold, G. Chen, Ohio University, USA (GOMD-SP-P012-2012) Calcium phosphate layer formation on bio- Transition-metal-doped chalcogenides are of great interest for their po- active borate glass microspheres in aqueous phosphate solutions tential application in conductive bridge random access memory (CBRAM). In this paper, we report X-ray absorption fine structure J. George*, R. Brow, Missouri University of Science and Technology, USA (XAFS) study of Ag doped Ge-Sb-Te (GST) compounds. The purpose is Borate bioactive glasses have been studied for use in scaffolds for soft to understand the role of Ag on the modification of the amorphous GST tissue and bone repair. The present work provides an analysis of reac- network structure. Ag-doped Ge1Sb2Te4 thin films were fabricated by tion products that are formed when bio-active borate glasses are dis- sputtering with Ag content up to 50 at.%. X-ray diffraction shows that solved in aqueous solutions of varying phosphate-ion concentration. all the as-deposited films are amorphous. The XAFS analysis reveals that Glass microspheres were reacted at temperatures between 21 °C and 60 the Ag exists in the form of ions and prefers to bond with Te rather than

36 2012 Glass & Optical Materials Division Annual Meeting Abstracts

Ge and Sb. The local structure of the glasses as a function of Ag dopant senic sulfide chalcogenide glass samples. We examined both virgin and concentration will be discussed. Molecular dynamic simulations were annealed thin film evaporated samples and the changes in conductivity also conducted on Ag-doped Ge1Sb2Te4 compounds, and the result vs. temperature profile with progressive heating. The fresh, un-annealed confirms the chemical bonding preference of Ag. films reveal considerable photoconductivity at lower temperature (20- 29 70° C) with a peak in the response near 50° C. With progressively higher (GOMD-SP-P017-2012) Si natural abundance MAFCPMG NMR temperature heating cycles the peak diminishes, until it essentially dis- analysis of anionic species in BaSi O glass 2 5 appears after heating to 170° C. Fully annealed samples show negligible K. J. Sanders*, E. G. Keeler, The Ohio State University, USA; J. H. Baltisberger, photocurrent at room temperature, with relative photocurrent gradu- Berea College, USA; P. J. Grandinetti, The Ohio State University, USA ally increasing with temperature until a maximum near 100° C. The sig- The two-dimensional Magic Angle Flipping CPMG Nuclear Magnetic nificant changes in photoconductivity thermograms during annealing Resonance (2D MAFCPMG NMR) experiment on 29Si nuclei at natural accessible with this simple apparatus lend this experiment ideal for an abundance has been used to determine the distribution of Q(n) sites in undergraduate laboratory in both photoconductivity as well as relax- ation in glass. an alkaline-earth silicate glass sample of composition BaSi2O5. Relative (2) (3) (4) abundances of 15-25% for Q 55-70% for Q , and 15-25% for Q (GOMD-SP-P037-2012) Multi Scale Studies of LiNbO3 Silicate Glass- were obtained from initial spectral fits of the 2D MAFCPMG spectrum Ceramic of the BaSi O glass; however these simulations are incomplete. Nuclear 2 5 H. Vigouroux*, E. Fargin, ICMCB, France; B. Le Garrec, CEA, France; M. shielding tensor anisotropy, ζ, and asymmetry, η, values have only been Dussauze, F. Adamietz, V. Rodriguez, ISM, France determined for Q(3) which are ζ = -58 ± 2 ppm, η = 0.2 ± 0.05. The re- sults are compared to previous MAF results for four 29Si-enriched sili- A two-steps heat-treatment consisting of both nucleation and growth cate glasses of compositions K2Si2O5, Na4Si3O8, CaSiO3 MgSiO3, and to on Li2O/Nb2O5/SiO2 glass provides transparent and translucid glass- 29 MAFCPMG results for Si-enriched Mg2SiO4 glass. A comparison of k3 ceramics with nonlinear optical properties. Scanning Electronic Mi- values indicate an exponential increase in k3 with increasing modifying croscopy and Second Harmonic Generation (SHG) measurements al- cation potential. lows the crystallization mechanism identification. In particular, bulk samples have been characterized with spherulites precipitation and a re- (GOMD-SP-P018-2012) Enhancing Sensitivity of Slow MAS producible SHG signal with a maximum intensity at normal incidence Correlation Experiments on K Si O glass using PIETA 2 4 9 [1]. Multi scale characterizations have been performed on LiNbO3- B. J. Walder*, E. G. Keeler, The Ohio State University, USA; J. H. Baltisberger, SiO2 glass-ceramic to investigate origin of nonlinear optical properties. Berea College, USA; P. J. Grandinetti, The Ohio State University, USA Both SHG and Raman spectroscopy were studied at the microscopic We present an approach to enhance the sensitivity of two experiments level. They point out a radial distribution of c-axis oriented LiNbO3 designed to produce a correlation between the isotropic and anisotropic crystallites inside spherulites. The macroscopic linear and nonlinear parts of the nuclear shielding tensor: 2D PASS (Phase Adjusted Spin- second order optical properties of glass-ceramics will finally be investi- ning Sidebands) and the closely related MAT (Magic Angle Turning). gated. A mechanism at the origin of bulk SHG within glass-ceramic will This is accomplished by utilizing the very recently developed Phase In- be discussed. [1] H. Vigouroux et al. J. Am. Ceram. Soc.,94, 2080 (2011) cremented Echo Train Acquisition (PIETA) technique. With PIETA, the (GOMD-SI-P022-2012) Shattering (Exploding) Glass Cookware introduction of linear phase increment and echo count dimensions al- Δ ± R. C. Bradt*, R. Martens, The University of Alabama, USA lows for the direct selection of the desired pI,n = 2 pathways for an ar- bitrary number of echoes. This allows one to discard all artifact path- Recent escalation of the household kitchen accidents with glass cook- ways that CPMG cannot eliminate. With this and the addition of one ware has been documented in two articles by Consumer Reports, several more mixing pulse for the 2D PASS experiment that allows all echoes to TV documentaries, complaints to the CPSC and on the internet under satisfy the PASS equations, we exhibit an accurate slow spinning 2D nu- “exploding pyrex”. This paper addresses the technical engineering as- clear shielding correlation spectra of Cu doped K2Si4O9 glass, where the pects of those incidents by a couple of approaches. The first is to sum- S/N is enhanced by a factor of between 2 to 4 when compared to stan- marize and categorize the histories of the reported failures which sug- dard MAT or PASS. gests that thermal shock may be responsible. The next is to examine the thermal shock resistance of the glasses, first by comparing soda lime and (GOMD-SP-P020-2012) Multi-technique Investigation of Ion- borosilicate glasses as described in the Corning glass properties catalog Exchanged Silicate and Aluminosilicate Glasses and literature. Finally the estimated ΔT for thermal shock fracture of the P. K. Kreski*, A. Cormack, A. K. Varshneya, Alfred University, USA two glasses from thermoelastic stress analysis. In total these items Despite their use in commercial markets, little is understood about the strongly suggest that thermal shock failure during temperature changes accommodation of stuffing alkali ions in ion-exchange strengthened sil- in the kitchen is the cause of the incidents. icate glass networks. Sodium aluminosilicate and soda lime silicate (GOMD-SI-P023-2012) Synthesis of CaO-MgO-SiO2 glass-ceramic compositions were studied using profilometry to quantify dimensional powders by using a waste solution of Na2SiO3 as silica source swelling by selective surface exchange. This technique was combined C. Yamagata, O. Higa, A. D. Rodas, Nuclear and Energy Research Institute, with birefringence, microhardness, and elastic finite element simula- Brazil; S. T. Reis*, Saint-Gobain Innovative Materials, USA tions to examine the relationship between dimensional changes and residual stress state as a function of varied ion-exchange time and tem- The glass-ceramics of the ternary CaO-MgO-SiO2 system have been perature. To aid structural understanding, molecular dynamics simula- studied for biomedical applications because of their good mechanical tions of sodium silicate glasses where sodium ions were substituted di- and chemical properties. CaO-MgO-SiO2 glass-ceramic powder was rectly by stuffing potassium ions were carried out under isotropic and synthesized by a novel method: Ca and Mg were precipitated on SiO2 anisotropic boundary conditions. MD simulation results and laboratory gel obtained from Na2SiO3 solution, derived from the alkaline fusion of profilometry were compared via estimation of linear network dilatation zircon. Non-aggregated SiO2 particles were initially prepared by surfac- coefficient obtained by each method. tant template sol-gel technique, via acid-catalyzed hydrolysis of Na2SiO3. The CaO-MgO-SiO2 glass-ceramic powders were character- (GOMD-SP-P021-2012) Effect of annealing on the temperature ized by SEM, BET, FTIR and XRD. XRD analysis of the sample sintered dependence of photoconductivity in As2S3 films at 1300 οC confirmed that it is mostly composed of wollstonite W. R. Heffner, Lehigh University, USA; M. Korngruen*, Rowan University, USA; (CaSiO3) and arkemanite (Ca2MgSi2O7) crystalline phases and dical- A. Kovalskyy, Austin Peay State University, USA; N. Ward, Oakwood University, cium silicate (Ca2SiO4) in minor intensity. The simulate blood fluid USA (SBF) was used to test the in vitro bioactivity and no toxic effect was We adapt a previously described student built electrometer to measure found in the cyto-toxicity test with CHO (Chinese hamster ovary) cells. electrical conductivity and associated photoconductivity in thin film ar-

2012 Glass & Optical Materials Division Annual Meeting 37 Abstracts

(GOMD-SI-P024-2012) Elasticity of sodium disilicate glass at high (GOMD-SI-P027-2012) Thermal Analysis of Waste Glass Feeds: pressures and high temperatures Modeling Kinetic Parameters T. Yu*, The University of Chicago, USA; Y. Kono, Carnegie Institution of D. Pierce*, R. Pokorny, J. Chun, P. Hrma, Pacific National Northwest Washington, USA; T. Sakamaki, Z. Jing, Y. Wang, The University of Chicago, Laboratories, USA USA; G. Shen, Carnegie Institution of Washington, USA Feeds formulated to vitrify high-level wastes (HLW) contain a large Studying the structures and physical properties of silicate melts under number of constituents that undergo multiple gas evolving reactions extreme conditions is essential for understanding the dynamics of the upon heating. Mathematical representation of the kinetics of these reac- earth’s interior. Sodium disilicate (Na2Si2O5) glass is a good model ma- tions is essential for modeling large-scale waste-glass melters. We used a terial for studying basalt magma since they have similar ratios of non- high-alumina HLW anticipated for processing in the Waste Treatment bridging oxygen to tetrahedrally coordinated cations. Synthesized and Immobilization Plant, currently under construction at Hanford in sodium disilicate glass was loaded into a Paris-Edinburgh cell and Washington State. We performed thermal analysis of feed samples with pressed up to 4GPa and heated up to 1000oC at the Advanced Photon TGA and DSC at constant heating rates ranging from 1 to 50 K/min. To Source. Ultrasonic elastic wave velocities of the sample were collected obtain the kinetic parameters for individual reactions such as reaction using the pulse reflection method. White beam x-ray radiographs were orders and activation energies, we employed a reaction kinetic model used to determine the elastic wave travel distance. Experimental results for independent multiple reactions, and used the Kissinger’s method show that before the glass transition temperature, the transverse wave with least square optimization. Our kinetic model showed excellent velocity remains nearly constant with increasing temperature, while the agreement with measured data. longitudinal wave velocity decreases monotonically. The geophysical implications will be discussed. (GOMD-SI-P028-2012) Formation and corrosion behavior of mechanically alloyed Cu-Zr-Ti bulk metallic glasses (GOMD-SI-P025-2012) Fractal Structure of Silicon Oxycarbide P. Lee*, National Taiwan Ocean University, Taiwan Polymer Derived Ceramics The Cu60Zr30Ti10 bulk metallic glasses were synthesized by vacuum S. Widgeon*, S. Sen, University of California, Davis, USA; G. Mera, Technische hot pressing the mechanically alloyed Cu60Zr30Ti10 metallic glass Universität Darmstadt, Germany; E. Stoyanov, University of California, Davis, powders. It was found that the pressure could enhance the thermal sta- USA; R. Riedel, Technische Universität Darmstadt, Germany; A. Navrotsky, bility and prolong the existence of the amorphous phase inside University of California, Davis, USA Cu60Zr30Ti10 powders.The corrosion behavior of Cu-based BMG in SiOC-PDCs exhibit unusual properties, such as oxidation and corrosion four different corrosive media was studied by the potentiodynamic resistance, low crystallization rates at elevated temperatures, and en- method. The Cu60Zr30Ti10 BMG shows lower corrosion rate and cur- hanced thermomechanical and optical properties, making them good rent density in 1N H2SO4, NaOH and HNO3 solutions. The XPS results candidates for a wide array of high temperature applications. Here we revealed that the formation of Zr- and Ti-rich passive oxide layers pro- report the results of the structural characterization of SiOC-PDCs with vide a high corrosion resistance in 1N H2SO4 and HNO3 solutions, differing carbon contents using 13C and 29Si NMR spectroscopy. The while the breakdown of the protective film by Cl- attack was responsible data suggest that the structure of the SiOC-PDCs consists of a continu- for pitting corrosion in the 3 mass% NaCl solution. The formation of ous mass-fractal backbone of corner-shared SiCxO4-x tetrahedral units the oxide films and the nucleation and growth of pitting will be dis- with “voids” occupied by sp2-hybridized graphitic carbon. The carbon cussed in light of microstructural investigations. rich SiC units are located on the exterior of the carbon domains and 4 (GOMD-SI-P004-2012) Corrosion behavior of P0798 type simulated wrap around the carbon clusters. The oxygen-rich SiCxO4-x units are lo- cated at the interior of this backbone with tenuously connected net- HLW glass in the presence of magnesium ion work. Such fractal percolation networks in these materials can give rise T. Maeda*, H. Ohmori, S. Mitsui, T. Banba, Japan Atomic Energy Agency, Japan to unusual mechanical and transport properties such as viscosity and Static leach tests were conducted for P0798 type simulated HLW glass in electrical conductivity. magnesium chloride solution to investigate the effects of Mg ion on the (GOMD-SI-P026-2012) Direct Atomic-Resolution Imaging of a Two- glass corrosion. The glass corroded at higher rate under the condition Dimensional Silica Glass that Mg ion exists in the leachate, while the rate dropped after the deple- tion of Mg ion in the leachate. Surface analyses showed that altered layer P. Huang*, Cornell University, USA; S. Kurasch, University of Ulm, Germany; A. including Mg and Si was observed at the surface of the leached glass. Srivastava, V. Skakalova, Max Planck Institute for Solid State Research, The present results implied that corrosion of the glass with the higher Germany; J. Kotakoski, A. Krasheninnikov, University of Helsinki, Finland; R. rate occurred as dissolution of Si from the glass network accompanied Hovden, Q. Mao, Cornell University, USA; J. Meyer, University of Vienna, with formation of magnesium silicates. Corrosion rate of the HLW glass Austria; U. Kaiser, University of Ulm, Germany; D. Muller, Cornell University, would be low for long-term if cations forming silicate compounds are USA scarce in groundwater. Typical glasses and their atomic structures are notoriously difficult to study using high-resolution, real-space techniques. Direct atomic reso- (GOMD-SII-P029-2012) UV-Covert Glass Taggants lution structural and chemical characterizations, however, should be M. Velez*, Y. He, Mo-Sci Corp., USA; M. Rupasinghe, V. A. Samaranayake, R. K. possible for materials that are glassy only in two dimensions. We report Brow, Missouri University of Science & Technology, USA the accidental discovery and characterization of such a two-dimensional There is a need for covertly detect and track objects from distances of (2D) silica glass on a graphene support membrane using atomic resolu- 100 m to 5 km. Retroreflector glass microspheres can be used as covert tion transmission electron microscopy and spectroscopy. Using these taggants on equipment or vehicles, for instance, to be detected from techniques, we identify the glass as SiO2, formed from a bilayer of long distances or from aerial platforms. Current commercial materials (SiO4)2- tetrahedra. Our images strikingly resemble Zachariasen’s orig- are designed to retroreflect light in the UV, IR or UV and IR regions inal 1932 cartoon models of 2D continuous random network glasses. while blocking visible light. Covert UV and/or IR retroreflectors not From the atomic coordinates contained in these images, we directly ob- only are valuable as long distance, easily hidden taggants, but spectral tain ring statistics and pair distribution functions that span the regimes analysis of the returned radiation can yield information about the envi- of short-, medium-, and long-range order. These results demonstrate a ronment around the object or area that has been tagged. Lead-free bo- new class of 2D glasses that open the door to atom-by-atom studies of rate and phosphate glass retroreflector microspheres (50 to 200 μm di- glass structures. ameter) tuned for UV wavelength were fabricated. A B2O3-La2O3 glass was further modified to block VIS and IR through the addition of NiO and CoO.

38 2012 Glass & Optical Materials Division Annual Meeting Abstracts

(GOMD-SII-P030-2012) Thermal stability and optical properties of sub-micron-core diameters to produce more than a full octave of super- rare earth doped oxyfluoride tellurite glasses continuum generation over the wavelength range 0.9 - 2.2 microns R. Morea, CSIC, Spain; A. Miguel, Universidad del Pais Vasco, Spain; J. using a picosecond pulsed laser pump. Gonzalo*, J. Fernandez-Navarro, CSIC, Spain; J. Fernandez, R. Balda, Universidad del Pais Vasco, Spain (GOMD-SII-P034-2012) In Situ Optical Spectroscopic Study of Annealing of Tin-doped Ruby Glass In this work we study the crystallization process and optical properties C. McDonough, University of Dallas, USA; C. Saiyasombat*, H. Jain, Lehigh of erbium doped TeO2-ZnO-ZnF2 glasses. The combination of the University, USA chemical and thermal stability of oxide glasses with the good optical properties of fluoride glasses make them attractive materials for active We have investigated the effects of tin on the formation of gold photonic applications. Differential thermal analysis, Raman spec- nanoparticles in sodium trisilicate glass during the annealing process. Samples of sodium trisilicate (NaO-3SiO ) glass were doped with a con- troscopy, Rutherford backscattering spectroscopy and X-ray diffraction 2 stant concentration of gold (0.1 mole% Au) but varying concentrations have been considered to characterize the glass structure, while the opti- 4+ cal properties were investigated using optical transmission, spectro- of tin (0 to 0.1 mole% Sn ). The quenched-glass samples were scopic ellipsometry and emission spectroscopy in the visible and in- mounted on a heating platform so that optical absorption spectra could frared region. Upon excitation at 800 nm, emission at 1.5 μm as well as be collected during the annealing process. It was found that the addition green and red upconversion is observed. The possible mechanisms re- of tin to gold-based ruby glass reduced the required amount of time to sponsible for this behaviour are discussed and related to the effect of form gold nanoparticles in sodium trisilicate glass. The presence of tin fluorine concentration on the structure and thermal stability of the also significantly increased the rate of formation of gold nanoparticles. glasses. A blue shift in absorption was observed for tin-doped gold-ruby glass. This indicated smaller gold nanoparticle size in a tin-doped gold-ruby (GOMD-SII-P031-2012) Laser fabrication of SbSI ferroelectric single glass than in an undoped system. This work is supported by NSF’s Inter- crystals on the surface of Sb-S-I and Ge-Sb-S-I glasses national Materials Institute for New Functionality in Glass (DMR- D. Savytskyy*, P. Gupta, B. Knorr, V. Dierolf, H. Jain, Lehigh University, USA 0844014). Crystallization of glasses by laser irradiation is a novel method recently (GOMD-SII-P035-2012) Europium doped oxyfluoride transparent recognized for constructing active elements. Antimony sulphoiodide glass-ceramics and their luminescence property (SbSI) is chalcogenide compound, which exhibits high values of dielec- Z. Pan*, R. Akrobetu, R. Mu, S. Morgan, Fisk University, USA tric constant, spontaneous polarization, and pyroelectric and pyrooptic coefficients. Glasses of SbSI and x(GeS2)(1-x)(SbSI) (x<0.3) systems are We investigate the reduction of Eu3+ to Eu2+ and their luminescence in obtained using fast cooling regimes of solidification. Laser-fabrication oxyfluoride transparent glass-ceramics. Europium doped oxyfluoride of crystal architecture is demonstrated using a CW 488 nm Ar laser glasses were fabricated in a SiO2-Al2O3-Li2O-CaF2/SrF2/BaF2 matrix source. This method requires fine tuning of various irradiation parame- using a melt-quench technique. The glass-ceramic was formed by a ters. In addition to optimizing laser parameters, only glasses of certain proper heat-treatment of the glass samples. The doping concentration chemical compositions form the desired SbSI crystalline phase. The ef- of EuF3 was 2 mol %. The composition of CaF2/SrF2/BaF2 was used for fect of composition variations on crystallization properties of the chal- reducing Eu3+ to Eu2+ in the glass-ceramic matrix. We found that the cohalide glasses is investigated by X-ray powder diffraction, differential Eu3+ luminescence decreases while the Eu2+ luminescence increases thermal analysis, scanning microRaman and electron microscopies. significantly from glass-ceramic samples compared to that from glass samples. Very strong luminescence of Eu2+ ions centered on 415 nm (GOMD-SII-P032-2012) Raman Studies of Laser-Induced was observed from glass-ceramic samples. Our results indicate that Crystallization in Oxide and Chalcogenide Glasses most of the Eu3+ ions were reduced to Eu2+ ions during the heat-treat- B. Knorr*, P. Gupta, A. Stone, H. Jain, V. Dierolf, Lehigh University, USA ment. This research is supported by US National Science Foundation NSF-CREST- CA: HRD-0420516, NSF-STC CLiPS - grant no. 0423914, We report crystallization and other structural changes in glass due to and NSF CBET-0829977. laser-induced localized heating. This heating is a result of non-radiative decay after a photon absorption process. To better understand and con- (GOMD-SII-P036-2012) Optical Properties Of lithium-aluminum trol the crystallization process, we have developed a combined CW silicate galss –ceramics containing Nano LaF3 using Tb/Gd laser-writing setup / confocal Raman microscope which allows in-situ A. Faeghi nia*, M. Vafaei fard, ceramic division, Islamic Republic of Iran monitoring of the Raman emission during crystallization. Data from this setup will yield insight into the phase, composition, and structure of In The present work, preparation and optical properties of Li-AL-Si-La the modified glass regions, while also aiding in the determination of op- glass containing LaF3 has been studied. It was shown that using timal experimental parameters such as writing speed, irradiation time, (2%mole) Tb and excitation of this system by 325 n.m (wave length) the heating rates, and defect concentration for growing useful, single-crystal blue and green emission occurred, whereas by accumulation 1% mole structures. A comparison between laser-induced changes in oxide and Gd beside Tb, the green range emission (493 to 486 nm) has been pro- chalcogenide glass systems will be presented. moted. Also it was shown that the emission intensity of glass-ceramic has been increased up to 25%, associated to the Tb diffusion in to the (GOMD-SII-P033-2012) Optical Dispersion Control and Full-Octave crystals structure Supercontinuum Generation in Robust Chalcogenide Glass Fibers and Tapers (GOMD-SII-P038-2012) Tm/Dy ions co-doped zinc-aluminum S. Shabahang, G. Tao*, A. F. Abouraddy, University of Central Florida, USA phosphate glasses for white LED L. ChunTeng*, L. JianShian, C. YeeShin, Y. Hsiwen, Z. Teng, National United Multi-material robust chalcogenide glass fibers and tapers offer novel University, Taiwan prospects for dispersion control and mid-infrared nonlinear optics. Compositional control over the glasses used in the core and cladding to- Tm3+ and Dy3+ ions co-doped zinc-aluminum phosphate glasses were gether with dimensional control over the fiber or taper cross sectional prepared by high temperature melt-quenching technique. Measured the features allow us to compensate for the high optical dispersion typical of absorption spectra, Judd-Ofelt intensity parameters have been evalu- chalcogenide glasses with engineered waveguide dispersion having the ated for Tm3+ and Dy3+ ions co-doped glasses. The luminescence opposite sign. We report the dispersion measurements on chalcogenide properties were investigated by excitation and emission spectra. White bulk samples, fibers, and fiber tapers, demonstrate experimentally nor- light emission could be induced by combined blue and yellow bands mal and anomalous waveguide dispersion in the tapers and support the under UV excitation, and the variety of excitation wavelength could results with finite-element simulations. We then leverage these fiber ta- change the luminescence color. The glasses were tempered to crystallize pers having high step-index-contrast between the core and cladding and and enhance the luminescence intensity. CIE chromaticity diagram of the glasses was also studied in this paper.

2012 Glass & Optical Materials Division Annual Meeting 39 Abstracts

(GOMD-SII-P039-2012) Spectral investigation on Eu3+- doped (GOMD-SIII-P042-2012) Sol-gel derived Ag-SiO2 Thin Films: Effect oxyfluoride glass and nanocrystalline glass-ceramics of Al Addition on Structural, Chemical, and Bactericidal Properties R. Bagga*, KMV, India; M. M. Falconieri, ENEA, Italy; V. Achanta, TIFR, India; B. Akkopru Akgun, Middle Eastern Technical University, Turkey; N. P. Mellott*, A. Goyal, Pacific Northwest National Laboratory, USA; J. Ferreira, Department Alfred University, USA; C. Durucan, Middle Eastern Technical University, of Ceramics and Glass Engineering, Portugal; N. Singh, Punjab Technical Turkey University, India; G. Singh, Akal College of Pharmacy, India; D. Singh, Guru Silver containing silica (Ag-SiO2) thin films with and without alu- Nanak DevUniversity, India; V. Contini, ENEA, Italy; G. Sharma, KMV, India minum (Al) were prepared on soda-lime-silica glass by spin coating of We report on the nanocrystallization behavior of melt quenched glass- aqueous sols followed by calcination in air at 100, 300 and 500 C. Thin with nominal composition 34 SiO2: 14 Al2O3: 27 CdF2: 23 PbF2: 2 YF3: films were characterized using x-ray diffraction (XRD), ultraviolet-visi- 0.68 EuF3. Differential thermal analysis (DTA) has been employed to ble spectroscopy (UV-VIS), and x-ray photoelectron spectroscopy shed light on the crystallization parameters of the investigated glass sys- (XPS). The effect of sol composition and processing methods on mi- tem. Based on these measurements the studied system has been sub- crostructure, chemistry, and durability of the thin films were deter- jected to heat treatment at 450 degree centigrade for 24 and 36 hours. mined. The bactericidal activity of the films was also analyzed against The crystalline phase evolution in heat treated glass has been followed Staphylococcus aureus via disk diffusion assay studies before and after using X-ray diffraction (XRD) and scanning electron microscopy chemical durability tests. It was determined that the addition of Al to (SEM) while the glass/glass-ceramic structure has been studied using the silica-based thin film improved their optical properties, bactericidal Raman spectroscopy. The resulting glass ceramic system reports the activity and chemical durability. presence of PbxCd1-xF2nanocrystalline phase,having12-17nm size crystals. The photoluminescence spectra of glass ceramics demonstrate (GOMD-SIV-P043-2012) Effect of Tin and Gold Dopings on Sodium a much stronger emission as well as a significant decrease inthe electric Ion Movement in Silicate Glass to magnetic dipole intensity( 0.4:1 for 24 and 36 hours), in comparison P. Wanninkhof, University of Florida, USA; C. Saiyasombat*, H. Jain, Lehigh to the glass system (1.67:1). University, USA (GOMD-SIII-P040-2012) New Glasses: Higher Performance at Lower The addition of tin induces a deeper red color in gold ruby glass. To ex- Cost plore electrical effects of the addition of tin, sodium trisilicatewas doped with 0.1 mol% gold and varying amounts of tin (0.005≤0.1 mol%)and O. A. Prokhorenko*, Laboratory of Glass Properties, USA; D. Laurent, Y. Houet, electrical conductivity was determined. AC conductivity was measured 3B Fiberglass Co, Belgium as a function of frequency and temperature in order to ascertain the Ar- The glass industry has well-established range of glass formulas. Com- rhenius behavior. Separately adding 0.1 mol% gold and 0.1 mol% tin mercial glasses are manufactured with minimal modifications for increased the electrical conductivity compared to pure sodium trisili- decades for known parameters of melting and processing, sources of cate by 1.9 and 2.6 times, respectively. Combining the dopants resulted raw materials, and properties of the products. We consider three parts of in an increase in conductivity compared to pure sodium trisilicate, vary- successful search for new glass formulas with the best cost/performance ing from 4.1 times for 0.02 mol% tin-0.1 mol% gold to 2.1 times for 0.1 combinations. Algorithms for finding global minimums or maximums mol% tin-0.1 mol%. No clear trend was observed in the activation en- for optimization of cost factors along with key properties. Simple, sensi- ergy of dc conductivity when the amount of tin was varied with the gold tive, and accurate methods for modeling of properties by their chemical held constant. This work is supported by NSF’sInternational Materials formulas. Experimental methods allowing fast and accurate screening of Institute for New Functionalityin Glass (DMR-0844014). compositional ranges, containing the best candidates. The paper con- siders all three aspects: LGP OptiMax 1.0 software program for “global” (GOMD-SIV-P044-2012) Color and oxygen diffusion in niobium optimization of glass compositions on cost/performance base. The phosphate glass method of compound coefficients used for for calculations of glass L. Ghussn*, R. K. Brow, Missouri University of Science & Technology, USA properties by composition. The technique of searching for glass formu- The color of niobium phosphate glasses range from clear to deep blue las, combining different methods of glass synthesis and testing. depending on their thermal history. The reduction of Nb5+ ions to Nb4+ (GOMD-SIII-P041-2012) NMR methods for studying the cation ions is believed to be the source of color [1]. We have studied the devel- opment of color in a base glass (mole%) 23K O•40Nb O •37P O . A dynamics in solid electrolytes 2 2 5 2 5 glass quenched from the melting temperature (1370°C) and annealed in M. Storek*, M. Adjei-Acheamfour, R. Böhmer, TU Dortmund, Germany air at 730°C for 30 minutes is clear, but changes to dark blue when

Nuclear magnetic resonance spectroscopy provides an invaluable tool to heated for 3 hours at 730°C in an atmosphere of flowing 99% N2 - 1% study the ion transport in solids. Because the ions are sensitive to the H2. The kinetics of thermal bleaching the reduced glass to its clear state local chemical and electrical environment the spatial dependence of the have been studied by analyzing the UV/VIS spectra collected from sam- NMR precession frequencies renders the NMR observables time de- ples heated in oxygen between 650 and 730°C and for times up to 24 pendent in the case of translational ionic motion. The combination of hours. Diffusion coefficients for oxygen were calculated from these re- various methods allows one to cover an enormously broad dynamic sults and will be compared to those reported in the literature. [1] Dolci, range. Here we focus on analyses of two-phase spectra, in order to de- F., Di Chio, M., Baricco, M. J Mater Sci (2007) 42, 7180-185. termine broad distributions of motional correlation times, and on two- time hopping correlation functions. To separate the various contribu- (GOMD-SIV-P045-2012) Approach to Predict the Long-term tions affecting the NMR time signal in stimulated-echo experiments we Weathering of Iron Phosphate Glass for the Immobilization of employ spin dynamics calculations. In particular, we model the Hanford Low-Activity Waste quadrupolar and dipolar interactions in a local field approach for spin I E. Pierce*, Oak Ridge National Laboratory, USA = 3/2 nuclei based on work for I = 1 [1]. We compare our findings to ex- Phosphate-based glasses potentially offer significant increases in load- 7 perimental results on Li ion conductors. [1] T. Hasiuk, K.R. Jeffrey, ing of wastes that are high in some components and are difficult to dis- Solid State Nucl. Magn. Reson. 34, 228 (2008) solve in silicate melts (e.g., S, Cr, P, F, and Cl). However, limited infor- mation on the processes that control the long-term weathering of phosphate glass exists. Here the results of a thorough literature review on the structure of phosphate glasses, the weathering of primary phos- phate minerals, and the hydrolysis of inorganic phosphate compounds will be used to provide insight into the reaction mechanism that will play a role in controlling long-term weathering of the waste form. Lastly, we propose a strategy that integrates experimentation and modeling to

40 2012 Glass & Optical Materials Division Annual Meeting Abstracts provide an evaluation of the long-term weathering of phosphate glass in creasing average chain lengths with increasing O/P ratios between 3.0 a near-surface disposal facility. and 3.5. Zn-Al-phosphate glasses were prepared and the nature of the phosphate and aluminophosphate networks were determined using nu- (GOMD-SIV-P046-2012) A High-Energy X-Ray Diffraction Study of clear magnetic resonance spectroscopy and Raman spectroscopy. The Neodymium Doped Sodium Phosphate Glasses phosphate anion distributions in the glass structures were determined K. Marasinghe*, E. Gunapala, University of North Dakota, USA; R. Brow, using high pressure liquid chromatography of aqueous solutions pre- Missouri University of Science & Technology, USA; L. Skinner, C. Benmore, pared by dissolving glass powders, and were found to be in good agree- Argonne National Laboratory, USA ment with phosphate tetrahedral distributions determined by NMR. The atomic-scale structure of neodymium doped sodium phosphate The effects of the different modifying cations (Zn2+and Al3+) on the (NdNaP) glasses of composition (Nd2O3)x(Na2O)y(P2O5)1-x-y where anion distributions will be discussed and related to the compositional 0.04 < x < 0.13, and x + y ~ 0.4 have been studied using the high energy trends in glass properties. X-ray diffraction technique. Inter-atomic distances, coordination num- (GOMD-SIV-P050-2012) Effect of Crystal Nucleation Rates on DSC bers, and their dependence on the neodymium concentration have been Crystallization Peaks investigated. Emission spectra of these glasses show that their flores- A. A. Cabral*, A. M. Rodrigues, A. M. Carvalho, Federal Institute of Maranhao, cence efficiency decreases with increasing neodymium content suggest- Brazil ing even at these very low rare earth concentrations. Nd-O coordination number decreases from approximately 9 to 6 as x increases from ~ 0.05 It has been assumed that the height of the crystallization peak, (dT)p, to ~ 0.13. Structural changes induced by neodymium doping appear to and the reciprocal of the crystallization peak temperature, 1/Tp, should occur at much smaller neodymium concentrations in these glasses as increase as a function of nucleation heat-treatment time as a direct re- compared to neodymium phosphate (NdP) glasses. In contrast, those sult of the increasing concentration of nuclei in the glass. In this study, structural changes occur at an approximate [O]/[P] ratio of 2.9 – 3 in monolithic pieces of fresnoite (2BaO.TiO2.2SiO2) and lithium dissili- both NdNaP and NdP glasses. cate (Li2O.2SiO2) were heat-treated in a DSC furnace. The results demonstrated that these glasses have similar behavior with respect to (GOMD-SIV-P047-2012) The crystallization of lithium-iron- peak crystallization temperature, i.e., 1/Tp decreases with fn. But the re- phosphate glasses with substitutes sults with the B2TS2 samples demonstrated that (dT)p increases with R. Yang, H. Liu, Y. Wang, H. Jiang, S. Liu*, University of Jinan, China rising heating rates for nucleation (shorter nucleation heat treatments Crystallization of lithium-iron-phosphate (LIP) glasses can give rise to times), fn, whereas (dT)p was found to decrease with fn in the LS2 spec- materials which may find applications in rechargeable lithium ion bat- imens. This unexpected behavior is attributed to the different orders of teries or magnetic field. LIP glasses with a basic molar composition of magnitude of the crystal nucleation rates in these glasses. 20Li2O-30Fe2O3-50P2O5 and with alkali and alkali-earth oxides as (GOMD-SIV-P051-2012) Non-isothermal Crystallization Kinetics of substitutes were prepared. All the glasses exhibit a surface crystalliza- a Na-Fluorrichterite Glass-Ceramic Precursor tion. However, the LIP glasses containing Na2O or K2O have reduced J. Pérez*, R. Casasola, M. Romero, J. Rincón, CSIC, Spain degree of crystallization. The basic LIP glass has LiFeP2O7 as the crys- talline phase after thermal treatments. It is shown that when the amount Na-fluorrichterite glass-ceramics have better mechanical properties of Na2O or K2O is more than 4 mol%, NaFeP2O7 or KFeP2O7 crystal- compared with current commercial glass-ceramics because of their in- lizes as the second phase besides Li FeP2O7. The substitutions of Li2O terlocking acicular microstructure. The present work shows the kinetic with alkali-earth oxides including MgO, CaO and BaO more signifi- study on a previously nucleated Na-fluorrichterite glass carried out by cantly suppress the crystallization of the LIP glass than those with Na2O DSC. The results were obtained by different non-isothermal procedures or K2O. The alkali-earth oxides as the substitutes do not alter the crys- (Kissinger and Kissinger-Akahira-Sunose (KAS) methods). The Avrami talline phase. parameter was determined by Ozawa and Malek equations. They have pointed out the coexistence of surface and bulk crystallization in the de- (GOMD-SIV-P048-2012) Synthesis and structural characterization vitrification process of the studied glass. The kinetic study has shown of copper based lithium phosphate glasses that the activation energy of the crystallization process is over 400 C. Mugoni*, M. Montorsi, C. Siligardi, H. Jain, University of Modena and kJ/mol, and the mechanism proposed is a JMA with n = 3. The variation Reggio Emilia, Italy of the activation energy with crystallization by the KAS method has Phosphate glasses are of much scientific and technological interest be- shown that the crystallization process undergoes a multiple mechanism cause of their several application fields including fast ion conductors, with the main part of the whole process corresponding to a three-di- biomedical components and optical devices. Studies on these glassy ma- mensional growth of crystals. terials were mainly conducted in order to explore their structural prop- (GOMD-SIV-P052-2012) Crystallization of red mud-based glasses erties. Indeed, it is known that the properties that make them good can- containing BaO, SrO, and ZrO2 didates for so many different applications are related to their molecular H. Vieira*, Nuclear and Energy Research Institute, Brazil; R. K. Brow, Missouri level structure. In the present work, glasses with compositions belong- University of Science and Technology, USA; J. R. Martinelli, Nuclear and Energy ing to copper lithium phosphate systems (50-x Li2O-xCu2O-50P2O5, Research Institute, Brazil 0

2012 Glass & Optical Materials Division Annual Meeting 41 Abstracts

(GOMD-SIV-P053-2012) Bioactive Glass Implants for Bone Repair ated with the symmetric oxygen breathing vibrations in 4-member made by Selective Laser Sintering rings) seems to take much longer time to recover. M. Velez, Mo-Sci Corp., USA; K. Kolan*, M. Leu, G. Hilmas, Missouri University of Science & Technology, USA; S. Jung, Mo-Sci Corp., USA; D. E. Day, Missouri 10:20 AM University of Science & Technology, USA; T. G. Chu, Indiana University, USA (GOMD-SI-021-2012) Experimental and Computational Studies of Sodium Silicate Glasses Bone disease and fracture due to aging and accidents is a relevant bur- Q. Zhao, M. Guerette, G. Scannell, L. Huang*, Rensselaer Polytechnic Institute, den on society. There are over 6.2 million bone fractures in the U.S. each USA year and 10% fail to heal properly due to a delayed union. Osteoporosis is projected to affect 14 million people by 2020, resulting in health care In-situ Raman and Brillouin spectroscopy together with molecular dy- costs of over $25 billion per year. Selective Laser Sintering (SLS) was namics (MD) simulations were used to study Na2O-SiO2 glasses con- used to fabricate scaffolds for bone repair using 13-93 bioactive glass taining a wide range of Na2O concentration (0-40 mol%). A strong cor- particles. The SLS scaffold prototypes were used as femur substitutes in relation was found between the dynamic properties of glass at ambient segmented defects in rats. From X-ray imaging, the scaffolds with BMP- conditions and the evolution of its elastic properties with increasing 2 appeared to close the defect gap as expected, showing cortical bone temperature and pressure. For silica-rich glasses, characterized by the bridging for at least one side of the cortical bone at 3 and 6 weeks. Forty main band in Raman spectra or by modes populated around 400 cm-1 percent of the scaffolds showed cortical bone bridging in one side of the in vibrational density of states (VDOS) at ambient conditions, glasses cortical bone while twenty percent showed bridging in both cortexes at behave abnormally (stiffening upon heating and softening upon com- 6 weeks. pression). In sodium silicates glasses with high Na2O concentration (>20 mol%), these characteristic bands in Raman or VDOS at ambient conditions gradually diminish due to the loss of the network connectiv- Tuesday, May 22, 2012 ity, glasses behave like normal solids (softening upon heating and stiff- ening upon compression). In between, intermediate glasses emerge, Symposium I: Glass Science whose elastic moduli don’t change with temperature and pressure. 10:40 AM Session 1: Glass Structure and Properties III (GOMD-SI-022-2012) Anomalous compressibility of vitreous silica Room: Salons E, F, & G illuminated: Polyamorphism and the effect of hydration Session Chair: Sabyasachi Sen, University of California, Davis A. N. Clark*, C. E. Lesher, S. Sen, University of California, Davis, USA; S. D. Jacobsen, Northwestern University, USA; Y. Wang, Univeristy of Chicago, USA 9:20 AM The P-V equation of state of silica glasses with different OH contents (GOMD-SI-019-2012) Densified silica glass : structure and were measured from 0-9 GPa and at ambient temperature by high pres- properties (Invited) sure X-ray microtomography and GHz ultrasonic interferometry to in- B. Champagnon*, C. Sonneville, A. Kassir-Bodon, C. Martinet, T. Deschamps, D. vestigate the mechanistic origin of anomalous compressibility. Vitreous de Ligny, CNRS-University Lyon1, France; G. Kermouche, CNRS-ENISE, silica with <100 ppm OH shows a smooth reduction in volume and France; S. Le Floch, A. San Miguel, CNRS-University Lyon1, France; R. Lacroix, compressibility below 3 GPa is higher than previously reported in the J. Teisseire, E. Barthel, CNRS-Saint-Gobain, France literature. Vitreous silica with ~200 ppm OH shows complex P-V be- Pressure induced structural transformation of glasses is of fundamental havior with high compressibility near 1 GPa bounded at lower and interest and important from a technological point of view. The concept higher pressures by regions of lower compressibility than previously re- of polyamorphism characterized by Low Density Amorphous (LDA) ported. The bulk modulus K obtained from GHz ultrasonic interferom- and High Density Amorphous (HDA) “phases” is extensively studied. etry displays anomalous behavior with K decreasing from 0.3-1 GPa Silica is widely studied but nevertheless the densification processes tak- while lower and higher pressures display normal behavior. These results ing place at a microscopic level are not fully understood. We will focus indicate that the anomalous compressibility is due to a polyamorphic on densified silica and in particular on the evolution of the elastic be- phase transition and increasing the OH content extends the stability havior of densified silica with high pressure. The progressive vanishing field of the low-pressure phase. of the elastic anomaly with the rate of densification of silica is followed 11:00 AM by Raman and Brillouin scattering in situ under pressure (in a Diamond Anvill Cell).The structure of permanently densified silica samples, (GOMD-SI-023-2012) Structure and Properties of Compressed quenched from high pressure and temperature (in a Belt high pressure Borate Glasses device experiment) is also discussed. Moreover the mechanical proper- M. M. Smedskjaer*, Corning Inc., USA; U. Bauer, H. Behrens, Leibniz University ties of densified silica are studied by indentation and large changes in Hannover, Germany; S. Striepe, J. Deubener, Clausthal University of Technology, hardness with densification are demonstrated. Germany; R. E. Youngman, M. Potuzak, J. C. Mauro, Corning Inc., USA; Y. Yue, Aalborg University, Denmark 10:00 AM While the influence of thermal history on the structure and properties (GOMD-SI-020-2012) In-situ Raman and Brillouin light scattering of glasses has been thoroughly studied in the past century, the influence studies of pressure-quenched glasses of pressure history has received considerably less attention. In this study, M. Guerette*, L. Huang, Rensselaer Polytechnic Institute, USA we investigate the pressure-induced changes in structure and properties In-situ high temperature and high pressure Raman and Brillouin spec- in a series of borate glasses. Upon isostatic compression, NMR experi- troscopy have been used to study the structure and elastic properties of ments show that the fraction of tetrahedral boron increases, leading to silica-rich glasses quenched from temperatures near the glass transition an overall decrease of the molar volume of the network. We correlate under pressures up to 4 GPa. With the increase of the quenching pres- these structural changes with changes in elastic moduli from Brillouin sure, the elastic moduli of as-quenched glasses increase substantially, scattering experiments, hardness and crack formation from nanoinden- and the anomalous behaviors (positive temperature derivative and neg- tation experiments, and overshoot in isobaric heat capacity from DSC ative pressure derivative of elastic moduli) in silica-rich glasses gradu- experiments at ambient pressure. The influence of the initial boron spe- ally diminish. Detailed studies of the relaxation of densified glasses as a ciation on the degree of changes in structure and properties will also be function of time and annealing temperature will be presented as well. discussed. Our studies show that after densified glasses relax back to the undensi- fied state based on the elastic properties and the major characteristic bands in Raman spectra, yet the D1 line (~492 cm-1, generally associ-

42 2012 Glass & Optical Materials Division Annual Meeting Abstracts

11:20 AM 10:20 AM (GOMD-SI-024-2012) Effect of Network Polymerization on the (GOMD-SI-055-2012) A Virtual Reality Tool for Studying the Pressure-Induced Structural Changes in Multi-component Silicate Microstructure and Ion Dynamics of Glassy Materials Glasses and Melts (Invited) Z. Zhou*, Shanghai University, China; G. N. Greaves, E. Flikkema, Aberystwyth S. Lee*, Seoul National University, Republic of Korea University, United Kingdom With an aim of establishing a systematic relationship between pressure, In comparison with crystalline materials, the atomic microstructure composition, and glass structures, we report multi-nuclear NMR spec- and dynamics of glasses are difficult to visualize because periodicity is tra for diverse multi-component silicate glasses with varying composi- not available as a spatial reference. We have developed a virtual reality tion and pressure up to 8 GPa. The fraction of [5,6]Al at a given pressure (VR) tool based on VSG Avizo to ease the difficulty by extracting graph- vary nonlinearly with variations of NBO/T. [5,6]Al fraction at 8 GPa in- ical structural information with 3 spatial dimensions as a function of creases with decreasing degree of melt polymerization from the fully time. The VR tool in conjunction with state-of-the-art ab initio calcula- polymerized glasses to partially depolymerized glases and then it then it tion, molecular dynamics simulation, as well as experimental observa- gradually decreases with a further decrease in the melt polymerization. tion, such as 3D atom probe, is enabling the complexity of ion dynamics This observed trend in the densification behavior at a given pressure in- within the network structure to be deciphered quantitatively. In this dicates competing densification mechanisms involving steric hindrance paper, we demonstrate the functionality of the computational tool, and vs. changes of NBO fraction in the silicate melts. The NMR results also how significant visualization methods can be in extending dynamic suggest that the distribution of non-network forming cation is homog- atomistic configurations obtained from simulations and experiments. enous around both NBO and BO at high pressure without spatial segre- gation of silica-rich and alkali-rich domains. 10:40 AM (GOMD-SI-056-2012) A new force field for ion-conducting network glasses with general composition wLi O-xB O -ySi O -zP O Session 3: Atomistic Simulation and Modeling of 2 2 3 2 4 2 5 C. R. Trott*, Technische Universitaet Ilmenau, Germany; M. Schuch, P. Maass, Glass I Universitaet Osnabrueck, Germany Room: Salon A A new force field for glasses with general composition wLi O-xB O - Session Chair: Jincheng Du, University of North Texas 2 2 3 ySi2O4-zP2O5 is presented that involves Coulomb and Buckingham con- 9:20 AM tributions as well as O-B-O and O-P-O bond-angle terms. The a priori large number of more than 50 parameters is strongly reduced by requir- (GOMD-SI-053-2012) Molecular Dynamics Simulations of Network ing that (i) the parameters of the Buckingham part for X-X- and Li-X- Dilation Anomaly in Ion-Exchanged Glass (Invited) interactions (X=Si, B, and P) are the same and equal to those of the A. Tandia*, V. Deenamma, J. C. Mauro, Corning Incorporated, USA; A. K. Habasaki potential for lithium silicate glasses, and (ii) the units Li O, Varshneya, Alfred University, USA 2 SiO2, B2O3 and P2O5 are charge-neutral. After optimization of the 7 re- Chemically strengthened glasses are of increasing technological impor- maining parameters, the resulting potential reproduces experimental tance for personal electronic devices, tablet computers, and a variety of data of structural, thermodynamic, and ion transport quantities with other applications. However, there are many unexplained phenomena comparable or even higher agreement than previously reported ones for associated with the physics of the ion-exchange process used for lithium conducting glasses with only one network former. The new strengthening. One of the most puzzling of these is the anomalous be- force field opens a way to study effects of glass former mixing on the havior of the network dilation coefficient, i.e., the parameter governing basis of a common force field. the amount of linear strain of the glass per unit of alkali ions exchanged, which is inevitably a factor of 2-4 higher for as-melted glasses as com- 11:00 AM pared to chemically strengthened versions of the same glass composi- (GOMD-SI-057-2012) Effect of Second-Shell Neighbors on the IR tions prepared by ion-exchange. We investigate the atomistic origin of Vibrational Modes in Silicate Glasses via MD Simulations this discrepancy between as-melted and ion-exchanged glasses using K. Sebeck*, X. Zhou, J. Kieffer, University of Michigan, USA molecular dynamics simulations. The network dilation anomaly is ex- Characterization of the structure and vibrational behavior of amor- plained by variation of local environments between Na and K sites in phous materials relies on tools such as infrared spectroscopy. The as- the glass network and a two-stage relaxation process of the local K envi- signment of vibrational modes to a structural moiety is commonly ronment after ion-exchange. based on comparison with previously characterized materials or group 10:00 AM theory calculations. The network structure of dense inorganic glasses, however, leads to coupling and energy exchange beyond the first neigh- (GOMD-SI-054-2012) Investigation of Ion-Exchange ‘Stuffed’ Glass bor shell. Using a technique based on the Fourier filtering of atomic tra- Structures by Anisotropically-Bounded Molecular Dynamics jectories generated by molecular dynamics simulations, IR absorption Simulation peaks can be reliably assigned to vibrational modes of structural con- P. K. Kreski*, Alfred University, USA; A. K. Varshneya, Saxon Glass Technologies, stituents, revealing insights into the effects of second shell neighbors Inc., USA; A. N. Cormack, Alfred University, USA and overall network rigidity on the spectral features. We will discuss the Recent work has utilized molecular dynamics simulations to study stuff- influence of the second neighbor shell on the vibrational modes associ- ing alkali accommodation during ion-exchange strengthening of silicate ated with the 960 cm-1 shoulder and the conclusions that can be drawn glasses. Whereas prior work has made use of isotropic boundary condi- from this spectral feature with respect to the underlying glass network tions, the present study applies anisotropic boundary conditions allow- structure. ing free expansion in one dimension to better model the conditions found in laboratory glasses. Results are compared against those of 11:20 AM isotropically-bounded simulations and observations of laboratory (GOMD-SI-058-2012) Simulating the luminescence of Eu3+ ions in glasses. Specifically, direction-sensitive linear network dilatation coeffi- silicate glasses and the effect of the distribution of Eu3+ ion sites cient and structural features, such as coordination distributions and G. Mountjoy*, Q. Ting, University of Kent, United Kingdom bond angle distributions, are examined. Molecular dynamics has been used to make models of Eu3+ doped silica and sodium silicate glasses. The results provide an insight into the driv- ing force for clustering of Eu3+ ions in silicate glasses. The models can also be used to predict the distribution of distances between Eu3+ ions which is important for phenomena such as concentration quenching.

2012 Glass & Optical Materials Division Annual Meeting 43 Abstracts

Eu3+ ions are found in a range of different local environments in the fringe alignment with the planet. The interference pattern suppresses molecular dynamics models. The details of these local environments intense starlight, while efficiently transmitting dim planet light. The have been combined with the Superposition Model for crystal field the- photonic interferometer element is patterned directly into a multilayer ory to simulate optical emission and absorption spectra for each indi- chalcogenide thin film structure using laser photomodification. This vidual Eu3+ ion. The results reveal which features of local environment approach provides rapid fabrication of high performance, mid-infrared have the biggest effect on the crystal field strength and hence inhomoge- transparent photonic components. Device characterization confirmed neous linewidth broadening. The insights from these results can be use- low propagation loss, single mode operation, and high fringe visibility. ful for understanding the relationship between glass compositions and luminescence properties. 10:20 AM (GOMD-SII-021-2012) Thermally evaporated chalcogenide thin 11:40 AM films for mid-infrared applications: materials analysis, device design, (GOMD-SI-059-2012) Nanoindentation Study of Densified Silica fabrication, and testing Glass by Molecular Dynamics Simulations V. Singh*, A. M. Agarwal, L. C. Kimerling, Massachussetts Institute of F. Yuan*, L. Huang, Rensselaer Polytechnic Institute, USA Technology, USA; J. Hu, University of Delaware, USA; J. Wilkinson, Massachussetts Institute of Technology, USA; J. D. Musgraves, K. Richardson, J. Molecular dynamics (MD) simulations, based on a charge-transfer Giammarco, I. Luzinov, Clemson University, USA; J. M. Hensley, K. M. three-body potential and a pairwise potential (BKS), were used to study Parameswaran, D. M. Scherer, B. D. F. Casse, Physical Sciences Inc., USA; C. S. densified silica glass prepared either by pressure-quenching from the Kim, W. W. Bewley, C. L. Canedy, I. Vurgaftman, J. Abell, J. R. Meyer, Naval liquid state or by hydrostatic compression-decompression in the glassy Research Laboratory, USA; M. Kim, Sotera Defense Solutions, USA stage. Large-scale MD simulations of nanoindentation tests were carried out in normal and densified silica glass by using both potentials. A re- Many chemical and biological species of interest exhibit strong optical duction of brittleness as well as an enhancement of hardness with in- absorption at mid-infrared (MIR) wavelengths. The development of in- creasing density of silica glass was generally observed. The correlation terband cascade lasers operating at room temperature and planar between densification, shear flow and Poisson’s ratio of silica glass was chalcogenide glass (ChG) resonators makes it feasible to construct a examined and a qualitative explanation was proposed. Furthermore, a compact system for highly selective chemical sensing based on integrat- systematic comparison between the charge-transfer three-body poten- ing a laser, sensing element, and detector on a common platform. Our tial and the pairwise potential was conducted to study the influence of approach towards this goal employs polymer coated ChG resonators three-body interaction in the deformation mechanisms of densified sil- coupled to waveguides to accomplish sensitive biochemical detection ica glass. via cavity enhanced spectroscopy. Here we present our initial work on the development of these sensors including materials evaluation and de- vice design and fabrication. Thin films of thermally evaporated ChG Symposium II: Optical Materials & Devices have been investigated. Waveguides and resonator devices based on these glasses have been designed via simulation, fabricated using Session 3: Planar Glass Photonics CMOS-compatible processes, and tested at telecom and MIR wave- Room: Salon B lengths. Session Chairs: Norm Anheier, Pacific Northwest National Lab; Juejun 10:40 AM Hu, University of Delaware (GOMD-SII-022-2012) On-chip integration of mid-IR sources and 9:20 AM detectors using planar and 3D chalcogenide glass structures (GOMD-SII-019-2012) Planar Mid Infrared Integrated Glass-on- Y. Zha, M. Waldman, C. Lu, C. B. Arnold*, Princeton University, USA Silicon Microphotonics for Imaging and Sensing (Invited) With the advance of small scale mid-infrared sources and detectors it A. M. Agarwal*, MIT, USA has become increasingly important to create integrated components for reducing system size and improving the optical efficiency. In particular, The MIR regime is extremely interesting for hyperspectral imaging and one of the key challenges is the ability to integrate these components chem-bio sensing because most chemical and biological toxins have with waveguides and fibers without excessive loss. In this presentation, their fingerprints in this range. Our work on MIR materials and devices we discuss the use of drop-casting and soft-lithographically patterned creates a planar, integrated, Si-CMOS-compatible microphotonics plat- arsenic sulfide to directly integrate 2-d and 3-d waveguide structures form which enables on-chip imaging and sensing. Challenges and op- with quantum cascade sources for use in mid-IR applications in sensing portunities associated with planar integration of non-traditional glass and detecting. The deposited structures are analyzed for their ability to materials with silicon photonic components such as light sources, sen- reduce loss as compared to free-space optics. Finally implications for 3- sors, detectors, and imagers are presented. For imaging, we demonstrate D structures that enable higher density integration of components and low-cost resonant-cavity enhanced narrow-band photon detectors for devices will be discussed. enabling large-area multi-spectral infrared digital cameras for advanced detection and intelligence applications. For sensing, we demonstrate a 11:00 AM planar glass-on-silicon-based highly sensitive and selective chem-bio (GOMD-SII-023-2012) Chalcogenie Glass 1-D Photonic Crystal sensor that integrates several key photonic and electronic functions. Cavities for Single-molecule Mid-infrared Photothermal 10:00 AM Spectroscopy: Theory and Design (GOMD-SII-020-2012) A Mid-Infrared Integrated Chalcogenide H. Lin*, Y. Zou, J. Hu, University of Delaware, USA Nulling Interferometer for Extrasolar Planet Detection We propose and theoretically examine a novel mid-infrared (mid-IR) N. Anheier*, B. Bernacki, H. Qiao, Pacific Northwest National Lab, USA; L. photothermal spectroscopic sensing technique using chalcogenide glass Labadie, I. Physikalisches Institut, Universität zu Köln, Germany photonic crystal nanobeams. Chalcogenide glasses (ChGs) are identi- fied as the ideal material for photothermal spectroscopy device fabrica- We present the design, fabrication, and characterization of a chalco- tion given their low thermal conductivity, large refractive index and genide integrated optical beam combiner for mid-infrared (3-16 μm high thermo-optic coefficient. By using a Bloch mode engineering ap- wavelength) astrophysics research. The beam combiner is a key photon- proach, we designed and numerically analyzed high quality factor 1-D ics component for next generation nulling interferometry designs that nanobeam photonic crystal cavities for gas phase molecular sensing will enhance extrasolar Earth-like planet detection and spectroscopic using a pump-probe configuration. Unlike conventional mid-IR spec- analysis. The interferometer superimposes a destructive null fringe over troscopy, the technique also eliminates the need for cryogenically cooled the star, as the pathlength difference is adjusted to obtain constructive mid-IR photo-detectors, as optical detection is performed solely at the

44 2012 Glass & Optical Materials Division Annual Meeting Abstracts near-IR probe wavelength. Our result indicates that the dramatically how far we have come to explain most striking features of the mixed al- amplified photothermal effect in a ChG nanobeam cavity potentially kali effect. enables single small molecule detection. 10:40 AM 11:20 AM (GOMD-SIV-003-2012) Structural Aspects of the Mixed Alkali Effect: (GOMD-SII-024-2012) Fabrication of Two-dimensional Photonic A Solid State NMR Point of View (Invited) Crystals on Erbium Doped Tellurite Thin Films and its Anisotropic H. Eckert*, F. Behrends, S. Puls, J. Epping, S. Faske, WWU Münster, Germany Photoluminescence The ion transport properties in glasses are thought to be closely related P. Lin*, M. Vanhoutte, MIT, USA; J. Hu, University of Delaware, USA; N. Patel, to the local environments and spatial distributions of the cations in the V. Singh, Y. Cai, R. Camacho-Aguilera, J. Michel, L. Kimerling, A. Agarwal, MIT, material. Modern solid state NMR methods focusing on the measure- USA; C. Dimas, Masdar Institute of Science and Technology, United Arab ment of magnetic dipole-dipole interactions are uniquely suitable to Emirates provide new quantitative insights into this topic for both single- and 3+ Two dimensional photonics crystals (PhCs) are fabricated on Er -TeO2 mixed alkali glasses. Specifically for mixed alkali glass systems, statistical thin film. The PhC structures are written by dual beam focused ion unlike-cation mixing is observed when the cation size differences are beam (FIB). Highly uniformed patterns with smooth surfaces are ob- small, while partial segregation effects are apparent in systems with large served. PhC arrays with periodicities from 350 nm to 1700 nm are gen- cation size differences. {23Na}7Li crosspolarization experiments suggest erated in order to examine the PL extraction efficiency. Strong photolu- that Li+ ions in sodium-rich environments are less mobile than Li+ ions minescence (PL) at 1530 nm is achieved by 488-532 nm laser pumping. located in lithium-rich environments. The thin film PhCs demonstrate broadband anisotropic PL emission. A 60 % enhancement of surface extraction efficiency is achieved when 11:20 AM PhC with periodicity a=800 nm is applied. PL intensity profiles are cal- (GOMD-SIV-004-2012) Structure and Dynamics of Mixed Alkali culated by two dimensional finite difference time domain (FDTD) Glasses Formed by Ion Exchange (Invited) method. The experimentally observed anisotropic emission agrees well E. I. Kamitsos*, National Hellenic Research Foundation, Greece with the simulation results. The broadband anisotropic PL from Er3+ - Despite numerous reports on ion-exchanged glasses there are still fun- TeO thin film PhCs paves the way for integrated photonic circuits. 2 damental questions on structure and ion transport in the ion-ex- changed layer. While most previous studies have focused on commercial Symposium IV: Festschrift to the Glass soda-lime silicate glasses, we report also on structure and dynamics of K/Na exchanged borate glasses at temperatures below Tg. Infrared re- Research Career of Prof. Delbert E. Day flectance measurements on ion-exchanged 0.3Na2O-0.7B2O3 glasses showed local structural changes, which point towards the occurrence of Session 1: The Mixed Alkali Effect and Ion cation-induced sub-Tg structural relaxations of the borate network. The conductivity spectra of the ion-exchanged glasses are dominated by Conducting Glasses I two distinct responses, one at the high and the other at the low fre- Room: Grand Suites II & III quency regime. The former response is determined primarily by proper- Session Chair: David Sidebottom, Creighton University ties of the base glass and the latter is attributed to the presence of a highly resistive ion-exchanged layer. The characteristics of this ion-ex- 9:20 AM changed layer are discussed in relation to structural and dynamic prop- (GOMD-SIV-001-2012) Day’s Studies of Internal Friction and Ionic erties of melt-grown mixed K-Na borate glasses. Diffusion in Silicate Glasses (Invited) J. E. Shelby*, Alfred University, USA Symposium I: Glass Science Del Day began his career by studying the internal friction of sodium aluminosilicate glasses. His first major research grant after arriving at Rolla funded a study of the internal friction of mixed alkali silicate and Session 1: Glass Structure and Properties IV aluminosilicate glasses. This work expanded our knowledge of internal Room: Salons E, F, & G friction effects in glasses and eventually led to Day’s work on alkali dif- Session Chair: Randall Youngman, Corning Incorporated fusion in glasses. The study of both sodium and rubidium diffusion in mixed alkali silicate glasses resulted in our current understanding of the 1:20 PM effect of mixing alkali ions on the transport of charges in glasses, i.e. that (GOMD-SI-025-2012) Internal Residual Stresses in Lithium Diborate the ions act independently based on their own concentration in the Glass-Ceramics glass. The “mixed alkali effect” is a natural result of this general phe- F. C. Serbena*, State University of Ponta Grossa, Brazil; L. Ghussn, R. M. Reis, E. nomena. This presentation will review the work in Day’s group on inter- D. Zanotto, Federal University of São Carlos, Brazil nal friction and diffusion of ions in glasses. Glass-ceramics (GCs) are polycrystalline materials prepared by con- 10:00 AM trolled crystallization of one or more crystalline phases embedded in a (GOMD-SIV-002-2012) Revisiting a prominent review: Do we glass matrix. An open problem related to the mechanical performance understand the most striking features of the mixed alkali effect? of GCs refers to the type and level of residual stresses around the crys- (Invited) talline precipitates that arise due to thermal and elastic mismatch be- P. Maass*, University of Osnabrück, Germany tween the crystals and the glass matrix. In this work, we measured hard- ness, elastic modulus, indentation fracture toughness and residual In 1976 Delbert E. Day published a prominent review on the mixed al- stresses in a lithium-boron-oxygen GC containing a low volume frac- kali effect, where he classified quantities to show slight, small, moderate, tion of crystals embedded in the glass matrix using XRD synchrotron and major deviations from an additive mixing behavior, if one type of radiation. Residual stresses are still being evaluated for several heat mobile ion is successively replaced by a second type of mobile ion in a treatments. Our first analysis for one particular heat treatment revealed glass. Since then experimental and theoretical work have unraveled residual stress relieve due to precipitate microcracking. The experimen- many of the mysteries of this effect, which, due to its universal occur- tal results are compared with theoretical models. rence, is believed to be of fundamental importance for our understand- ing of ion transport in glassy materials. With a focus on the quantities showing major deviations from additive mixing behavior it is discussed

2012 Glass & Optical Materials Division Annual Meeting 45 Abstracts

1:40 PM 2:40 PM (GOMD-SI-026-2012) Heterogeneities, phase separation and (GOMD-SI-029-2012) Silicate Glasses at the Ionic Limit: Alkaline- nucleation in silicate glasses Earth Sub-Orthosilicates L. Cormier*, O. Dargaud, N. Menguy, UPMC - CNRS, France; G. Patriarche, N. Nasikas, Institute of Chemical Engineering and High Temperature Chemical CNRS, Laboratoire de Photonique et de Nanostructures, France Processes FORTH, Greece; T. Edwards, S. Sen*, University of California, Davis, USA; G. Papatheodorou, Institute of Chemical Engineering and High Glasses are not homogeneous materials but exhibit strong tendency to Temperature Chemical Processes FORTH, Greece segregate and phase-separate. However, comprehensive compositional or structural information below about 50 nm are limited. We present an Container-less levitation techniques and CO2 laser heating were used to investigation using scanning transmission electron microscopy in high prepare a series of novel silicate glasses along the compositional join (1- angle annular dark field imaging mode (STEM-HAADF) to determine x)(Ca,Mg)O-xSiO2 beyond the orthosilicate limit for the first time with the glass structure at the nanometer scale, coupled with chemical reso- x ranging from 0.33 down to 0.27. Raman and 29Si NMR spectroscopic lution. In MgO-SiO2-Al2O3 glasses containing ZrO2/ZnO, we observed measurements show complete loss of connectivity between the SiO4 that glass structure is intrinsic inhomogeneous, with Zr/Zn atoms seg- tertahedra in glasses with x < 0.3. The corresponding glass structures are regated in enriched-domains. We show that the self-organization of the characterized by isolated negatively charged “tetrahedral” SiO44- and parent glass structure drives directly the crystallization and explains the O2- anions with M2+ (M=Mg,Ca) as the counter cations, held together efficiency of crystal formation in glass ceramics [1]. [1] O. Dargaud, L. by pure Coulombic (ionic) interactions. This structural view is also sup- Cormier, N. Menguy, G. Patriarche, G. Calas, Mesoscopic scale descrip- ported by semiempirical MO simulations which were used to derive the tion of nucleation processes in glasses, Appl. Phys. Lett., 99 (2011). structure of the Ca,Mg sub-orthosilicate glass 0.5(1-x)CaO - 0.5(1- x)MgO - xSiO2 with x=0.286. 17O MAS and 3QMAS NMR results pro- 2:00 PM vide direct evidence of the presence of “free” oxygen atoms in the struc- (GOMD-SI-027-2012) Evidence for self-organization in Borate tures of all glasses. Structure-property relationships in these glasses will Glasses be discussed. P. Boolchand, K. Vignarooban*, Univ of Cincinnati, USA; M. Micoulaut, University of Paris 6, France; M. Malki, University of Orleans, France; R. Kerner, 3:20 PM University of Paris 6, France (GOMD-SI-030-2012) Fictive temperature measurement of silica and doped-silica glasses using FTIR method: glass containing Si-H Experiments using Raman scattering , IR reflectance, modulated DSC, bonding and thick sample AC conductivity and molar volumes on (Na2O)x(B2O3)1-x glasses are C. Li*, M. Tomozawa, Rensselaer Polytechnic Institute, USA undertaken as a function of soda content in the 0 < x < 45% range. A re- versibility window is observed in the 20% < x < 40% range, with walls A simple IR method using silica structural band at ~2260 cm -1 was de- identified respectively with the stress- (xc(1) = 20%) and the rigidity- veloped, some years ago, to determine the fictive temperature of silica transition (xc(2) = 40%). In Raman scattering a triad of modes (705 and high silica glasses. The method has been used to determine the fic- cm-1, 740 cm-1, 770 cm-1 )is observed next to the Boroxyl ring mode tive temperature of silica glasses with unknown thermal history as well (808 cm-1). The fractional scattering strength of the 770 cm-1 mode as for the study of relaxation kinetics. In the present study, the same shows a maximum as x increases to x =25%, suggesting that sodium tri- technique using silica structural band at ~ 2650 cm -1 was explored and borate units percolate at the stress transition. Raman scattering also sug- was found to be advantageous in some applications. One advantage is gests that sodium-diborate (740 cm-1) and sodium tripentaborate (705 for silica glasses containing Si-H bonding since Si-H gives absorbance cm-1) units percolate near the rigidity transition. Conductivity meas- close to ~2260 cm-1. The other advantage is that thick samples can be urements show a two orders of magnitude jump across the stress transi- used since the absorbance per unit thickness is less for ~2650 cm-1. tion, suggesting that carrier mobility increases as networks become With the use of a thicker sample, the effect of surface effect can be min- stress-free in the Intermediate phase. imized. Some examples of the advantage of the use of ~ 2650 cm-1 will be demonstrated. 2:20 PM (GOMD-SI-028-2012) The structure of binary high alumina Al2O3- 3:40 PM SiO2 glass forming liquids (GOMD-SI-031-2012) Simulations of the Effect of the Addition of L. B. Skinner*, Stony Brook University, USA; C. J. Benmore, Argonne National Phosphate on Er-doped Silica Glasses Lab, USA; R. Weber, Materials Development Inc., USA; J. B. Parise, Stony Brook H. Inoue*, The University of Tokyo, Japan; A. Masuno, The University of Tokyo, University, USA Japan; Y. Saito, Sumitomo Electric Industries, Ltd, Japan Aluminosilicate glasses are used in many high-performance technologi- The structural models for SiO2, SiO-P2O5 and SiO2-Al2O3-P2O5 cal applications as they can withstand high temperatures and are good glasses doped with Er ions were prepared by means of the molecular dy- electrical insulators, high alumina glasses are also resistant to chemical namics technique. The emission spectra of the Er ions were calculated attack from alkalis. Binary alumino-silicates are also interesting as they from the structural models. For oxygen around Er ions, the effect of the represent an extreme case of oxygen deficiency for a corner shared tetra- addition of P2O5 was smaller than that of Al2O3. By the addition of 10 hedral network. i.e. there is less than a 2:1 O:(Al+Si) ratio. How does the mol% of P2O5, the oxygen coordination number of the Er ions was in- network make up for this oxygen deficiency? Do the AlO tetrahedra creased from 4.9 to 5.4. The coordination number at 10 mol% of Al2O3 form oxygen tri-clusters (three tetrahdedra sharing an oxygen corner)?. was 5.9. For the number of cations within 4.2 Å from Er ions, the effect How much higher coordinated AlOn polyhedra are there? How do these of addition of P2O5 was reverse to that of Al2O3. By the addition of features change with Al concentration, and correlate with liquid viscos- Al2O3, the number of the cations increased. On the other hand, the ity? We present results on binary Al2O3-SiO2 glasses, and liquids using number decreased by the addition of P2O5. However, both concentra- levitation, in the composition range 20-66mol% alumina. Diffraction tions of Al and P around Er ions were higher than the average concen- and NMR measurements have been combined with MD and Monte trations. Also, it was found that the additions had an effect on the emis- Carlo simulation techniques to obtain a complete, data consistent struc- sion spectra of Er ions calculated from the structural models. tural model of these glasses.

46 2012 Glass & Optical Materials Division Annual Meeting Abstracts

4:00 PM x)[40Fe2O3-60P2O5] (x= 2-20, mol%) have been investigated by DTA, (GOMD-SI-032-2012) Inert Failure Strain Measurements of Sodium XRD, IR and Mössbauer spectroscopy. Tg increased with increasing Borate Glass Fibers B2O3 content for the glasses in the first series which indicate that boron Z. Tang*, N. P. Lower, Missouri S&T, USA; C. R. Kurkjian, University of addition increases the thermal stability of glasses in this series. The dis- Southern Maine, USA; R. K. Brow, Missouri S&T, USA solution rates of boron containing bulk glasses were found to be around 10-9 gr/cm2.min which are comparable to that of the base iron phos- The two-point bend (TPB) technique was used to measure the failure phate glass. When the B2O3 content was above 14%, new bands related strains of xNa2O (100-x)B2O3 glass fibers in inert conditions (under liq- to BO4 tetrahedral groups have been observed in the IR spectra. Iron uid nitrogen). In such experiments, the effects of extrinsic flaws and en- ions existed as Fe(II) and Fe(III) in glasses and both iron ions had dis- vironmental fatigue are minimized so that intrinsic failure characteris- torted octahedral coordination. Fe2+ fraction was found to be 23% for tics might be determined and related to glass composition and the base glass while it was 10-22% for the boron doped glasses. ± structure. The inert failure strain for pure B2O3 glass is 36 5%; to our knowledge this is the largest inert failure strain ever reported for an oxide glass in a TPB experiment. Failure strains decrease systematically Session 3: Atomistic Simulation and Modeling II Room: Salon A as Na2O contents of glasses increase. The addition of Na2O increases the dimensionality and connectivity of the borate glass structure and hence Session Chairs: Jincheng Du, University of North Texas; Liping Huang, increases its resistance to deformation before failure. Similar correla- Rensselaer Polytechnic Institute tions between inert failure strain and network connectivity have been reported for silicate and aluminosilicate glasses. 1:20 PM (GOMD-SI-060-2012) Structural, dynamic and electronic properties 4:20 PM of sodium-silicate glasses and liquids from ab initio simulations (GOMD-SI-033-2012) Structure-Property Relationships of the (Invited) Mixed Glass Former Glasses 0.2Na2O + 0.2[xBO3/2 +(1-x) SiO2] W. Kob*, L. Pedesseau, S. Ispas, University Montpellier 2, France R. Christensen*, Iowa State University, USA We will present the results of large scale computer simulations of Na2O- Ion-conducting glasses hold the potential for widespread use in batter- 1.5(SiO2) liquids and glasses. In particular we will focus on structural ies, fuel cells, sensors, and thermionic devices. It has been found that the properties of the liquid as well as its relaxation dynamics. For the glass ionic conductivity of ternary alkali glasses can be increased by up to two we will discuss the vibrational and electronic density of states, as well as orders of magnitude at constant alkali concentration by mixing glass the correlations between the local charge density and the bond distance forming anions or cations. However, not all Mixed Glass Former Glasses and bond angles. show a positive, non-additive and non-linear increase in ionic conduc- tivity. In order to increase understanding of this Mixed Glass Former Ef- 2:00 PM fect, a study of multiple ternary systems properties and structures has (GOMD-SI-061-2012) Structural properties of liquid and been undertaken. The y(Na2O) + (1-y)[xBO3/2 + (1-x)SiO2], y = 0.2 amorphous Ge2Se3: first principles studies system, has been found to have a negative deviation from linear in ionic S. Le Roux*, C. Massobrio, Institut de Physique et Chimie des Matériaux de conductivity and its structural causes have been examined through IR, Strasbourg, France Raman, and NMR spectroscopies. The findings of this study will be The structural properties of liquid and amorphous Ge2Se3 were investi- compared to the findings of previous studies on the mixed glass former gated by Car-Parrinello molecular dynamics. The calculated total neu- sodium borophosphate system. tron S(q) and g(r) are in excellent agreement with the experimental re- 4:40 PM sults, both for the liquid and the glass. The two phases exhibit an intermediate range order associated with the Ge-Ge correlations. The (GOMD-SI-034-2012) Space Charge Formation and High Field structure is made predominantly of fourfold coordinated Ge atoms in Properties of Low Alkali Glasses the form of Ge-GeSe3 or Ge-Se4 motifs. There is also a large variety of P. Dash*, M. T. Lanagan, C. G. Pantano, E. Furman, The Pennsylvania State motifs in which Ge and Se are not fourfold and twofold coordinated, re- University, USA spectively. This departure from the standard chemical order decreases Low alkali borosilicate glasses have shown promising trends to be used from the liquid to the amorphous state. In both phases the mis-coordi- as high energy density materials with energy density as high as 35 J/cm3. nated atoms and the homopolar bonds lead to a highly perturbed net- Thickness dependence of this glass on its dielectric breakdown strength work as reflected by the evaluation of the connectivity using ring statis- has been studied and results have shown increase in breakdown strength tics. with decreasing glass thickness. Thermoelectric treatment of these glasses under high voltage and temperature leads to depletion layer for- 2:20 PM mation beneath the anode due to migration of monovalent and divalent (GOMD-SI-062-2012) Molecular Dynamics Simulation of Sodium ions. The thickness of this depletion layer was found to depend on the Borate Glasses poling temperature and voltage and is limited by the intrinsic break- A. Takada*, Asahi Glass Company, Japan; S. Feller, M. Affatigato, Coe College, down strength of the glass. Beyond this field, electronic conduction in USA the depleted layer results in eventual breakdown of the sample. TSDC It is well known that borate glasses show the unique features of struc- measurement show activation energy for Na and Ba motion to be 0.8 eV ture. The addition of network modifier to boron oxide initially trans- and 1.7 eV respectively. Low frequency impedance spectroscopy results forms 3-fold coordinated boron atoms to 4-fold coordinated. The fur- have also confirmed inhomogeneity in a poled glass due to formation of ther additions cause the production of non-bridging oxygen atoms. alkali depleted space charge layer. Moreover, depending on the concentration of network modifier the 5:00 PM generation of a variety of superstructural units has been suggested. In this study, structures of x Na2O-(1-x) B2O3 glasses (0.0< x < 1.0) are (GOMD-SI-035-2012) Structure and Properties of Iron investigated by Molecular Dynamics simulation. Several new accelera- Borophosphate Glasses tion techniques are applied to overcome the process of very slow relax- M. Karabulut*, G. Mamedov, H. Ertap, B. Yuce, O. Bozdogan, Kafkas University, ation to stable glass structure. The calculated structures are compared Turkey with several crystal structures in terms of coordination numbers, Qn Effects of boron addition on the glass forming characteristics, structure species, and superstractural units. Finally, the change of medium-range and properties of iron phosphate glasses with nominal compositions of order in structure depending on the concentration of modifier is dis- xB2O3-(40-x)Fe2O3-60P2O5 (x= 2-20, mol%) and xB2O3-(100- cussed.

2012 Glass & Optical Materials Division Annual Meeting 47 Abstracts

2:40 PM 4:20 PM (GOMD-SI-063-2012) Three-dimensional structure of (GOMD-SI-066-2012) Atom size effect and chemical bonding in multicomponent (Na2O)0.35 [(P2O5)1-x (B2 O3)x ]0.65 glasses by high- rigidity transitions energy x-ray diffraction and constrained reverse Monte Carlo M. Micoulaut*, M. Bauchy, UPMC, France simulations We describe in this contribution how bond-bending and bond-stretch- S. Le Roux*, Institut de Physique et Chimie des Matériaux de Strasbourg, ing constraints can be handled from Molecular Dynamics simulations France; V. Petkov, Central Michigan University, USA using partial bond angle distributions. Applications to the Ge-Se and al-

Experimental structure functions for (Na2O)0.35[(P2O5)1-x(B2O3)x]0.65 kali silicate families in the glassy and liquid state are described, and these glasses, where x = 0.0, 0.2, 0.4, 0.6, 0.8 and 1.0, have been measured by allow to obtain the temperature dependence of all possible constraints. high-energy x-ray diffraction up to 28 Å-1 to obtain atomic g(r) with It provides an interesting means to understand subtle effects found in high real space resolution. The experimental data have been used to rigidity transitions and intermediate phases when e.g. the alkali size is guide constrained reverse Monte Carlo simulations. The resulting mod- increased. els show that the glasses exhibit a very complex atomic-scale structure 4:40 PM that evolves from an assembly of chains of corner shared P(O)4 tetrahe- (GOMD-SI-067-2012) Glass structure with well defined thermal dra for x = 0 to a network of B(O)4 tetrahedra and trigonal B(O)3 units for x = 1. In the glasses of intermediate composition (i.e. 0 < x < 1), P, B history and glassy dynamic C. Scherer*, M. Letz, Schott AG, Germany; F. Schmid, Johannes-Gutenberg and oxygen atoms sit on the vertices of P(O)4, B(O)4 and B(O)3 units mixed in various proportions. Sodium atoms are found to fill up the University, Germany cavities in between the P/B oxygen units in a more or less random man- Glasses have a huge range of applications, however, they are still theoret- ner. ically not well understood. Also experimental access to the structure of 3:20 PM glasses is limited. This motivates the study of glass systems by means of (GOMD-SI-064-2012) Molecular dynamics modelling of iron and computer simulations. In this work a set of glass structures with well de- other phosphate glasses (Invited) fined thermal history is generated on the computer. Each glass structure is created by gradually cooling down a set of 100-200 atoms by means of G. Mountjoy*, University of Kent, United Kingdom a molecular dynamics simulation as long as the system still can be equil- Molecular dynamics simulations with rigid ion potentials have been ibrated in reasonable simulation time. Afterwards, it is quenched down used to model a range of phosphate glasses: pure P2O5, and Na, Ca, Fe to room temperature and used as a starting point for a quantum-me- and Tb phosphate glasses. The results show distinct P bonding to bridg- chanical relaxation by means of density functional theory. Then the vi- ing and non-bridging oxygens as expected, and show reasonable agree- brational spectrum is determined and compared to experimental re- ment with experimental neutron and x-ray diffraction data. The models sults. From the vibrational spectrum a set of thermodynamic quantities, illustrate key differences compared to silicate glasses: lack of bonding to as the temperature dependent specific heat, are obtained and compared bridging oxygens, and durability increasing with modifier content. The to measured data. First successful tests on the model glass former SiO2 latter culminates in the striking chemical durability of iron phosphate are presented. glasses which include non-network oxygens. There is difficulty repro- ducing experimental Qn distributions from NMR, as for other oxide 5:00 PM glasses. This becomes more difficult for compositions where Qm-Qn (GOMD-SI-068-2012) Glass stability parameters and glass forming ordering is expected, such as in ultraphosphates. The models also enable ability. Comparison and opportunities an inspection of modifier cation distributions. The latter can sometimes A. F. Kozmidis-Petrovic*, University of Novi Sad, Faculty of Technical Sciences, be analysed, such as in Tb phosphate glasses, but remain a challenging Serbia topic for other phosphate glasses. If glass stability (GS) criteria show a good correlation with critical cool- 4:00 PM ing rate Rc, they can be used for indirect estimation of glass forming ability (GFA) as well. Besides the already well-known Hruby criterion (GOMD-SI-065-2012) The structural role of ZnO in strontium γ γ β containing bioactive glass: molecular dynamics simulations KH and Lu and Liu criterion we analyzed the following criteria: m, , β’, α , Φ, ζ , ω and ω2. All these criteria we expressed through tempera- Y. Xiang*, J. Du, University of North Texas, USA ture relationships: r =Tx,c/Tg and m= Tl,m/Tg . The possibility of the Bioactive glasses have received much attention in research and clinic ap- existence of a linear relationship between γ and γm, ω2, ζ, ω, β’ and Φ plications. Recent advances of bioglass research have shown that addi- was predicted in our theoretical derivation. This depends on whether we tion of other components such as SrO and ZnO to the traditional bio- can assume that r and m are constants or not in the linear coeffi- glass compositions can lead to improved functionalities such as cients.We analyzed variations of values of r and m for oxide and two antibacterial and tissue growth enhancement. In this paper, we’ve stud- groups of bulk metallic glasses (BMGs). The existence of a linear rela- ied the structure and dynamic behaviors of Na2O-CaO-SrO-ZnO-SiO2 tionship with high R2 factors between γ and γm, ω2, ζ, ω, β’ and Φ was by combining X-ray and neutron diffraction and molecular dynamic confirmed by testing on these groups of glasses. simulations. Detailed local environments around zinc, silicon and mod- ifiers, intermediate-range structures such as Qn distribution and net- 5:20 PM work connectivity are examined. A direct comparison with experimen- (GOMD-SI-069-2012) Fiber Drawing: Basic Principals Model tal X-ray scattering spectra validates the effectiveness of simulation O. A. Prokhorenko*, Laboratory of Glass Properties, USA results. The diffusion behaviors of modifiers and networking forming Fiber drawing process is characterized by sharp decrease of both the cations have also been studied. The ionic diffusivity behavior has been melt layer thickness and temperature. The process is sensitive to param- related the dissolution behaviors of these glasses. eters of the whole system. Fiber parameters also depend on tip location at bushing plate. Steady-state modelling gives an idyllic picture. Fiber parameters change smoothly in space, doesn’t change in time. In reality one faces perturbations of drawing velocity caused by different noises. At high drawing ratio force applied to a single fiber can resonate. Thus, one should use non-steady state model. The model includes all stages of the process (forehearth, bushing, fan of fibers, and non-steady state model of fibers) . The model calculates molten glass flow and tempera- ture distributions in different locations above, in, and below bushing

48 2012 Glass & Optical Materials Division Annual Meeting Abstracts plate. Non-steady state routine calculates responses of individual fibers der x-ray diffraction (P-XRD) are used to verify that the glass-clad sili- (diameter, stress, drawing force) to perturbations at frequencies from con optical fibers possess very low oxygen concentrations and that the 0.1 to 1000 Hz. Non-stationary state model allows finding parameters, SiC is consumed fully during the reactive molten core fabrication. More at which resonance phenomena are minimal. generally, this work shows that the high temperature processing of opti- cal fibers can be an asset to drive chemical reactions rather than be lim- Symposium II: Optical Materials & Devices ited by them. 2:40 PM Session 3: Optical Fibers (GOMD-SII-028-2012) The influence of core geometry on the Room: Salon B crystallography of silicon optical fiber J. Ballato*, S. Morris, T. Hawkins, C. McMillen, P. Foy, Clemson University, USA; Session Chairs: Norm Anheier, Pacific Northwest National Lab; Juejun R. Rice, Dreamcatchers Consulting, USA Hu, University of Delaware In a continued effort to better understand the nature of the crystal for- 1:20 PM mation in crystalline optical fibers, this work studies the role of the (GOMD-SII-025-2012) Recent Developments in IR Glass and Fiber cross-sectional geometry on the resultant core crystallography. More Technology (Invited) specifically, a molten-core approach was used to fabricate silicon optical J. S. Sanghera*, Naval Research Lab, USA fibers clad in silica tubes of either circular or square inner cross-sec- tions. In both geometric cases, the silicon core was found to possess re- Naval Research Laboratory (NRL) is developing chalcogenide glass gions of single crystallinity where specific crystal orientations persisted. fibers for applications in the IR wavelength regions from 1-12 μm. The However, the rotation and tilting angular combination needed to align a chalcogenide glasses (i.e., glasses based on the elements S, Se, and Te) are given crystallographic axis with the fiber axis was more constant over transparent in the IR, possess low phonon energies, are chemically the single crystalline region in the case of the square-core fiber while durable and can be drawn into fiber. Both conventional solid core/clad more significant variations were observed in the round-core case. This and microstructured fibers have been developed. Chalcogenide glass work begins to elucidate some of the microstructural features, not pres- compositions have been developed which allow rare earth doping to en- ent in conventional glass optical fibers, that could be important for fu- able rare earth doped fiber sources and potentially lasers in the IR. Also, ture low-loss single crystalline semiconductor optical fibers. highly nonlinear compositions have also been developed with nonlin- earities ~1000x silica which enables nonlinear wavelength conversion 3:20 PM from the near IR to the mid and long wave IR. In this paper, we will re- (GOMD-SII-029-2012) Tellurite and Chalcogenide Microstructured view our work in rare earth doped chalcogenide fiber for IR sources and Optical Fibers for Broadband Sources in the Infrared (Invited) lasers and highly nonlinear chalcogenide fiber and photonic crystal fiber F. Smektala*, Universite de Bourgogne, France for wavelength conversion in the IR. Fibered broadband sources working in the infrared above 2 μm and 2:00 PM based on chalcogenide or heavy oxide glasses remain actually a challeng- (GOMD-SII-026-2012) One-step Multi-material Optical Fiber ing issue. Microstructured optical fibers (MOFs) are a suitable photonic Preform Extrusion for Robust Chalcogenide Glass Optical Fibers and structure to reach that target since they allow both the management of Tapers the non linearity and of the chromatic dispersion. The latter is a key a G. Tao*, S. Shabahang, E. Banaei, J. J. Kaufman, A. F. Abouraddy, University of parameter to allow a pumping near the zero dispersion wavelength. Central Florida, USA Thus it is possible to reach a supercontinuum generation extending far in the infrared and covering the entire transparent window of the The development of robust and low-loss mid-infrared fibers is crucial MOFs, through modulational instability, soliton formation and their for harnessing the capabilities of new mid-infrared laser sources. self Raman shift. In the past years, great improvements have been Chalcogenide glasses are an ideal candidate for this application. Their reached. We present here our recent achievements in the elaboration of utility has been hampered heretofore in part by unfavorable mechanical low losses chalcogenide and heavy oxides MOFs, the management of characteristics. We demonstrate a novel approach to the fabrication of their dispersion, their linear and non linear characterization in the in- fiber preforms containing chalcogenide glasses and thermoplastic poly- frared as well as the results obtained in the infrared supercontinuum mers: one-step multi-material preform extrusion. The preform consists generation. of a glass core, glass cladding, and an outer polymer cladding. The poly- mer provides mechanical support but does not participate in the optical 4:00 PM functionality. Using this approach we extrude several distinct preform (GOMD-SII-030-2012) Multi-material Fibers: Current Progress and structures, draw them into fibers, and characterize their optical and me- Future Prospects (Invited) chanical performance. Furthermore, the polymer cladding allows us to A. F. Abouraddy*, University of Central Florida, CREOL, USA produce high-index-contrast fiber tapers with sub-micron core diame- ters that are suitable for a variety of nonlinear applications. Incorporating new materials combinations in a single optical fiber paves the way to novel optical and optoelectronic functionalities delivered on 2:20 PM optical fiber length scales. Experimental progress towards this goal has (GOMD-SII-027-2012) Reactive molten core fabrication of silicon made us aware of the challenges and opportunities offered by explo- optical fiber (Invited) rations of new multi-material fiber systems that combine chalcogenide J. Ballato*, S. Morris, T. Hawkins, P. Foy, Clemson University, USA; R. Rice, glasses and thermoplastic polymers. I will review recent progress by my Dreamcatchers Consulting, USA; L. Zhu, R. Stolen, Clemson University, USA group in this field. Applications of these fibers range from robust chalcogenide glass fibers for mid-infrared beam delivery, the generation Silicon optical fibers fabricated using the molten core method possess of new mid-infrared coherent sources of radiation, to all-solid photonic high concentrations of oxygen in the core due to dissolution of the crystal fibers. I will also describe our research on the limits imposed by cladding glass by the core melt. The presence of oxygen in the core can fluid instabilities on the miniaturization of features in fibers combining influence scattering, hence propagation losses, as well as limit the per- heterogeneous materials, leading to novel approaches to the fabrication formance of the fiber. Accordingly, it is necessary to achieve oxygen-free of nanowires and structured micro-particles and nanoparticles via ther- silicon optical fibers prior to further optimization. In this work, silicon mal fiber drawing. Finally, I will lay out a roadmap for future develop- carbide (SiC) is added to the silicon (Si) core to provide an in situ reac- ments in this area. tive getter of oxygen during the draw process. Scanning electron mi- croscopy (SEM), energy dispersive x-ray spectroscopy (EDX), and pow-

2012 Glass & Optical Materials Division Annual Meeting 49 Abstracts

4:40 PM Symposium IV: Festschrift to the Glass (GOMD-SII-031-2012) Annealing of Silicon Optical Fibers J. Ballato*, N. Gupta, C. McMillen, R. Singh, R. Podila, A. Rao, T. Hawkins, P. Research Career of Prof. Delbert E. Day Foy, S. Morris, Clemson University, USA; R. Rice, Dreamcatchers Consulting, USA; L. Zhu, Clemson University, USA Session 1: The Mixed Alkali Effect and Ion The recent realization of silicon core optical fibers has the potential for Conducting Glasses II novel low insertion loss rack-to-rack optical interconnects and a num- Room: Grand Suites II & III ber of other uses in sensing and biomedical applications. To the best of Session Chair: Philipp Maass, University of Osnabrueck our knowledge, incoherent light source based rapid photothermal pro- cessing (RPP) was used for the first time to anneal glass-clad silicon core 1:20 PM optical fibers. X-ray diffraction examination of the silicon core showed a (GOMD-SIV-005-2012) A role of the heterogeneity of dynamics in considerable enhancement in the length and amount of single crys- the mixed alkali effect (Invited) tallinity post-annealing. Further, shifts in the Raman frequency of the J. Habasaki*, Tokyo Institute of Technology, Japan; K. L. Ngai, University of Pisa, silicon in the optical fiber core that were present in the as-drawn fibers Italy were removed following the RPP treatment. Such results indicate that the RPP treatment increases the local crystallinity and therefore assists We use molecular dynamics simulation to study the role of the dynamic in the reduction of the local stresses in the core leading to more homog- heterogeneity in the MAE in ionically conducting glasses. In the mixed enous fibers and permits a path forward to in-situ enhancement of the alkali lithium–potassium silicate glasses and related systems, a distinct- structure and properties of these new crystalline core optical fibers. part of the van Hove functions reveals that jumps from one kind of site to another are suppressed. Although, consensus for the existence of 5:00 PM preferential jump paths for each kind of mobile ions seems to have been (GOMD-SII-032-2012) An acentric crystalline oxide core optical reached amongst researchers, a role of the dynamic heterogeneity re- fiber mains controversial in explaining the MAE. Dynamical heterogeneity J. Ballato*, C. McMillen, T. Hawkins, P. Foy, L. Zhu, Clemson University, USA; R. and ‘‘cooperativity blockage’’ originating from ion–ion interaction and Rice, Dreamcatchers Consulting, USA; O. Stafsudd, UCLA, USA correlation are fundamental for the observed ion dynamics and the MAE. Suppression of long range motion with increased back-correlated Described here are a new class of glass-clad optical fibers that comprise motions is shown to be a cause of the large decrease of the diffusivity es- an acentric crystalline oxide core fabricated using conventional fiber pecially in dilute foreign alkali regions. Related changes in the fractal di- draw processes. More specifically, the fiber possessed a borosilicate glass mension of paths and motions are shown by the multifractal analysis. cladding with a core of crystalline bismuth germinate (Bi2GeO5) and crystalline bismuth oxide (δ-Bi2O3/BiO2-x), which was derived using a 2:00 PM molten core process with Bi12GeO20 (BGO) serving as the starting core (GOMD-SIV-007-2012) Ion transport in copper oxide containing material. While representing an initial proof-of-concept, this work lithium phosphate glasses shows that commercially-relevant draw processing can be employed to C. Mugoni*, G. Broglia, M. Montorsi, C. Siligardi, University of Modena and realize optical fibers that possess acentric, hence optically nonlinear, Reggio Emilia, Italy; H. Jain, Lehigh University, USA oxide crystals. Ion conducting phosphate glasses are interesting due to their several un- 5:20 PM usual properties that make them suitable candidate materials for solid (GOMD-SII-033-2012) Surface Enhanced Raman Scattering of silica electrolytes, glass-ceramics, amorphous semiconductors and optoelec- matrixes containing noble metal nanoparticles for the improvement tronic devices. The aim of the present work is to investigate the effect of of Raman Amplification in telecommunication optical fibers copper oxide (as Cu2O) addition on the electrical properties of lithium B. Champagnon*, E. Nardou, D. Vouagner, A. Jurdyc, A. Berthelot, O. Ben phosphate glasses. Different copper-lithium phosphate glasses were pre- Amara, A. Pillonnet, CNRS-University Lyon1, France; L. Bertry, O. Durupthy, C. pared with varying Cu2O/Li2O ratio, while keeping the P2O5 content Chanéac, Uninversity Pierre et Marie Curie, France; A. Pastouret, E. Burov, constant at 50 mol%. Their electrical properties were measured through Draka Comtek France, France AC impedance methods as a function of frequency and temperature. The data reveal the mainly ionic nature of electrical conductivity. Struc- Fiber-optic telecommunication systems are widely used for high-speed tural properties were explored using both experimental and computa- information transfer. However, the signal is attenuated during its prop- tional (Molecular Dynamic simulation) methods. The results are ana- agation in the fiber due to optical losses in silica and needs amplifica- lyzed to correlate the structure with the ionic transport mechanism in tion. Raman Amplification based on stimulated Raman scattering is this glass series. rapidly growing for very high speed optical communication and it is an effective technique for signal amplification. The matrix signal exaltation 2:20 PM can be obtained from Surface Enhanced Raman Scattering (SERS) effect (GOMD-SIV-008-2012) In-situ study of bias-induced particle growth using the Surface Plasmon Resonance (SPR) of noble metal nanoparti- on a lithium-ion conductive glass ceramic (LIC-GC) (Invited) cles (Me-NP). In this work, the SERS response of several model samples J. Krümpelmann*, C. Yada, Uni Marburg, Germany; F. Rosciano, Toyota Motor composed of Au or Ag embedded into a silica matrix is studied by Europe, Belgium; B. Roling, Uni Marburg, Germany micro-Raman scattering measurements at varying wavelengths accord- ing to the SPR band positions of NP-Me. Concentration and size -de- In order to study ion transport and electrochemical behavior of the pendence of Me-NP on the SERS effect is discussed as well as the SERS LIC-GC on a nanoscopic level, we carried out nano-electrochemical range in silica. measurements using a conductive AFM tip as working electrode. Due to the huge area difference between working and counter electrode, a third reference electrode is not needed. We present nanoscopic cyclic voltam- mograms and chronoamperometric measurements probing the growth of metallic lithium particles under the biased AFM tip when a critical negative bias voltage is exceeded. The particle growth is analyzed by si- multaneously monitoring current and particle height. Due to its rela- tively high room-temperature ionic conductivity and high stability against water and aqueous lithium salt solutions, the Ohara lithium-ion conductive glass ceramic is of interest as solid electrolyte for lithium-air batteries.

50 2012 Glass & Optical Materials Division Annual Meeting Abstracts

3:20 PM Session 4: Glasses for Bio-Medical Applications (GOMD-SIV-009-2012) Critical Ordering Temperature of Mixed Room: Salon C Alkali Glasses (Invited) Session Chairs: Julian Jones, Imperial College; Matthew Hall, Alfred M. Tomozawa*, P. J. Lezzi, M. Yoshiyagawa, RPI, USA University It was observed previously that the enthalpy of mixing was negative for various mixed alkali silicate glasses. As a result it was postulated that a 1:20 PM critical temperature may exist at which the dielectric relaxation strength (GOMD-SIV-032-2012) Composition Structure Property approaches infinity. The dielectric properties of a series of single and Relationships in Bioactive Glasses (Invited) mixed alkali glasses in a lithium-sodium di-silicate system were investi- R. G. Hill*, Queen Mary University of London, United Kingdom gated in search of this phenomenon. It was observed that the mixed al- Solid state NMR provides a unique tool for studying composition struc- kali glasses definitively show such a critical temperature. This is inter- ture property relationships in bioactive glasses. The structural role of preted as evidence of a critical short-range ordering effect resulting in phosphorus, magnesium oxide and fluoride will be outlined. Phospho- the large dielectric relaxation strength for mixed alkali glasses, and as rus exists as orthophosphate in bioactive glasses and there are no Si-O-P the likely cause of the mixed alkali conductivity effect. bonds. Adding phosphate without adding additional modifying oxides 4:00 PM increases the connectivity of the silicate part of the network. Magne- sium oxide partially enters the silicate network and partially acts as a (GOMD-SIV-010-2012) New Studies of Ion Conduction in modifying oxide and when substituted for CaO increases the connectiv- Phosphate-Based Mixed Glass Former Glasses (Invited) ity. Fluoride is complexed by calcium ions in bioactive glasses. Adding S. W. Martin*, Iowa State University, USA; R. B. Christensesn, Iowa State CaF2 results in no change in connectivity. In contrast substituting CaF2 University, USA; G. Olson, Iowa State University, USA; P. Maass, University of for CaO increases the connectivity and ultimately reduces bioactivity. It Osnabruick, Germany; M. Schuch, University of Osnabruick, Germany will be demonstrated how understanding glass structure, the mecha- Due to their strong glass forming character over wide compositional, nism of dissolution and the formation of “apatite like” phases can be phosphate glasses have been extensively studied as hosts for mobile ions. used to design compositions for coatings, scaffolds, toothpastes and Most of these studies have been conducted on glassy systems where chewing gum. P2O5 is the only glass former and the studies of ion conductivity and 2:00 PM the impact the modifying oxide has upon the structure of the phosphate (or thiophosphate) glass have been conducted as a function of the alkali (GOMD-SIV-033-2012) Treatment of Chronic Ulcers with Bioactive concentration. In our new studies. In these studies we have found that Borate Glass Nanofibers P2O5 additions to B2O3 increase the Na+ ion conductivity, while SiO2 S. B. Jung*, T. Day, MO-SCI Corporation, USA; W. V. Stoecker, P. Taylor, Phelps additions decrease the Na+ ion conductivity. In this talk, we will survey County Regional Medical Center, USA; D. E. Day, Missouri University of Science recent studies of phosphorous-based mixed glass former glasses and and Technology, USA contrast the positive mixing behavior of Na-P-B-O systems with the Bioactive glass has been used primarily for hard tissue regeneration in negative mixing behavior of the Na-Si-B-O system. orthopedics and dental applications. Recently, the use of bioactive glass 4:40 PM to stimulate soft tissue regeneration has become a larger area of study as certain bioactive glasses have shown promising results for promoting (GOMD-SIV-011-2012) Internal friction of calcium alumino-silicate angiogenesis (blood vessel formation). In this study, angiogenic bioac- glasses substituted with Ba, Sr and Mg tive glass nanofibers that mimic the microstructure of a fibrin clot were A. K. Swarnakar*, Leuven University, Belgium; A. Stamboulis, University of used for healing chronic wounds. Over forty five patients, each with a Birmingham, United Kingdom; O. Van der Biest, Leuven University, Belgium non-healing ulcer, were treated with a pad composed of bioactive glass Fluorine-calcium-alumino-silicate glasses are widely used in dentistry nanofibers (BGNF) one to two times per week until the wound resolved. as a component in dental cement. The structural changes due to the Thus far twenty seven of the ulcers have been resolved with the treat- substitution of Ca by Ba, Sr and Mg in a glass composition of 4.5SiO2- ment of the BGNF, seven patients have dropped from the study for per- 3Al2O3-1.5P2O5-3CaO-2CaF2 has been studied with the Impulse Exci- sonal reasons, and the other eleven patients are in different stages of tation Technique (IET). The E-Modulus has been measured as a func- healing. As the ulcers heal, it was noted that the new tissue has minimal tion of temperature and simultaneously the internal friction behaviour scarring and the original defect area is difficult to detect visually. of the glass samples has been analyzed. The interpretation of internal 2:20 PM friction behaviour is further corroborated by carrying out structural analysis using MAS-NMR.The internal friction peaks observed below (GOMD-SIV-034-2012) Glass-ceramics with high strength for dental the glass transition were associated with the diffusion of non-bridging application oxygen and cations in the network. An increase in internal friction W. Hoeland*, C. Ritzberger, M. Schweiger, V. M. Rheinberger, Ivoclar Vivadent above the glass transition temperatures is attributed to the onset of crys- AG, Liechtenstein tallisation which was documented by high temperature XRD. It is a great challenge to develop and to apply metal-free biomaterials for 5:00 PM dental restoration. The authors report on the formation of the lithium disilicate glass-ceramics in the SiO2-Li2O-K2O-Al2O3-ZrO2 system . (GOMD-SIV-012-2012) Dynamic Light Scattering in Mixed Alkali The solid state reactions, nucleation and crystallization processes are Metaphosphate Glassforming Liquids demonstrated by SEM and XRD studies. The fracture propagation in D. L. Sidebottom*, J. Changstrom, Creighton University, USA this glass-ceramic showed that the high fracture toughness, and high The inherent viscoelastic relaxation of both single alkali and mixed al- flexural strength was caused by crack deviation in the vicinity of the dis- kali metaphosphate glasses were studied at temperatures well above the ilicate crystals. The glass-ceramic is applied as a moldable or machinable glass transition using photon correlation spectroscopy. Values for the product. The glass-ceramic framework, e.g. of a dental bridge, is ve- glass transition temperature, the fragility index, and the heterogeneity neered with fluoroapatite glass-ceramic. Machining is applied using an parameter (a.k.a., the Kohlrausch exponent) were determined and seen intermediate product(lithium metasilicate glass-ceramic). After ma- to display a mixed alkali effect in that each displays a deviation from lin- chining it undergoes heat treatment at 850 °C. During thermal treat- ear behavior with alkali mixing ratio. Contrary to expectations, the ment, it is transformed into a lithium disilicate glass-ceramic. Kohlraush exponent however decreases with decreasing fragility. Here, we attempt to interpret these findings within the framework of current theoretical models for the mixed alkali effect.

2012 Glass & Optical Materials Division Annual Meeting 51 Abstracts

2:40 PM 4:20 PM (GOMD-SIV-035-2012) Phosphate Based Glass Fibre Reinforced (GOMD-SIV-038-2012) Alkali-free bioactive glasses for bone tissue Composites for Bone Repair Applications engineering I. Ahmed*, A. J. Parsons, C. A. Scotchford, D. Grant, C. D. Rudd, University of A. Goel*, Pacific Northwest National Laboratory, USA; J. M. Ferreira, University Nottingham, United Kingdom of Aveiro, Portugal The potential of bioresorbable composites to replace traditional metal- Alkali-free bioactive glasses doped with Sr and Zn have been designed lic devices has many advantages including improved biocompatibility along the diopside –fluorapatite – tricalcium phosphate join. The in and reduced stress shielding. The main advantage of having a material vitro bioactivity analysis of glasses has been made by immersion of glass that degrades is so that an implant would not necessitate a second surgi- powders in simulated body fluid (SBF) while chemical degradation has cal event for removal. In addition, biodegradation may offer other ad- been studied in Tris–HCl in accordance with ISO-10993-14. Some of vantages. For example, a fractured bone fixated with a rigid metallic im- the investigated glasses exhibit hydroxyapatite formation on their sur- plant may refracture upon removal of the implant. This is because the face within 1–12 h of their immersion in SBF solution. The sintering bone does not carry sufficient load during the healing process. However, and crystallization kinetics of glasses has been studied using differential an implant prepared from biodegradable materials could be engineered thermal analysis, hot-stage microscopy, X-ray diffraction and scanning to degrade at a rate that would slowly transfer load to the healing bone. electron microscopy. The alkaline phosphatase activity and osteogenic In the present study, fully resorbable composite bone repair plates com- differentiation for glasses have been studied in vitro on sintered glass prising a PLA matrix reinforced with phosphate-based glass fibres were powder compacts using rat bone marrow mesenchymal stem cells. The investigated. Composites with increasing fibre volume fraction and al- as-designed glasses are ideal candidates for their potential applications ternate fibre geometries (random and unidirectional) were evaluated. in bone tissue engineering in the form of bioactive glasses as well as glass/glass–ceramic scaffolds. 3:20 PM (GOMD-SIV-036-2012) Effect of the Glass Composition on In Vivo 4:40 PM Behavior of Bioactive Glasses (Invited) (GOMD-SIV-039-2012) Effect of titanium oxide in the development L. Hupa*, Åbo Akademi University, Finland of an organically modified silicate based dopamine sensor P. C. Pandey, A. Prakash*, D. S. Chauhan, Institute of Technology, Banaras This presentation is a review of the work at Åbo Akademi on the influ- Hindu University, India ence of glass composition on the properties of bioactive glasses. The main focus is on the parameters governing the bioactivity, such as the Here we present a novel protocol for the synthesis of organically modi- growth of the apatite layer on the glasses in vitro. Also the results from fied silicate (ormosil) films with improved stability. The thin films of or- in vivo testing with fifty compositions will be discussed. The in vitro mosil were synthesized using alkoxysilane precursors along with a sol of and in vivo results have been modeled to present bioactivity as func- Titanium oxide film. The ormosil films were cast over glassy carbon tions of glass oxide composition. Recently, the tissue bonding properties electrode (GCE) followed by chemical modification using potassium of selected compositions have been correlated with the ion dissolution ferricyanide as electron transfer mediator. The films were utilized for kinetics in vitro. Selected glass compositions have been studied in vivo the determination of dopamine in presence of an excess concentration as solid conical implants, porous implants or as reinforcing fibers in of ascorbic acid. To impart selectivity to the modified electrodes, Nafion biodegradable polymers. Our observations of various glass composi- was incorporated in the same. Results show that the presence of AuNp tions and product forms emphasize that in the tailoring of glasses for in the ormosil matrix dramatically improves the electrochemical behav- novel tissue engineering applications not only the glass composition but ior of potassium ferricyanide. The electrochemical performance of the also the product form must be taken into account to achieve the desired modified electrodes indicated high sensitivity, selectivity and an im- biological response. proved lower limit of detection for sensing of dopamine. 4:00 PM (GOMD-SIV-037-2012) In vitro and in vivo response of tailored Wednesday, May 23, 2012 amorphous multi porous (TAMP) bioscaffolds M. Saad, M. Sabry, M. Marei, Alexandria University, Egypt; S. Wang, T. Kowal, J. Marzillier, M. Falk, H. Jain*, Lehigh University, USA Symposium I: Glass Science We have developed several methods for fabricating tailored amorphous Session 2: Non-Oxide Glasses I multi porous (TAMP) bioscaffolds making use of multi-scale phase sep- aration in the systems based on 45S Room: Salons E, F, & G (24.4Na2O–26.9CaO–2.6P2O5–46.1SiO2) or 30CaO-70SiO2 bioactive Session Chairs: Andriy Kovalskyy, Austin Peay State University; David glass compositions. It has been possible to control the nano and macro Musgraves, Clemson University scale porosity independently, thus permitting the matching of degrada- 8:00 AM tion rate with tissue growth rate. In this paper we present our recent re- sults demonstrating the in vitro bioactive response of such TAMP struc- (GOMD-SI-049-2012) Ab initio simulations of chalcogenides: size tures using adhesion, proliferation and upregulation of bone formation effects, structure, rigidity and dynamics (Invited) markers of MC3T3 pre-osteoblast cells. For in vivo response, the M. Micoulaut*, UPMC, France bioscaffold samples were implanted under the skin of New Zealand rab- Due to their covalent nature, a continuous effort has been spent on the bits. Subsequent observations revealed normal cascade of wound heal- ab initio molecular simulation of chalcogenides in the Ge-Se or As-Se ing and closure, hair growth, rapid degradation, minimal fibrous tissue families. In fact, homopolar defects which are typical of such systems, formation and highly angiogenic and vascular development, indicating and electronic transfer can not been obtained/described with classical osteoinduction by the TAMP bioscaffolds. Molecular Dynamics using force fields. In this talk, we describe the most recent efforts to achieve at the highest level of accuracy the description of structural and dynamic properties of liquid and glassy Ge-Se and As- Se with changing composition. We show that size effects do not alter such properties and describe in detail possible signatures for the onset of rigidity when Ge or As content are steadily increased.

52 2012 Glass & Optical Materials Division Annual Meeting Abstracts

8:40 AM 10:20 AM (GOMD-SI-036-2012) Observation of polyamorphism in GeTe- (GOMD-SI-041-2012) SiOC glass-diamond composites Sb2Te3 Phase Change Materials T. Rouxel*, P. Sellappan, University Rennes 1, France; L. Toma, G. Miehe, TU S. Sen*, University of California, Davis, USA; B. Kalkan, Advanced Light Source, Darmstadt, Germany; F. Célarié, University Rennes 1, France; R. Riedel, TU Lawrence Berkeley Laboratory, USA; S. Clark, University of California, Berkeley, Darmstadt, Germany USA; B. Aitken, Corning Incorporated, USA New types of bulk SiOC glass matrix composites reinforced with dia- The thermodynamic nature of phase stabilities and transformations are mond particles were successfully fabricated. Diamond particles were in- investigated in crystalline and amorphous Ge1Sb2Te4 (GST124) phase troduced into the SiOC matrix by the polymer-derived ceramics (PDC) change materials as a function of pressure and temperature using high- route using polysiloxane and two different sized diamond particles, 2 resolution synchrotron x-ray diffraction in a diamond anvil cell. When and 30 μm as starting precursors. Dense bulk specimens were prepared taken together, the phase equilibria relations are consistent with the by warm pressing at 150-160 °C followed by pyrolization at 1100 °C for presence of polyamorphism in this system with the as-deposited amor- 2 h. Elastic properties were determined by means of ultrasonic echogra- phous GST phase being the low entropy LDA phase and the laser melt- phy and Young’s modulus was found to increase from 96 to 154 GPa quenched and high-pressure amorphized GST being the high entropy when diamond content increased from 0 to 25 vol%. Reinforcement re- HDA phase. At pressures above 30 GPa the HDA phase transforms into sults in significant improvement in hardness. TEM investigations reveal a bcc phase that remains metastable upon decompression but eventually that SiOC glass matrix and 2 μm diamond particles have excellent transforms to the LDA phase with large hysteresis at pressures below 10 bonding. The present study demonstrates the possibility of fabricating GPa indicating the presence of a novel reversible amorphous to crys- bulk SiOC glass-diamond composites via the polymer-processing route, talline phase transition. The fundamental implications of polyamor- resulting in composites with promising mechanical properties. phism on optical memory device performance will be discussed. 10:40 AM 9:00 AM (GOMD-SI-042-2012) Study of Europium Valence in ZBLAN Image (GOMD-SI-037-2012) Meeting experimental challenges to physics of Plates (Invited) network glasses- assessing the role of sample homogeneity (Invited) J. Johnson*, C. Johnson, UTSI, USA; C. Passlick, Fraunhofer Center for Silicon P. Boolchand*, S. Bhosle, K. Gunasekera, P. Chen, Univ of Cincinnati, USA; M. Photovoltaics, Germany; S. Gray, UTSI, USA; R. Weber, Materials Development Micoulaut, University of Paris 6, France; C. Massobrio, Institut de Physique et Inc., USA; S. Schweizer, Fraunhofer Center for Silicon Photovoltaics, Germany de Chimie des Materiaux de Strasbourg,, France ZBLAN glass-ceramic materials are being developed as x-ray imaging To establish the intrinsic behavior of physical properties with chemical plates. The materials are doped with europium and chlorine and can be composition in network glasses, homogeneous and dry samples are a heat-treated in such a way that they form a novel nanocomposite mate- prerequisite. We show that the enthalpy of relaxation at Tg in binary rial containing (orthorhombic phase) barium chloride nanocrystals, GexSe100−x glasses is particularly sensitive to sample heterogeneity; it is with the ability to convert x-rays into stable electron-hole pairs. The square-well like [1] with sharp edges at the rigidity (xc(1) = 19.5%) and ZBLAN glass only acts as an imaging plate upon annealing. As the an- stress ( xc(2)= 26.0%) transitions in homogeneous samples (Δx =0), but nealing temperature and annealing time are increased, so a higher de- Δ Δ becomes trapezoidal ( x =1.5%), then triangular ( x =3%) to eventu- gree of nucleation of BaCl2 crystallites inside the glass matrix is ob- ally disappear as glasses become steadily heterogeneous. The hetero- served. As a result, more crystallites are available to incorporate Eu2+ geneity of batch compositions can be established from Raman profiling and hence increase the fluorescence intensity. However, Eu2+ has a ten- experiments [1] yielding directly the Ge-stoichiometry variation (Δx). dency to oxidize to Eu3+ and recent studies have focused on this redox We comment on the slow kinetics of homogenization of dry chalco- reaction. Techniques used to study this phenomenon include Möss- genide melts and the underlying physical processes. [1]. S. Bhosle, K.Gu- bauer and x-ray absorption near-edge spectroscopy. The complex nasekara, P.Chen, P.Boolchand, M.Micoulaut and C. Massobrio, Sol. St. chemistry and the ingredients and techniques necessary to synthesize a Commun. 151, 1851 (2011). functional glass plate will be presented. 9:40 AM 11:20 AM (GOMD-SI-039-2012) Glass formation and molecular structure in (GOMD-SI-043-2012) Nanostructure of Silicon Carbonitride and the SixGexTe100-2x ternary Silicon Boron Carbonitride Polymer-Derived Ceramics (PDCs) P. Boolchand, K. Gunasekera*, Univ of Cincinnati, USA; S. Mamedov, Horiba using Solid State Nuclear Magnetic Resonance (SSNMR) Jobin Yvon Inc, USA S. Widgeon*, University of California, Davis, USA; Y. Gao, G. Mera, Technische Universität Darmstadt, Germany; E. Stoyanov, S. Sen, A. Navrotsky, University of Alloys of group IV (Si, Ge) and group V (Sb) elements with Te are of in- California, Davis, USA; R. Riedel, Technische Universität Darmstadt, Germany terest as phase change materials. Glass formation in the titled ternary is realized in the 8% < x <16% range by melt-quenching. Tg(x) increase SiCN and SiBCN PDCs have excellent thermal, chemical and mechani- linearly in the 8% < x < 12% range, and then a decrease thereafter ( x > cal properties to temperatures up to 1500 oC and have potential for 12%). The enthalpy of relaxation at Tg shows a minimum centered near many applications. The properties can be adjusted for each application 9%, a maximum near 12% and then a slow decrease at higher x. Group by adjusting the fraction of C and adding species such as B. The nanos- IV additives cross-link Te-chains, and increase network connectivity at tructure of these PDCs is not fully understood and must be known to low x increasing Tg. But at x > 12%, the reduction in Tg suggests glasses exploit these promising properties. We will report the results of a struc- segregate. Raman scattering, excited using low power density of 785 nm tural study of SiCN and SiBCN PDCs using 29Si, 13C and 11B SSNMR. radiation, shows evidence of a broad mode near 160 cm−1 (characteris- We will show that the nanostructure contains two separate amorphous − tic of a-Te chains) and a narrower one near 127cm 1 (group IV cross- domains of Si3N4 and C. The C domains are an amorphous graphitic linking units). The scattering strength of the 127 cm-1 mode increases network and play a major role in controlling the properties. In the at the expense of the 160 cm-1 mode as x increases. The nature of struc- SiBCN PDCs, the nanostructure remains similar but BN sheets are ture evolution with glass composition will be commented upon. formed that are responsible for impeding crystallization at high temper- atures. The implications of these findings in understanding the thermo- dynamic stability of these PDCs will be discussed.

2012 Glass & Optical Materials Division Annual Meeting 53 Abstracts

11:40 AM ramics and glasses, because it results in time dependence of their physi- (GOMD-SI-044-2012) Silicon Oxycarbide Glass as a Low Dielectric cal properties. Chalcogenide glasses (ChG) can be considered as the material model materials for observing general trends of this phenomenon and Y. Kim*, Y. Lee, S. Kim, W. Kwon, Korea Institute of Ceramic Engineering and its microstructural origins. PhA can be detected most conveniently with Technology, Republic of Korea differential scanning calorimetry (DSC) through appearance of strong endothermic peak superimposed on the endothermic step of the glass- Silicon oxycarbide glasses as a low dielectric material has been great at- to-supercooled liquid transition signal. DSC results show that chalco- tention in the semiconductor industry to develop high performance in- gen-rich glasses stored far below the glass transition temperature or terlayer dielectrics with low k for Cu interconnect technology. They have subjected to different external influences (γ-radiation, light exposure) the potential range of properties through a change in carbon-to-oxygen lose their excess of configurational entropy, enthalpy or free volume ratios. In our study, the dielectric properties of SiOC low dielectric thin (gained at the stage of synthesis) to reach a more favourable thermody- film derived from polyphenylcarbosilane were investigated as a poten- namic state. We will discuss various aspects of PhA and describe its mi- tial interlayer dielectrics for Cu interconnect technology. SiOC low di- croscopic mechanism in terms of Johari-Goldstein relaxation processes. electric thin film was fabricated onto n-type silicon wafer by spin coat- ing using 20wt % polyphenylcarbosilane (PPCS) in cyclohexane. Curing 10:20 AM of the film was performed in the air at 300°C for 1h. The thickness of the (GOMD-SI-073-2012) Analysis of small volume changes at film is ranged from 0.5μm to 1μm. The dielectric constant was deter- temperatures below the glass transition region (Invited) mined from the capacitance data obtained from metal/polyphenylcar- S. M. Rekhson*, Cleveland State University, retired, USA bosilane/conductive Si/ MIS capacitors and the thin film derived from polyphenylcarbosilane show a dielectric constant as low as 1.3 without In the 1986 J. of Non-Crystalline Solids article titled “Memory Effects in added porosity. Glass Transition” I claimed the existence of a small peak on the short- time tail of structural relaxation times. Its location and size were only tentatively established because the data obtained at the time within the Session 4: Relaxation I standard glass transition region were poorly suited for this task. During Room: Salon A the past decade some very accurate measurements of glass substrate Session Chair: Ulrich Fotheringham, SCHOTT AG movement appeared in the literature motivated by the TFT LCD tech- nology. I reduced some of these data to resolve more accurately the 8:00 AM short-time peak of structural relaxation times and used this new spec- (GOMD-SI-070-2012) Relaxation, Polyamorphism and Perfect trum to calculate the evolution of soda-lime glass volume within the Glasses (Invited) temperature range of 150 to 350oC. A number of effects involving both N. Greaves*, University of Cambridge, United Kingdom; Z. Zhou, Shanghai increase and decrease of glass volume were established and explained in University, China terms of behavior of partial fictive temperatures. Polyamorphism is a supercooled phenomenon resulting in glassy phases 11:00 AM having the same composition but differing in entropy and density. These have been detected with X-ray and neutron scattering, not least in (GOMD-SI-074-2012) Glass Transition Studies of Mechanically the critical fluctuations that accompany coexistence. For aluminosilicate Milled Amorphous Materials (Invited) glasses, in addition to the high density glasses derived from melts that S. W. Martin*, Iowa State University, USA; M. Marple, Iowa State University, are typically fragile, low density glasses – sometimes called “perfect USA; C. Bischoff, Iowa State University, USA glasses” can be formed by amporphising nanoporous zeolites. Such Studies of relaxation processes in the glass transition region are nor- polyamorphic phases have different nanostructure and also different mally conducted on liquids that have been supercooled to the glassy fragilities as the glass transition is approached. In particular the low state after having been equilibrated both chemically and thermally at el- density liquid phase is far stronger than its high density counterpart, evated temperatures well above the melting and/or liquidus tempera- and the corresponding perfect glass has nanostructural elements in ture of the composition. In this new study, we have observed that a glass common with its zeolite precursor, and distinct from the continuous transition temperature can be observed for materials have been random network structure of a melt quenched glass. mechano-chemically milled at room temperature and have never been exposed to the liquid state. The first up scan in the DSC for example 8:40 AM shows a very large exothermic relaxation associated with a very high fic- (GOMD-SI-071-2012) On the fragility and relaxation behavior of tive state for the supercooled liquid and a subsequent Tg signature. After bulk metallic glass forming liquids (Invited) cooling back down to well below the Tg of the glass, the second and sub- R. Busch*, Chair for Metallic Materials, Germany sequent rescans show normal Tg behavior. In this talk, we will review This presentation gives an overview of the kinetic and thermodynamic the Tg behavior of such mechano-chemically prepared amorphous ma- properties of bulk metallic glass forming liquids. Experimental results terials and report the first ever study of the relaxation characteristics of on the relaxation of enthalpy, viscosity and volume are presented based these liquids. on calorimetric, rheological and volumetric methods. They present a 11:40 AM consistent picture of structural relaxation in these metallic liquids and (GOMD-SI-075-2012) Relaxation in NaAlSi O across the glass glasses. The data are described using the Cohen-Turnbull and Cohen- 3 8 Grest model for free volume. Additionally, an interpretation of the free transition interval at high pressure volume based on the Adam-Gibbs equilibrium viscosity model is dis- S. J. Gaudio*, C. E. Lesher, S. Sen, University of California, Davis, USA cussed [1]. Good bulk metallic glass forming liquids are rather strong Density and structural relaxation are explored in NaAlSi3O8 glass liquids and a general trend is found that the strength increases with the quenched from pressures up to 7.4 GPa and temperatures above and number of components in the liquid. [1] Z. Evenson, and R. Busch, Acta 27 below Tg using Al MAS NMR spectroscopy and density measure- Materialia 59, 4404 (2011). ments. Some configurational and topological structural changes are ir- reversible on decompression and reflect both fictive pressure (P ) and 9:20 AM f fictive temperature (Tf) conditions. The average Al coordination num- (GOMD-SI-072-2012) Physical aging of chalcogenide glass (Invited) ber and density increase at constant pressure with increasing annealing R. Golovchak, Lehigh University, USA; A. Kozdras, Opole University of temperature. Most of the increase in average Al coordination and den- Technology, Poland; H. Jain*, Lehigh University, USA sity occurs below the Tg associated with Na mobility. Samples recovered Structural relaxation during physical aging (PhA) is an important con- from superliquidus-quench experiments have significantly lower den- cern for application of disordered solids, such as organic polymers, ce- sity and average Al coordination than Tg relaxed samples, which sug-

54 2012 Glass & Optical Materials Division Annual Meeting Abstracts

gests that these differences are not simply a reflection of Tf. Characteri- 9:20 AM zation of structure and density across the glass transition at high pres- (GOMD-SI-086-2012) Dissolution Kinetics of Borosilicate SON68 sure provides a probe of ionic mobility in the glassy state that is inacces- Glass Determined by Experiment: Effects of Al and Si sible by most common experimental methods. J. Icenhower*, C. Steefel, Lawrence Berkeley National Laboratory, USA Single-pass flow-through dissolution experiments were carried out at 90 Session 5: Glass Corrosion and Surface Science I degrees C and pH = 9 on SON68 glass to quantify its corrosion kinetics. Room: Salon B Both monoliths (1.5 cm x 1.0 cm x 4 mm coupons) and powders (149 - Session Chair: Nathan Mellott, Alfred University 75 micrometer diameter) were utilized. Experiments were conducted over a solution saturation interval from 0 added Si up to saturation with 8:00 AM respect to amorphous silica. In other experiments, small concentrations (GOMD-SI-083-2012) Glass-Water Interfacial Reactions: Role of of aqueous Al (up to 1 mmol)were added to ascertain the rate depend- Experimentation and Modeling in Predicting Long-term Weathering ence on aluminum. The experiments ran from 17 days to 3 months. Re- (Invited) sults showed that aqueous Si suppressed rates by more than a factor of E. Pierce*, Oak Ridge National Laboratory, USA 100X. In solutions with low concentrations of aqueous Si, Al suppressed Glass-water interfacial reactions play a critical role in the evolution of rates by a factor of 50X. At higher concentrations of aqueous Si, the ef- engineered systems (e.g., geologic repository). A mechanistic under- fects of aqueous Al were minor. These results show the importance of standing is required to accurately forecast contaminant release from aqueous Si on borosilicate glass dissolution and step towards the goal of corroding glass. The existing scientific challenge is to decipher the com- predicting long-term rates in the disposal environment. plex coupled reactions controlling the formation, evolution, and trans- 9:40 AM formation of silica-rich surface layers. Silica-rich surface layers, similar to inorganic coatings on natural minerals, can affect the microscopic (GOMD-SI-087-2012) New insight into the composition-dependent processes (e.g., ion diffusion, etc.) that impact elemental release rates long-term alteration rate of glass and contaminant migration. Accurately describing the impact of these S. Gin*, X. Beaudoux, C. Jegou, CEA, France layers on the long-term weathering of glass will require a molecular level Nine simple borosilicate glasses of nuclear interest and the complex understanding of the rates and mechanisms occurring at the glass-water SON68 glass have been leached at 90°C, in static mode and in initially interface. The presentation will focus on a broad range of experimental pure water, for nearly 10 years to allow accurate measurement of their and computational approaches being implemented to develop a predic- long-term dissolution rate. The simple glasses were designed to have the tive understanding of the long-term weathering of glass. same elemental molar ratios as SON68 nuclear glass. We show that the residual rate strongly depends on the glass composition, and is from 2 to 8:40 AM 5 orders of magnitude lower than the forward rate. Some synergic ef- (GOMD-SI-084-2012) First-Principles Study Of Barriers For fects have been evidenced, mainly between Al and Ca and between Zr Dissolution Reactions In Silicate Minerals And Glasses and Ca, leading to the lowest rates. These effects appear to be related to P. Zapol*, H. He, X. Tan, Argonne National Laboratory, USA the gel properties. Moreover, as expected, when crystalline phases pre- Atomistic-informed models have potential to reduce uncertainties in cipitate during glass leaching the residual rates are systematically higher. long-term predictions of dissolution behavior of glass waste forms in Finally we show that the 6-oxide glass selected for the international col- aqueous environments. For model development we have used well- laboration on glass corrosion is a good surrogate for SON68 glass. characterized crystalline aluminosilicates that have a known structure, 10:20 AM but possess key characteristics of waste form glass, such as compositions with multiple cations, pH dependence and formation of secondary (GOMD-SI-088-2012) Studies of Glass Corrosion Combining phases in dissolution. We have performed a Kinetic Monte Carlo study Analytical Spectroscopies and Computational Chemistry (Invited) based on first-principles calculations of surface site distribution and K. Mueller*, Pacific Northwest National Laboratory, USA; C. Pantano, Penn barriers for water reactions at neutral, protonated and deprotonated State University, USA sites. The dissolution rate far from equilibrium is compared to experi- Understanding of glass corrosion at the atomic or molecular sub-unit ments. We have also extended this approach to multi-component level typically requires a range of analytical capabilities aimed at identi- glasses. Using initial amorphous structures generated from classical mo- fying relevant structures and dynamics. This presentation will be tuto- lecular dynamics, we calculated reaction energies and barriers from rial in nature and scope, reviewing progress in following glass corrosion first-principles. This can provide insights into the molecular-level and reactivity utilizing spectroscopic methods and computational stud- mechanisms of glass dissolution. ies within our laboratories and with collaborators. In particular, the an- alytical tools discussed will include solid-state nuclear magnetic reso- 9:00 AM nance (NMR) methods as well as infrared techniques, x-ray (GOMD-SI-085-2012) Distinguishing Chemical Reaction Affinity photoelectron spectroscopy (XPS), secondary ion mass spectrometry from Mass Transport in Silica-Saturated Solutions (SIMS), and inverse gas chromatography (IGC). When coupled with W. Ebert*, Argonne National Laboratory, USA computational studies (ranging from simple atomistic modeling to den- Solution exchange tests were conducted to evaluate the relative impor- sity functional calculations), these spectroscopic tools provide informa- tance of chemical reaction and mass transport on the glass dissolution tion on the chemical nature of glass corrosion processes. rate in solutions with high Si concentrations. The effects of these 11:00 AM processes on the long-term corrosion behavior of waste glasses must be known for reliable performance modeling, but the contributions are (GOMD-SI-089-2012) Observed Structural Changes in Leached difficult to distinguish in typical corrosion tests because they yield simi- Nuclear Waste Glasses by Solid State NMR lar kinetics and small differences in the modeled behavior are similar in K. Murphy*, The Pennsylvania State University, USA; K. T. Mueller, Pacific magnitude to uncertainties from testing artifacts. Periodic exchange of Northwest National Laboratory, USA; C. G. Pantano, The Pennsylvania State the test solution with fresh leachant was used to maintain a nearly con- University, USA; J. V. Ryan, N. M. Washton, Pacific Northwest National stant reaction affinity and highlight mass transport effects. Although Laboratory, USA glass dissolution displays diffusion-like kinetics suggesting densification The influence of the surface alteration layer on long-term residual leach of the glass surface provides a transport barrier, the effectiveness of the rates for nuclear waste glasses is not fully understood. Solid State NMR barrier is sensitive to the solution composition. Glass corrosion models was utilized to ascertain the structural differences between the alteration should account for the interdependencies of these processes. layer and the bulk glass for two simplified compositions based on well-

2012 Glass & Optical Materials Division Annual Meeting 55 Abstracts studied systems. Leaching reactions were conducted at 90 °C with a high photo-reduced iron). The techniques to mitigate this absorption in PTR surface area to volume ratio. Cross-polarization magic angle spinning glass by means of optical bleaching of silver containing particles are de- (CP-MAS) NMR isolated surface information via polarization transfer scribed and the associated mechanisms are discussed. A study of the from protons (1H) to various glass components. The Carr-Purcell-Mei- thermal stability of this absorption was performed. We show that low boom-Gill pulse sequence enhanced signals obtained from 1H-29Si CP- absorption is maintained up to 200C, however heating the glass beyond MAS NMR. Surface area was determined by reactive silanol quanitifica- 200C results in the formation of new silver containing particles which tion through functionalization with a fluorine-containing chlorosilane have structure of absorption different than before bleaching. and subsequent analysis by 19F MAS NMR. Observations indicate that the alternation layer structure is derived from interactions with the so- 8:40 AM lution, which are a function of the original glass composition and (GOMD-SII-035-2012) Formation and structure of Au nanoparticles leachant conditions. in sodium trisilicate ruby glass by X-ray absorption and optical spectroscopy 11:20 AM C. Saiyasombat*, H. Jain, Lehigh University, USA (GOMD-SI-090-2012) The Use of Isotopic Tracing to Determine Elemental Diffusion Profiles Through an Established Alteration Development of color in ruby glass through the precipitation of gold Layer nano-particles is a well known phenomenon. We have investigated its atomistic mechanism by X-ray absorption near edge structure (XANES) J. Ryan*, A. V. Mitroshkov, Z. Zhu, J. J. Neeway, D. A. Schreiber, Pacific analysis at the Au L -edge and Sn K-edge in sodium trisilicate glass Northwest National Laboratory, USA 3 ≤ doped with 0.1mol% HAuCl4; varying amounts of SnO2 (0.005 0.1 One of the key remaining questions in the long-term corrosion behav- mol%) was added to facilitate the reduction of Au ions. The samples ior of glass is the mechanism and extent by which alteration layers pres- were prepared by conventional melt-quench technique followed by ent a barrier to corrosion. To investigate the diffusion of ions and their thermal treatment. Development of ruby color was followed with opti- rate of dissolution/reprecipitation/exchange from glasses in a mature cal spectroscopy in-situ heating apparatus, which showed red-shift and state of corrosion, compositionally equivalent glasses with two different blue-shift of gold peak depending on tin concentration, while XANES isotopic ratios were synthesized and allowed to corrode under the same indicated transformation of ionic gold to metallic gold. However, the tin conditions. Following the development of a mature alteration layer, the remained as Sn4+ ions even after heat treatment, indicating that tin may solutions were swapped and the concentration of individual isotopes served as a reducing agent or a catalyst for the reduction of ionic to monitored both in solution (ICP-MS) and alteration layer depth pro- metallic gold, and gold diffusion is the rate limiting step. files (SIMS, APT). The results suggest substantial and rapid participa- tion of several monitored ions in solution with the alteration layers. For 9:00 AM Li, diffusion far into the glass is observed, despite an “uphill” concentra- (GOMD-SII-036-2012) Brillouin scattering from superpolished tion gradient. The implications of these results on mechanistic interpre- vitreous silica in the Urbach-tail region tations of glass corrosion will be discussed. B. Rufflé*, E. Courtens, M. Foret, University of Montpellier II, France 11:40 AM Recent ab initio simulations have shown that the Urbach-tail of v-SiO2 (GOMD-SI-091-2012) Atomic Profiles of Corrosion Layer Interface is related to the existence of structural correlations that were called “hid- by Atom Probe Tomography den structures” in [1]. It would be of considerable interest to experi- mentally observe these structures. To this effect one can envision to D. K. Schreiber*, J. Ryan, Pacific Northwest National Laboratory, USA study the Landau-Placzek ratio RLP. Indeed, the resonant Rayleigh scat- Atom probe tomography (APT) was used to characterize the buried in- tering by hidden structures in the region of the Urbach tail should in- terface representing the corrosion front of a simulated nuclear waste crease the elastic intensity over that value simply due to the disorder glass that had been corroded for 25.75 years. Several samples of this in- frozen-in at the fictive temperature. Brillouin linewidths could also be terfacial region produced reconstructions of up to ~100 million atoms, affected by refractive index fluctuations. This paper discusses the output clearly showing concentration profiles with sub-nanometer resolution. of a recent inelastic UV Brillouin scattering experiment on v-SiO2 using The profiles of many elements appear to be significantly sharper than a high grade superpolished silica sample, with the main goal of deter- past observations. The intricacies of performing APT on interfacially mining the E-dependence of RLP and Brillouin linewidths close to the heterogeneous amorphous oxide materials will be discussed, as well as absorption edge [2]. [1] F. Inam, J. P. Lewis, and D. A. Drabold, Phys. the implications of the results on interpretations of the relative impor- Status Solidi A 207, 599 (2010). [2] B. Rufflé et al., PRB 84 132201 tance of diffusion vs. reaction corrosion mechanisms as modeled in (2011). long-term performance calculations. 9:20 AM (GOMD-SII-037-2012) Predicting the Photoelastic Response of Symposium II: Optical Materials & Devices Silicate Glasses M. M. Smedskjaer*, J. C. Mauro, X. Guo, S. A. Saxton, A. J. Ellison, Corning Inc., Session 4: Optical Absorption USA Room: Salon C Several interesting glass families are known for which the birefringence Session Chair: Mark Davis, SCHOTT North America, Inc. is zero in the presence of anisotropic stress. However, the underlying physical origins of zero-stress optic response are not yet understood. We 8:00 AM present a thorough experimental and modeling study revealing the mi- (GOMD-SII-034-2012) Photo-thermo-induced absorption in photo- crostructural origins of the photoelastic response of various silicate thermo-refractive glass (Invited) glasses. In particular, we investigate 32 sodium aluminosilicate glasses J. Lumeau*, L. Glebova, L. B. Glebov, University of Central Florida, USA with different types of alkaline earth oxides (MgO, CaO, SrO, and BaO). PTR glass is a photosensitive silicate glass which provides refractive We demonstrate that most of the composition dependence of the stress index change after UV-exposure and thermal treatment. This glass is optic response can be captured by a linear regression model and that the used for volume Bragg gratings recording and these optical elements individual contributions from the alkaline earths to the stress optic re- find many applications in high power laser systems. In this paper we sponse depend on the alkaline earth-oxygen bond metallicity. High present the sources of absorption in pristine and UV exposed and ther- bond metallicity is required to allow bonds to be distorted along both mally developed PTR glass. Using spectro-photometric and calorimet- the bonding direction and in the orthogonal directions. These findings ric techniques, we reveal the main species at the origin of photo- are valuable for predicting and tailoring the photoelastic response of sil- thermo-induced absorption (mostly silver containing particles and icate glasses.

56 2012 Glass & Optical Materials Division Annual Meeting Abstracts

9:40 AM tive measure of physical ageing and determining the boundaries of re- (GOMD-SII-038-2012) Calorimetric Absorption Measurements of versibility windows. Laser Glasses 11:20 AM M. J. Davis*, J. S. Hayden, SCHOTT North America, Inc., USA (GOMD-SI-106-2012) Transport, intermediate phases and rigidity in A calorimetric-based approach for low-loss absorption measure- glass-forming liquids ments—in which the temperature excursion of a sample upon absorp- M. Micoulaut, M. Bauchy*, UPMC, France tion of light is carefully monitored—has a very long history, dating back nearly to the invention of the laser itself. Simple in theory, this approach Using Molecular Dynamics simulations, we study the effect of pressure has a number of technical challenges that must be surmounted in order on a flexible alkali disilicate glass and associated liquid. Viscosity, diffu- for the technique to have practical use. This presentation will cover re- sion, structure, vibrational properties are computed and display differ- cent work at SCHOTT in which the surface temperature of small Nd- ent régimes that can be linked to the underlying elastic nature of the doped laser rods (3 x 25 mm) in a vacuum environment were carefully network backbone: flexible, intermediate, rigid. It underscores the pos- measured while illuminated by a ~160 mW 1064 nm laser source. The sibility for a given system to become rigid by either compositional beam profile in the laser rod, heat losses, thermal gradients, and various change or by application of pressure. transient effects were considered. Previous theoretical treatments tai- lored to extract the desired absorption loss value were compared and Symposium III: Cross-Cutting Topics contrasted in the present study to determine which offered the best combination of precision and accuracy while maintaining sufficient simplicity to be useful in an industrial R&D setting. Session 3: Archeological Glass Science and Technology Symposium I: Glass Science Room: Grand Suites II & III Session Chair: Denis Strachan, Pacific Northwest National Laboratory Session 6: Topological Constraints and Rigidity: 8:00 AM Theory and Experiment I (GOMD-SIII-032-2012) An archaeological slag for probing glass/iron Room: Salon C interaction (Invited) Session Chair: Pierre Lucas, Univ of AZ-Harshbarger Rm 224B S. Gin*, A. Michelin, D. Neff, P. Dillmann, E. Burger, D. Rebiscoul, CEA, France An archaeological slag from the 16th century has been investigated as an 10:20 AM analog of nuclear waste glass for deep geological disposal. We focused (GOMD-SI-104-2012) Topological Principles of Borosilicate Glass on the glass/iron interaction in order to better understand why and how Chemistry (Invited) iron increases glass alteration. The results were compared with those J. C. Mauro*, M. M. Smedskjaer, R. E. Youngman, C. L. Hogue, M. Potuzak, from in-lab experiments on nuclear glass/iron/clay systems. In both Corning Incorporated, USA; Y. Yue, Aalborg University, Denmark cases, SEM, TEM and STXM characterization revealed that iron metal, Borosilicate glasses display a rich complexity of chemical behavior de- when corroded in anoxic and reducing conditions, leads to the precipi- pending on the details of their composition and thermal history. We in- tation of iron silicates and the incorporation of iron within the gel, sus- vestigate the topological principles of borosilicate glass chemistry cover- taining glass alteration by consumption of silica in nonprotective mate- ing the extremes from pure borate to pure silicate end members. Based rials. This process warrants further investigation, and thermodynamic on NMR measurements, we present a two-state statistical mechanical data on the iron silicate phase are required to assess the long-term be- model of boron speciation in which addition of network modifiers leads havior of glass when situated near a source of iron. to a competition between the formation of nonbridging oxygen and the 8:40 AM conversion of boron from trigonal to tetrahedral configuration. Using this model, we derive a detailed topological representation of alkali-al- (GOMD-SIII-033-2012) The formation regularity of black-glazed tea kaline earth-borosilicate glasses that enables the accurate prediction of bowls from the Jian kiln site of ancient China properties such as glass transition temperature, liquid fragility, hard- W. Li*, H. Luo, Shanghai Institute of Ceramics, China ness, and configurational heat capacity. The implications of the glass The Jian kiln, located in present-day Jianyang county of Fujian province topology are discussed in terms of both the temperature and thermal of China, mainly produced black-glazed tea bowls. Jian tea bowl was history dependence of the atomic bond constraints and the influence on used as a utensil for tea tasting and was greatly appreciated by emperor relaxation behavior. Huizong of the Northern Song dynasty. The black glaze of Jian bowl was sometimes marked with streaks or spots, usually called ‘‘hare’s fur’’ or 11:00 AM ‘‘oil spot’’, which are the crystalline markings of iron oxide precipitated (GOMD-SI-105-2012) On the criterion for identification of during firing in the dragon kiln. Based on the physico-chemical founda- intermediate phases in network glasses tion for the formation of glaze microstructure, the correlation among R. Golovchak*, Lehigh University, USA composition, microstructure, and visual appearance has been investi- Recent search for the intermediate phases (reversibility windows) in gated by means of energy-dispersive X-ray fluorescence, X-ray diffrac- various glass-formers yields numerous experimental methods and theo- tion, and field emission electron microscopy. For the first time, the retical approaches. In particular, it was assumed that marginality of study provides realizing proofs for two kinds of microstructural form- non-reversible heat flow in temperature-modulated DSC experiments ing mechanics. with short-term aged samples is a reliable criterion for identification of 9:00 AM these phases. At the example of As-Se, As-S and Ge-Se glasses subjected to long-term (tens of years) physical ageing it is shown, that non-re- (GOMD-SIII-034-2012) Characterization of Roman Glasses as versible heat flow component has a time-dependent kinetics. Therefore, Analogues for Nuclear Waste Glasses it can not be used as an appropriate criterion for establishing the limits D. Strachan*, J. Ryan, J. Crum, D. Schreiber, Pacific Northwest National of reversibility windows in terms of self-organized network and non- Laboratory, USA ageing ability. The only DSC experiments (both temperature-modu- Glasses have been used for treasured articles for at least the last 4500 y. lated or conventional) performed in a real time scale from earliest stages The ancient people who produced these glasses and glass artifacts un- of as-prepared up to long-term aged state can be useful for the quantita- wittingly started ‘experiments’ that can help us determine the mecha- nism by which silicate glasses dissolve. Ancient glasses, while having

2012 Glass & Optical Materials Division Annual Meeting 57 Abstracts simple compositions relative to nuclear waste glasses, dissolve by the quadrupolar effects per Massiot et al. (1990) gives an NBO content of same mechanism and have been found in a variety of different environ- 67.6% vs. the known value of 67.7%. Applying these techniques to the ments. The characterization of alteration products and dissolution glass, the corrected NBO content is 58.4% ± 0.7% vs. the 55.5% ± 1.6% depths can yield important information on the dissolution mechanisms expected from stoichiometry (based on EMPA analysis). This informa- operating over long periods of time. In this paper, we discuss several tion will allow improved accuracy and give new insight into questions glasses that we have obtained, their compositions, the areas where these such as the presence/absence of measureable amounts of free oxide ions glasses were found, and the analyses we are performing to help elucidate or oxygen triclusters in both simple silicate and more complex alumi- the dissolution mechanism, and the impact of the results on current nosilicate glasses. glass corrosion theory. Session 2: NMR Studies of the Structure of Glass 1: Symposium I: Glass Science Mixed Glass Former Systems Session 2: Non-Oxide Glasses II Room: Grand Suites II & III Room: Salons E, F, & G Session Chair: Steve Martin, Iowa State University Session Chairs: Andriy Kovalskyy, Austin Peay State University; David 10:20 AM Musgraves, Clemson University (GOMD-SIII-017-2012) Mixed Glass Former Effect in alkali 1:20 PM borophosphate glasses: Structural investigation by advanced 31P and (GOMD-SI-045-2012) Chalcogenide glasses, materials for homeland 11B NMR (Invited) security applications (Invited) A. Pradel*, B. Raguenet, Université Montpellier 2, France; G. Tricot, Université M. Vlcek*, University of Pardubice, Czech Republic des Sciences et technologies de Lille, France; G. Silly, M. Ribes, Université Montpellier 2, France In this paper we will demonstrate some unique properties and function- alities of chalcogenide glasses (CHG) which make them suitable candi- The concept of mixed glass former effect has been re-visited thanks to dates for homeland security applications. In large part, the demand to the combination of (i) an efficient elaboration technique that helped in secure our society against various possible threats has grown within the producing a series of Li-rich borophosphate glasses from pure phos- last decade because of globalization and the concurrent increase in ac- phate to pure borate and (ii) a structural investigation based on ad- tivity of extremists, terrorists, hackers and counterfeiters. The pervasive vanced 1D/2D solid state NMR performed at standard and very high nature of these threats has resulted in dedicated efforts to develop: (i) magnetic fields using very recently developed methods (11B{31P} D- new sensors capable of detecting parts per billion concentrations of HMQC, 11B DQ-SQ). Homogeneous glasses were prepared all along volatile organics; (ii) optical devices which allow secure data transmis- the 45Li2O– 55[xB2O3– (1-x)P2O5]. It allowed to investigate the rela- sion; (iii) the next generation of high density data storage materials; and tion between electrical/thermal properties and structure over the full (iv) the next generation of optical security devices for the protection of range of composition. The advanced 1D/2D solid state NMR investiga- government documents, banknotes and products of high interest tion helped in producing unreported and deep insights onto the glass against counterfeiters. These are but a few examples where the use of structure about (i) the multiple BO4 chemical environments, (ii) the CHG-based devices already play a key role or could have an enabling BO3-BO4 connectivity, (iii) the wide range of phosphate speciation and role in the near future. (iv) unexpected and unreported correlations between trigonal boron and phosphate species. 2:00 PM 11:00 AM (GOMD-SI-046-2012) Structural interpretation of spectral selectivity of photoinduced effects in As S thin films (GOMD-SIII-018-2012) The Mixed Network Former Effect in 2 3 A. Kovalskyy*, Austin Peay State University, USA; M. Vlcek, University of Glasses: Structure-Property Correlations in Phosphate-Based Glass Pardubice, Czech Republic; J. Oelgoetz, Austin Peay State University, USA; H. Systems (Invited) Jain, Lehigh University, USA H. Eckert*, M. Rinke, D. Larink, F. Behrends, WWU Münster, Germany; S. Martin, WWU Münster, Germany, WWU Münster, GermanyIowa State Photoinduced effects in chalcogenide glass thin films are one of the University, USA most popular topics in physics of amorphous solids. Various interpreta- tions of the above effects include photoinduced changes of electron-lat- Non-linear changes in the physical properties of glasses containing tice interactions, photostructural transformations, and photo-induced more than one type of network former species are often exploited for defect formations. Many of the optically-induced effects reveal spectral optimizing the technological performance of glasses. Issues at the struc- selectivity associated with different energy of irradiation, specifics of tural level concern the identification of the coordination polyhedra, band gap structure films and spectral dependence of photoinduced their connectivity distribution, and the competition of both network structural relaxation in glass. The aim of this work is to reveal the mech- formers for the network modifier species. Modern solid state nuclear anisms of photostructural transformations of thermally evaporated magnetic resonance (NMR) techniques present a new element-selective, As S thin films laser irradiated with sub-, super- and bandgap light. inherently quantitative approach to this problem. Quantitative results 2 3 The structure of freshly prepared and irradiated films is determined are discussed for a variety of phosphate and borate based mixed-net- both on atomic and molecular level using high-resolution X-ray photo- work former glasses electron spectroscopy and Raman spectroscopy methods. Experimental 11:40 AM spectra are compared to theoretical predictions based on density func- (GOMD-SIII-019-2012) Increased Accuracy For Non-bridging tional theory. Oxygen Measurements in Silicate Glasses Using 17O NMR 2:20 PM L. M. Thompson*, J. F. Stebbins, Stanford University, USA (GOMD-SI-047-2012) Structure and Properties of B-containing Oxygen-17 nuclear magnetic resonance (NMR) provides a number of GeAs Sulfide and Selenide Glasses (Invited) insights into glass and melt structure. Increasingly, it is being used to B. Aitken*, S. Currie, R. Youngman, Corning Inc., USA measure the non-bridging oxygen (NBO) content in a variety of glasses Although an important constituent of many oxide glasses, boron is to test structural models. To test the accuracy of this method, we have rarely used as a component in unmodified network chalcogenide synthesized a crystalline barium silicate, BaSiO , and a barium silicate 3 glasses. In this study we have synthesized homogeneous glasses in the glass (BaO) (SiO2) , chosen for the resolution between NBO and 0.43 0.57 GeAsB sulfide and selenide systems with B concentrations as high as BO components of spectra. Correcting the observed intensities for the

58 2012 Glass & Optical Materials Division Annual Meeting Abstracts

20% and with S,Se levels ranging from chalcogen-excess through stoi- 4:40 PM chiometric to chalcogen-deficient. The glasses have been characterized (GOMD-SI-050-2012) DFT studies of the atomic structure of by calorimetry as well as by optical and NMR spectroscopy. Increasing B disordered chalcogenides levels result in a steady decrease in Tg. 11B MAS NMR shows B to be S. Le Roux*, C. Massobrio, Institut de Physique et Chimie des Matériaux de present only in 3-fold coordination, with evidence for both ring and Strasbourg, France non-ring BS,Se3/2 species. The redshifted absorption edge of chalco- gen-deficient Ge-containing glasses signals the presence of metal-metal Over the past 17 years we have undergone an atomic-scale study of short bonding, but the lack of a NMR resonance typical of elemental B indi- and intermediate range properties in disordered chalcogenides. We have cates that chalcogen deficiency is accommodated only by the formation based our investigations on first-principles molecular dynamics carried of Ge-Ge bonds. out in the self-consistent density functional theory (DFT) framework. At the outset, we were stimulated by the intriguing presence of the inter-

3:20 PM mediate range order in the structure of liquid GeSe2, as shown by the (GOMD-SI-048-2012) Structure and properties of telluride glasses appearance of the first-sharp diffraction peak in some of the partial for sensing applications (Invited) structure factors. Ever since that time, a wealth of information on the P. Lucas*, Z. Yang, A. Wilhelm, University of Arizona, USA; P. Jovari, RISSPO, short and intermediate range properties and the interplay between Hungary; B. Bureau, University of Rennes, France topology and electronic structures were collected. Among the systems studied we can mention glassy GeSe , glassy SiSe , liquid and glassy Telluride glasses are good glass formers over wide range of compositions 2 2 GeSe4, liquid and glassy Ge2Se3 as well as glassy GeS2. The talk will pres- and can incorporate halide, alkali and metallic elements in large quanti- ent a few representative examples of these research accomplishments. ties. The heavy component elements result in low phonon energy and confer very wide infrared transparencies to these glasses. They also have 5:00 PM low band-gap which results in significant charge carrier density and (GOMD-SI-051-2012) The stress-optic response of Ge-P-S glass: fairly high electrical conductivity. Finally they show good chemical re- experimental results and comparison with models sistance to aqueous environments. This set of properties makes these J. Galbraith*, J. Zwanziger, Dalhousie University, Canada; B. Aitken, Corning glasses ideal for sensing application. We will review the structure and Inc., USA properties of these novel glasses and their application to bio-sensing. The empirical model of photoelasticity proposed by Zwanziger et al. 4:00 PM [Chem. Mater. 19, 286-290 (2007)] relates the local structure of glass to (GOMD-SI-038-2012) Thermal Properties of Chalcogenide Glasses the stress-optic response. This model has been able to predict success- J. Musgraves*, S. Danto, P. Wachtel, K. Richardson, Clemson University, USA fully the composition of zero-stress optic oxide glasses. However, it has not been tested on chalcogenide glasses. The system Ge-P-S is used for Thermal analysis can deliver information about glass structure and analysis here of the empirical model because its local structure has been properties over a wide range of length scales and application areas. Due studied extensively [J. Non-Cryst. Solids 333, 28-36 (2004), J. Phys. to the fundamental differences in chemistry between chalcogenide Chem. B 106, 11093-11101 (2002)], and a variety of structures and co- glasses and their oxide counterparts, the thermal behavior and response ordinations are present. The stress-optic coefficients of stoichiometric of these glass families is markedly different in many important ways. GeS2-P2S5 glasses and non-stoichiometric Ge2.5PSx measured at 1550 This talk will review the composition dependence of a number of ther- nm are presented. The results are compared with the predictions of the mal properties of chalcogenide glasses including the glass transition, empirical model, and deviations and limitations of the model are dis- thermechanical properties, viscosity, and the thermo-optic coefficient. cussed. Data has been compiled from a large number of binary and ternary glass systems using the SciGlass database, permitting realistic compar- 5:20 PM isons across glass families in order to identify compositional factors (GOMD-SI-052-2012) Effects of Structure on the Distribution of controlling the thermal properties of these materials. This data is com- Activation Energy Model in the Na2S+GeS2+P2S5 Glass System pared with important structural models such as the Phillips Constraint C. Bischoff*, K. Schuller, S. P. Beckman, S. W. Martin, Iowa State University, USA and Stochastic Agglomeration Theories, showing where they success- fully capture the glass behavior and where they ultimately break down. A non-linear and non-additive composition dependent change in ionic 4:20 PM conductivity is known as the Mixed Glass Former Effect (MGFE). Alkali (GOMD-SI-040-2012) Thermal Poling Behavior and SHG Stability of ion conducting glasses are of particular interest for use in ion conduc- Multicomponent Chalcogenide Glasses tive batteries. Sulfide amorphous materials show promise as solid-state T. Shoulders*, University of Central Florida, USA; J. W. Novak, Clemson electrolytes due to their significantly large alkali ion conductivities as University, USA; M. Dussauze, Université Bordeaux, France; K. Richardson, compared to their oxide counterparts. Impedance spectroscopy meas- Clemson University, USA urements of the 0.5Na2S + 0.5[xGeS2 + (1-x)PS5/2] glass system exhibit a negative MGFE. Further, non-Arrhenius temperature dependence of Glasses of nominal compositions As36Ge6S58 and As34Ge6Na2S58 the conductivities can be explained by a distribution of activation ener- have been used to study the influence of both mobile cations and photo- gies (DAE). Vibrational and NMR spectra are used to identify composi- structural changes on the stability of second harmonic generation tional dependence of the short and intermediate range order of these (SHG) in thermally poled chalcogenide glass. Stability of the frequency- glasses and compared to insights resulting from the DAE model. Struc- doubled signal over time has been the major problem with poled ture-property correlations will be discussed. chalcogenides. This study discusses both the fabrication and optical characterization of samples before and after poling. Raman spec- troscopy has been used to examine photo-structural changes arising from irradiation at 633nm. Thermally poled samples showed an SHG response similar in magnitude to that reported previously for binary chalcogenide glass. Stability of SHG in the multicomponent glass, As34Ge6Na2S58, is superior to that of prior chalcogenide poling efforts. In addition to the role of sodium and glass network in enhancing the SHG stability, the effect of photo-structural changes of the network on both the stability and magnitude of SHG is discussed.

2012 Glass & Optical Materials Division Annual Meeting 59 Abstracts

Session 4: Relaxation II 3:20 PM Room: Salon A (GOMD-SI-079-2012) Insights into glass transition and relaxation Session Chair: Tanguy Rouxel, University Rennes 1 behavior using temperature-modulated differential scanning calorimetry 1:20 PM X. Guo*, J. C. Mauro, D. C. Allan, R. L. Stewart, Corning Inc., USA; Y. Yue, (GOMD-SI-076-2012) Thermodynamics of viscous flow and Aalborg University, Denmark elasticity of glass forming liquids in the Glass Transition Range Temperature-modulated differential scanning calorimetry (TMDSC) is (Invited) based on conventional DSC but with a sinusoidally modulated temper- T. Rouxel*, University Rennes 1, France ature path. Our simulations of TMDSC signals prove that the frequency The elastic moduli of glasses from different chemical systems, including correction of non-reversing heat flow can give a master curve within a oxide, chalcogenide, oxynitride, and metallic, were investigated through certain range of frequencies. This frequency range is dependent not only the glass transition (Tg), typically from 0.4 to 1.3 Tg. These data were on the measurement parameters such as linear heating/cooling rate and used to interpret the temperature sensitivity of the shear viscosity coef- frequency and amplitude of the modulation, but also on the previous ficient obtained on the same materials. The relevant Gibbs free activa- thermal history before the TMDSC measurement. The frequency cor- tion energy was estimated from the apparent heat of flow by means of rection for the reversing heat flow gives more insights into the glass the temperature dependence of the shear elastic modulus. The activa- structural response to thermal treatments. tion entropy associated with the viscous flow was also derived and was 3:40 PM found to correlate with the fragile versus strong character of the glass forming liquids. Finally, the physico-chemistry of the flow process was (GOMD-SI-080-2012) Prony series temporal spectra for structural described on the basis of the glass network de-structuration which relaxation in optical glass shows up through the temperature dependence of Poisson’s ratio, and E. Koontz*, V. Y. Blouin, Clemson University, USA an expression for the shear viscosity coefficient is proposed which is This study explores the Prony series expression of structural relaxation chiefly based on the high temperature elastic behavior. temporal spectra of N-BK7 glass in the temperature regime near the glass transition. In a TMA, square cross-section glass samples were sub- 2:00 PM jected to increasing and decreasing temperature steps just below the (GOMD-SI-077-2012) Phenomenological Modeling of Structural glass transition temperature. The structural relaxation behavior was Relaxation with a Modified TNM Model (Invited) quantified using a Prony series curve fit defined by weights and their R. G. Erdmann*, P. Lucas, E. A. King, University of Arizona, USA corresponding times. At a given temperature the plot of weights versus The TNM model has been successful in describing the relaxation of times shows discrete distributions of times in the short range, on the some chalcogenide glasses, but it performs poorly when used to model order of seconds and in the very long range, on the order of hours. GeSe and some As-rich AsSe glasses. Among the assumptions of the These times appear to describe specific relaxation behaviors of the glass. TNM model is the use of a KWW stretched exponential to capture the This study suggests that a Prony series fit of relaxation data can capture spectrum of characteristic relaxation times in the glass. Although con- the range of times at which different relaxation phenomena occur venient, the use of a stretched exponential implicitly assumes a specific within a glass. A comparison of relaxation spectra for different temper- unimodal distribution of relaxation times, implying that it may be inap- ature jumps can give insight into the time scale on which these processes propriate for simulating relaxation in which there are two or more dis- take place. tinct modes of relaxation. Evidence is presented that the poor perform- 4:00 PM ance of the TNM model for some chalcogenide glasses is caused by the Δ failure of this assumption. We present a modified TNM model in which (GOMD-SI-081-2012) The Temperature Width, Tg, of the Glass the stretched exponential is abandoned in favor of a bimodal distribu- Transition as a Function of Composition in Alkali Borate Glasses tion of relaxation times. The model’s performance is evaluated for S. Feller, T. Munhollon*, K. Podhajsky, M. Affatigato, Coe College, USA glasses where the normal TNM model fails and a comparison between We have measured the temperature width, ΔTg, of the glass transition as the model and MDSC experiments is made. a function of composition in alkali borate glasses. We have observed a sharp maximum in this parameter at about 2 to 5 molar percent modi- 2:40 PM fier with lithium showing the greatest effect and cesium the least. A dis- (GOMD-SI-078-2012) Parametric Studies of Simulated Modulated cussion of this result in terms of structure and relaxation is presented. DSC with the TNM Model Also, we conducted experiments as a function of the DSC heating rate E. A. King*, R. G. Erdmann, P. Lucas, University of Arizona, USA and as a function of thermal history. This work supported by NSF We previously showed the successful application of parametric opti- DMR-0904615. mization to extract accurate TNM model parameters by direct fitting of 4:20 PM experimental DSC data for chalcogenide glasses. The computational ef- ficiency of the model enables the simulation of arbitrarily complex ther- (GOMD-SI-082-2012) Phonon theory of liquids and their glass mal histories, including those applied in modulated DSC (MDSC) ex- transition periments. Simulation of MDSC enables the extraction of the real and K. Trachenko*, Queen Mary University of London, United Kingdom imaginary parts of the complex heat capacity, thereby enabling a more Calculating liquid energy and heat capacity in general form is an open detailed view of the kinetic and thermodynamic components of the problem in condensed matter physics. We develop a new approach to glass transition. We present a parametric study of simulation of MDSC liquids based on their phonon states, where the energy depends on re- across a wide range of TNM model parameters and show the relation laxation time only, but not on generally unavailable structural correla- between these parameters and the real- and imaginary parts of the sim- tions and interatomic potentials. We compare theoretical results to the ulated heat capacity. Particular attention is paid to the KWW stretching experimental data of many liquids including water, and find good agree- exponent and its effect on the shape of the imaginary heat capacity. ment in a wide range of temperature and pressure. We subsequently ad- dress the problem of glass transition of how to explain the origin of heat capacity jump at the glass transition temperature Tg without a reference to a distinct glass phase and a phase transition of sort. We show that the jump, both qualitatively and quantitatively, is a result of the change of the liquid’s elastic and thermal properties when the system stops flow-

60 2012 Glass & Optical Materials Division Annual Meeting Abstracts ing at the experimental time scale at Tg. Trachenko and Brazhkin, PRB 2:20 PM 83, 014201 (2011); Bolmatov and Trachenko, PRB 84, 012201 (2011) (GOMD-SI-095-2012) Nuclear glass dissolution at high pH K. Ferrand*, K. Lemmens, SCK-CEN, Belgium Session 5: Glass Corrosion and Surface Science II In the Belgian Supercontainer design for the geological disposal of vitri- Room: Salon B fied nuclear waste in the Boom Clay formation, the canisters of HLW or Session Chair: Nathan Mellott, Alfred University SF will be enclosed by a carbon steel overpack and a concrete buffer. Once the overpack will be perforated, the high pH of the incoming 1:20 PM water may have an impact on the lifetime of the vitrified waste. Hence, (GOMD-SI-092-2012) Effects of Alteration Product Precipitation on to evaluate the durability of glass matrix in such an environment, static Glass Dissolution: Preliminary Results tests were carried out at 30°C and 70°C in a water with a high pH of D. M. Strachan, J. J. Neeway*, J. V. Ryan, Pacific Northwest National Laboratory, 13.5. Moreover, the solution chemistry and its effect on glass dissolution USA will be different for large and small cracks. Consequently, tests were also Often it is observed that the precipitation of certain silica-bearing alter- performed with confined glass powder to give information about these ation products can cause an increase in the glass dissolution rate. How- possible mechanisms. Compared to tests with dispersed glass powder, ever, it has also been observed that in the presence of these silica-con- the long term rates at 30°C were lower indicating that the confinement taining species [H4SiO4] does not significantly decrease while other leads to an overall decrease of the alteration rate. At 70°C, the confine- elements continue to be released. In this study, we use the Geochemist’s ment had no effect on the glass dissolution rate. Workbench code to investigate the relationship between glass dissolu- 2:40 PM tion rates and the precipitation rate of silica-bearing alteration prod- ucts. We suppress all of the possible alteration products except a few, in- (GOMD-SI-096-2012) Structural evolution under aqueous corrosion cluding analcime (a surrogate alteration product) and amorphous silica. of borosilicate glasses containing rare earths The cross affinity code option allows us to establish glass equilibrium E. Molières*, F. Angeli, P. Jollivet, CEA - Marcoule, France; D. de Ligny, G. constants. Calculations of dissolution rates as a function of analcime Panczer, LPCML, France; T. Charpentier, A. Soleilhavoup, O. Spalla, CEA - precipitation rate and the meaning of results pertinent to long-term Saclay, France; S. Gin, CEA - Marcoule, France; P. Barboux, LCMCP-ENSCP, glass durability will be discussed. France Nuclear wastes are confined in borosilicate glass matrix in France. Fis- 1:40 PM sion products are part of nuclear wastes and some of them could be (GOMD-SI-093-2012) Measuring Long-Term Glass Dissolution simulated by rare earths(RE). In contact with water, glass constituents Rates in the Presence of Mineral Alteration Phases may be released, so it is necessary to investigate the influence and the be- C. L. Crawford*, Savannah River National Laboratory, USA; W. L. Ebert, havior of RE during aqueous alteration. To focus on RE contribution, Argonne National Laboratory, USA we study simplified borosilicate glasses with varying amounts of RE. Static tests were conducted to characterize the coupled kinetics of glass Pristine and altered glasses were characterized by Raman and high-reso- lution solid-state 17O MQMAS, 29Si and 11B MAS NMR. The oxygen ex- dissolution and alteration phase precipitation to identify the process 17 controlling the rate. Tests were conducted by immersing a glass test change sites during alteration by H2 O were characterized and quanti- specimen and a specimen of the same glass that had been pre-reacted to fied. RE are mainly retained and incorporated homogeneously into generate a crust of mineral alteration phases in a solution that had been alteration layer, they have a huge impact on silicon recondensation. pre-reacted with crushed glass to become nearly saturated with respect Glass without RE presents an alteration layer similar as amorphous sil- to the same suite of alteration phases. Tests were interrupted periodi- ica: repolymerization occurs. In presence of RE, repolymerization is cally to measure the mass of the test specimen and determine the disso- highly modified and inhibited. RE have also an impact on porosity as lution rate directly. The results of tests conducted at 90 °C with a simu- exhibited by SAXS experiments. lated waste glass known to be affected by alteration phase formation will 3:20 PM be presented. These tests show the relative importance of the surface areas and precipitation rates of key alteration phases, the solution com- (GOMD-SI-097-2012) Alteration mechanism of obsidian for its position and reaction affinity effects, and mass transport through alter- suitability as nuclear waste glass ation layers and solution during long-term waste glass corrosion. N. Rani*, J. P. Shrivastava, University of Delhi, India; R. K. Bajpai, BARC, India Paper discusses alteration of obsidian treated under near hydrothermal 2:00 PM conditions - relationships between mass loss and normalized mass loss. (GOMD-SI-094-2012) Coupled Waste Glass Dissolution and Mineral A protective layer composed of Si, Al, Na and K is developed over the Alteration Phase Precipitation glass surface, forms barrier preventing diffusion of water into secondary J. A. Fortner*, W. L. Ebert, Argonne National Lab, USA phases. Glass dissolution rate is affected by the formation of secondary The precipitation of mineral alteration phases is often observed to in- phases. The concentration of elements in leachates is reduced by their crease the dissolution rate for many simulated borosilicate waste glasses. adsorption onto neo-formed minerals thus, solution becomes under- It is hypothesized that the glass dissolution and precipitation rates are saturated. Obsidian alteration in natural environment yielded similar coupled through the common solution composition and that reaction physical and mineralogical changes - devitrification of glass along affinities are coupled. We will describe tests conducted to study this cou- cracks and formation of spherulite composed of yellowish brown pling of waste glass dissolution and mineral alteration phase precipita- chlorophiate and green coloured delesite, celadonite iddingsite and tion kinetics which combine detailed analyses of the solution and the chlorite, thus, consistent with the present experimental findings solids with the goal of determining the form of the affinity term, includ- 3:40 PM ing whether the reactions are best modeled as separate or coupled reac- tions. The initial tests are have used a glass for which alteration phase (GOMD-SI-098-2012) Understanding polishing-induced surface formation is known to significantly affect the glass dissolution rate. defectivity on EUV masks Knowing the solution composition and the size and abundance of key R. Teki*, A. Kadaksham, J. Harris-Jones, E. Stinzianni, F. Goodwin, SEMATECH, alteration phases triggering the increased glass dissolution rate is neces- USA sary to incorporating this effect in the glass performance models. Ultra-low thermal expansion Ti-doped fused silica substrates for ex- treme ultraviolet (EUV) lithography masks require sub-Angstrom sur- face roughness, sub-100 nm flatness, and no defects larger than 2 nm high/deep. Chemical mechanical polishing (CMP) to achieve such sur-

2012 Glass & Optical Materials Division Annual Meeting 61 Abstracts faces results in random sub-10 nm pit-type defects and scratches. More- droxyapatite, were characterized by x-ray diffraction, micro-Raman over, post-CMP cleaning of the substrates to remove particles adds to spectroscopy, analytical SEM, and TEM. At short times, 1393-B3 fol- the pit count and enlarges the scratches. The effects of different sub- lowed a reaction-controlled kinetic model, which transitioned to a dif- strate material characteristics on pit and scratch generation, such as fusion-controlled kinetic model at later times. The phosphate-free ana- doping, surface roughness/hardness, and extent of sub-surface damage, logue followed a reaction-controlled kinetic model for all times. are studied in this research. Metrology techniques such as nano-inden- tation, SIMS and TEM are used to gain a deeper understanding of the 5:00 PM surface. Results indicate that both doping and sub-surface damage (GOMD-SI-102-2012) Enhanced Dissolution Rate of Densified Glass: caused by CMP are responsible for making the substrates more prone to a Probe for Densification under Nanoindentations surface damage. Defect mitigation by removing sub-surface damaged J. Guin, CNRS-INSIS, France; K. Han*, Université de Rennes 1, France regions and using thin film smoothing layers is investigated. Oxide glasses present a permanent deformation phenomenon under 4:00 PM sharp contact conditions. Shear flow and densification are assumed to (GOMD-SI-099-2012) Study on glass frit corrosion influenced by be responsible for this behavior. Densification phenomenon involves - - permanent structural changes of the glassy network: number of SiO4 composition and water content in I /I redox electrolyte 3 units per ring, SiOSi angle, connectivity loss. In this work, a direct link K. F. Jensen*, A. Hinsch, W. Veurman, Fraunhofer Institute for Solar Energy between the measured enhanced dissolution rate and the densified ma- Systems ISE, Germany; S. Sarker, H. Son, J. Kim, Konkuk University, Republic of terial is established. This enhanced reaction rate, coupled with atomic Korea; C. Im, Konkuk University- Fraunhofer Next generation Solar cell re- force microscopy measurements, is used for probing the densified vol- search Center, Republic of Korea; J. Wilde, University of Freiburg, Germany; J. ume under nanoindentations. To do so, images of indents are captured Lee, Konkuk University- Fraunhofer Next generation Solar cell research Center, for different dissolution times.To reconstruct the zone affected by the Republic of Korea densification during indentation, the 3D cartography of dissolution The Dye-sensitized Solar cell (DSC) shows great potential as a building- vectors is computed from images captured at 2 different dissolution integrated façade element which generates electricity. One main chal- steps. Limitations of the developed technique will also be discussed. lenge towards long-term stable modules is the sealing. The liquid redox electrolyte has to be sealed hermetically in the DSC. Glass frit shows 5:20 PM promising results as sealant but interaction with redox species in the (GOMD-SI-103-2012) The Effect on Product Quality of Varying the electrolyte has been reported. Chemical reactions lead to decreasing Oxide to Magnox Ratio in High Incorporation UK Blend HLW Glass electrical performance and change the glass properties. Corrosion of a M. Harrison*, R. Short, N. Gribble, C. Steele, Sellafield Ltd, United Kingdom ZnO-SiO -Al O and a bismate glass frit in H O, I -/I- electrolyte and 2 2 3 2 3 The Sellafield Waste Vitrification Plant (WVP) converts highly radioac- electrolyte with 10 wt% H O were investigated. UV-vis photospectrom- 2 tive liquors from the reprocessing of spent nuclear fuel into glass to pro- etry was performed on electrolyte-filled cells in order to monitor vide a stable product suitable for safe long term storage and disposal. changes in I - absorbance. SEM and EDX analysis of the exposed glass 3 The WVP target waste incorporation was historically 25 wt%. However, frit surface allows a better understanding of the corrosion mechanisms. higher incorporations will result in fewer containers being produced, The influence of water was shown to be crucial for the corrosion of and thus reduce the burden on the Geological Disposal Facility. This ZnO-based glass frit, whereas the bismate glass frit showed greater sta- paper presents the results from the product quality assessment of 38 bility. wt% Oxide:Magnox blend glasses produced on the Vitrification Test Rig 4:20 PM (VTR). In particular, the durability of the product glasses was tested using both short- and long-term methodologies. The effect of varying (GOMD-SI-100-2012) Atomic Layer Deposition (ALD) Coating on the Oxide:Magnox blend ratio is also discussed. The overall conclusion Soda-lime-silicate Glass for Strength Improvement was that under the appropriate VTR operational parameters, the prod- Y. Arai*, C. G. Pantano, Pennsylvania State University, USA uct quality of 38 wt% Blend glass was within the acceptable range, and Cracks on the glass surface are hardly avoidable, and these can poten- in the case of durability, superior to lower waste incorporations. tially decrease glass strength. The modification of the cracks by coating to reduce the stress concentration at crack’s edge is a promising tech- nique for the strength improvement. We focused on atomic layer depo- Symposium III: Cross-Cutting Topics sition (ALD) which can coat high aspect ratio surface features such as cracks with precise layers. In this study, we investigated the effect of an Session 2: NMR Studies of the Structure of Glass 2: Al2O3 coating on strength for soda-lime-silicate glass. We evaluated sur- face strength based on cone-crack initiation loads (CIL) measured by Chemical Order and Disorder Effects Hertzian indentation, and then calculated the Weibull modulus (m). Room: Grand Suites II & III The ALD coated samples showed higher CIL values than the bare sub- Session Chair: Josef Zwanziger, Dalhousie University strate, and it increased with increasing the coating thickness. The m of 1:20 PM the coated samples were higher than the bare substrate, but it decreased with increasing the coating thickness. A 10 nm coated sample showed (GOMD-SIII-020-2012) Recent developments in the understanding the highest m which was more than three times larger than that of the of the structure of glasses containing lone-pair cations (Invited) bare substrate. D. Holland*, O. Alderman, N. Laorodphan, R. Dupree, Warwick University, United Kingdom; E. Barney, Nottingham University, United Kingdom; A. 4:40 PM Hannon, Rutherford Appleton laboratory, United Kingdom (GOMD-SI-101-2012) Dissolution kinetics of bio-active borate The “lone-pair” of non-bonding valence electrons which occur in the glasses in aqueous solutions low oxidation states of some heavy metal cations can be sterically inert, J. George*, R. Brow, Missouri University of Science and Technology, USA ns2, or sterically active (nsnp3)2. In the latter case, they give rise to a Borate bioactive glasses have been studied for use in scaffolds for soft low-coordination, asymmetric environment for the cation in which the tissue and bone repair. The present work provides a kinetic analysis of metal-anion bonds have a high degree of covalency. We have previously demonstrated, using mainly NMR and Mossbauer spectroscopies, that the dissolution behavior of 1393-B3 (51B2O3-24CaO-8MgO-9K2O- these environments are carried over from the crystalline state into the 6Na2O-2P2O5) and a phosphate-free analogue in deionized water. Glass powders were reacted at temperatures between 21 °C and 60 °C. The re- glass state. I will review the diffraction/NMR studies which have re- lease of B-, Ca-, P-, Na-, Mg-, and K-ions into solution was measured by cently been carried out on such glasses and indicate how the activity of ICP-OES and pH was monitored. Reaction end-products, including hy- the lone-pair depends on glass composition and also describe the

62 2012 Glass & Optical Materials Division Annual Meeting Abstracts knock-on effect which this can have on the environment of the network work-modifying cations) and temperature on B and Al coordinations former cations in the systems. Case studies will be given from systems and their interplay with oxygen speciation, notably the concentration of containing lone-pair cations of increasing nominal charge: Tl+, Pb2+, non-bridging oxygens (NBO). Analogous speciation reactions can relate Sb3+ and Te4+. Ge coordination and oxygen speciation in germanates, and play roles in ambient pressure aluminosilicate structures as well. In aluminosilicates, 2:00 PM glasses quenched from melts at pressures to 10 GPa again show analo- (GOMD-SIII-021-2012) Order and disorder in glasses : chemical and gous effects of modifier cation field strength on Si and Al coordination, geometrical contributions at different scales (Invited) with smaller and/or more highly charged cations favoring the concen- D. Massiot*, M. Deschamps, F. Fayon, V. Montouillout, N. Pellerin, P. Florian, D. tration of negative network charge on NBO and/or highly charged BO Neuville, S. Cadars, L. Martel, J. Hiet, CEMHTI-CNRS, France such as Al-O-Al groups. Complex equilibria among a number of struc- tural species may be needed to account for observations, but useful in- The local structure of glasses can be investigated by different high reso- sights can be transferred from one oxide melt system to another. lution NMR methods that allow sorting out chemical and geometrical contributions with impact on the description of these complex multi- 5:20 PM component systems at scales ranging from the coordination sphere up (GOMD-SIII-025-2012) Estimating the E-modulus of glasses from to the several nanometers. NMR structural data A. K. Swarnakar*, Leuven University, Belgium; A. Stamboulis, University of Session 2: NMR Studies of Structure of Glass 3: Birmingham, United Kingdom; O. Van der Biest, Leuven University, Belgium Structure and Dynamics The model developed by Makishima and Mackenzie (M-M) may yield Room: Grand Suites II & III reasonable estimates for the E-modulus of a range of glasses. In the M- Session Chair: Steve Martin, Iowa State University M model the bonding enthalpy and packing densities present in the compounds that form the glass are taken as input for the calculation. We 3:20 PM will show that a more accurate estimate can be obtained by incorporat- (GOMD-SIII-022-2012) Nuclear magnetic resonance studies of ing in the model structural information from MAS-NMR data. Specifi- mixing effects in ion conducting glasses (Invited) cally, we have determined the E-modulus for ionomer glasses with com- M. Storek, M. Adjei-Acheamfour, R. Böhmer*, TU Dortmund, Germany; R. position 4.5SiO2-3Al2O3-1.5P2O5-3CaO-2CaF2., in which Ca was Christensen, G. Olson, S. Martin, D. Larink, Iowa State University, USA; H. substituted by Ba, Sr and Mg. The structural studies on each glass sam- Eckert, Westfälische Wilhelms-Universität, Germany ple were performed by 27Al and 19F MAS NMR. The structural analysis shows that substitution of calcium by barium or strontium results in a Component mixing can have surprising effects on the ion conduction of disrupted network, whereas magnesium leads to a more packed net- inorganic glasses with the mixed mobile ion effect and the mixed net- work. When this structural information is incorporated in the M-M work former effect as well known examples. Both phenomena bear tech- model a significantly improved estimate of the E-modulus is obtained nological implications and were scrutinized by various theoretical ap- compared to the original model. proaches. Nevertheless, both effects are far from being fully understood on a microscopic level. This is partially due to a lack of detailed local structural and dynamical information regarding these non-crystalline Symposium I: Glass Science solids. As a local probe nuclear magnetic resonance provides useful in- sights into the concentration and temperature dependences of their charge transport. In this presentation we focus on how the cation dy- Session 6: Topological Constraints and Rigidity: namics in these interesting materials can directly be monitored by em- Theory and Experiment II ploying various mobile alkali species via spin-relaxation experiments, Room: Salon C line shape analyses, and stimulated-echo techniques. Partial funding of Session Chair: Pierre Lucas, Univ of AZ-Harshbarger Rm 224B this project was provided by the Deutsche Forschungsgemeinschaft. 1:20 PM 4:00 PM (GOMD-SI-107-2012) Towards ultra-strong glasses (Invited) (GOMD-SIII-023-2012) NMR Studies of Ion Transport in Solid and L. Wondraczek*, University of Erlangen, Germany Polymer Electrolytes (Invited) M. Vogel*, Institute of Condensed Matter Physics, TU Darmstadt, Germany New glassy materials are key for addressing major global challenges in energy, medicine, and advanced communications systems. For example, We combine a variety of 6Li, 7Li, and 109Ag NMR methods for a de- thin, flexible and large-area glass substrates will play an enabling role in tailed characterization of ion transport in solid and polymer electroytes. the development of flexible displays, roll-to-roll-processing of solar The methods include spin-lattice relaxation, line-shape, and stimulated- cells, next-generation touch-screen devices, and encapsulation of or- echo analyses. In particular, we measure multi-time correlation func- ganic semiconductors. The main limitation of glass in these applications tions to determine the degree and the origin of the nonexponential is its brittle fracture behavior, especially in the presence of surface flaws, ionic relaxation.Three- and four-time correlation functions indicate which reduces practical strength. Hence, the design of new ultra-strong that very pronounced and short-lived dynamical heterogeneities govern glassy materials and strengthening techniques is of crucial importance. the ionic hopping motion in both glasses and crystals. Two examples re- Here, we review the main issues regarding glass strength, with an em- veal the benefits of the NMR isotope selectivity. For mixed cation phasis on the underlying microscopic mechanisms responsible for me- glasses, it allows us to separately ascertain the mobility of the two cation chanical properties. The topological origin of these properties will be species and, for polymer electrolytes, it provides access to the coupling discussed, including its relation to structural and chemical heterogene- of ion and polymer dynamics. ity. Finally, toughening strategies for increasing the damage resistance of 4:40 PM glass products will be considered. (GOMD-SIII-024-2012) Network cation coordination and oxygen speciation in oxide glasses and melts: a view from NMR spectroscopy (Invited) J. F. Stebbins*, J. Wu, L. Thompson, stanford university, USA In borosilicate glasses, 11B, 17O, and 27Al NMR have recently con- firmed large effects of composition (e.g. the size and charges of net-

2012 Glass & Optical Materials Division Annual Meeting 63 Abstracts

2:00 PM 4:20 PM (GOMD-SI-108-2012) Anomalous elastic behavior of vitreous silica (GOMD-SII-041-2012) The Benefits of Polyalkylene Carbonate under high pressure and high temperature Binders (QPAC®) for Low Temperature Glass Frit or Powdered Glass S. Ayrinhac, M. Foret, H. Tran, R. Vacher, C. Weigel, B. Rufflé*, Montpellier in Low Temperature Thick Film Applications University, France P. A. Ferraro*, S. Hanggodo, Empower Materials, USA High-resolution Brillouin scattering experiments have been performed QPAC® 40 Polypropylene Carbonate, PPC, is an exceptional binder for under hydrostatic pressures in vitreous silica. At room-T, the internal use in low temperature firing thick film pastes because it decomposes at friction exhibits a sharp maximum located at 2 GPa, which appears to low temperatures leaving minimal residue after debind. The binder’s coincide with the well-known minimum in sound velocity. By analyzing low decomposition temperature allows for binder thermolysis at tem- the complex modulus in large frequency and T range the unrelaxed ve- peratures well below the sintering temperature of glass and metal pow- locity is found. It is constant at low-T and increases anomalously above ders that are used in ultra-low firing thick film applications. Dramati- a temperature onset. The onset strongly depends on pressure, which is cally reduced levels of remnant carbon after thermal processing will in agreement with a dynamical origin of the structural changes that pro- enable improvements in the mechanical, optical and electronic proper- duce the hardening [1]. We also report new in-situ studies under pres- ties of a fired thick film device. Thermal analyses of the rate of debind- sure at higher T. The compressibility anomaly shifts to higher pressure ing of thick film glass pastes made with ultra-low firing (420C) glass when T is increased to 500 K. Further, the maximum in the internal fric- and PPC were performed and compared with analogous thick film tion shifts even more rapidly. These new data are discussed with refer- pastes made with other common thick film binders. Rheological prop- ence to different models based e.g. on rigidity arguments or local modi- erties, residual carbon content and electrical properties of the various fications of ring structure. [1] S. Ayrinhac et al., Phys. Rev. B 84, 024201 binder systems was also evaluated. (2011). 4:40 PM (GOMD-SII-042-2012) Glass-Ceramic Nanocomposite Scintillators Symposium II: Optical Materials & Devices for Gamma-ray Spectroscopy B. Barta*, Georgia Institute of Technology, USA; J. H. Nadler, Z. Kang, B. Session 6: Optical Ceramics and Glass Ceramics Wagner, R. Rosson, B. Kahn, Georgia Tech Research Institute, USA Room: Salon C Glass-ceramic nanocomposite material systems show promise as alter- Session Chair: Robert Pavlacka, US Army Research Laboratory natives to single crystal scintillators currently used in gamma-ray spec- troscopy. The benefits of utilizing glass ceramic nanocomposites include 3:20 PM the ability to manipulate desired crystallite size, altering crystallite and (GOMD-SII-039-2012) Structural Characterization of Luminescent matrix glass compositions, and potential for up-scaling. This investiga- Glasses and Ceramics Using Solid State NMR (Invited) tion focuses on precipitating GdBr3(Ce) nanocrystals from sodium- H. Eckert*, H. Deters, WWU Münster, Germany; A. de Camargo, C. Magon, F. and alumino-borosilicate host matrices. Concentrations of up to de Lima, WWU Münster, Germany, WWU Münster, GermanyIFSC, USP, Brazil 31mol% GdBr3(Ce) have been achieved, which produces high light A comprehensive magnetic resonance strategy for the structural charac- yield while maintaining sample transparency. The glass-ceramic struc- terization of luminescent rare-earth doped glasses and vitroceramics ture is characterized to verify that the desired crystalline phase was pre- has been developed. It is based on the combined application of standard cipitated, and luminescence data collected to ensure peak emission lies solid state NMR methods and pulsed EPR spectroscopy, using the elec- within the 350-450nm wavelength range. Gamma-ray spectroscopy is tron spin echo envelope modulation effect. The strategy has been ap- performed to evaluate the ability of the glass-ceramic to differentiate plied to glasses and vitroceramics of the ternary system Y2O3-Al2O3- between radioisotope sources. B2O3, resulting in a detailed description of its structural organization 5:00 PM and crystallization mechanism. Extensions to other laser ceramic sys- (GOMD-SII-043-2012) Crystallization and optical properties in tems will be discussed. La2O-B2O3-GeO2 Glasses 4:00 PM H. Vigouroux*, E. Fargin, ICMCB, France; B. Le Garrec, CEA, France; M. (GOMD-SII-040-2012) A new synthesis way for the production of Dussauze, V. Rodriguez, F. Adamietz, ISM, France; J. Ravaux, R. Podor, ICSM, bulk chalcogenide glasses and glass-ceramics by mechanical alloying France; S. Lotarev, V. Sigaev, Mendeleyev University of Chemical Technology, and Spark Plasma Sintering Russian Federation; D. Vouagner, D. De Ligny, B. Champagnon, LPCML, France M. Hubert*, Université de Rennes 1, France; G. Delaizir, Groupe d’Etudes des Transparent glass-ceramics with second order non linear optical prop- Matériaux Hétérogènes (GEMH), Centre Européen de la Céramique, France; X. erties can be elaborated through bulk precipitation of non-centrosy- Zhang, L. Calvez, Université de Rennes 1, France metric nano-crystallites. The 25La2O-25B2O3-50GeO2 glass composi- Chalcogenide glasses are widely used for infrared applications. The tion seems promising to provide transparent glass-ceramic due to the presence of oxygen during their synthesis process leads to the presence very weak difference of refractive index between the crystalline phase of detrimental absorption bands on the transmission spectra. To avoid and the glassy matrix. The surface crystallization of this glass composi- this phenomenon, chalcogenide glasses are synthesized using expensive tion was studied in-situ by SEM, Raman and X-Ray Diffraction. Con- and single use silica tubes sealed under vacuum. The low thermal con- sidering the results, both bulk and surface crystallization have been de- ductivity of silica also limits the quenching rate, and thus the size of the veloped. For each sample, the surface crystalline layer was removed by samples produced. In this study, we present a new way to synthesize polishing allowing the study of crystalline particles size and orientation chalcogenide glasses without use of silica tubes. An amorphous powder in bulk samples. Linear and nonlinear optical properties were then in- is produced by mechanical milling of the raw starting elements in stoe- vestigated in crystallized samples. Micro-Raman and micro-Second chiometric proportion and then sintered around Tg using Spark Plasma Harmonic Generation have also been performed and shown a particular Sintering technique. Bulk glasses and glass-ceramics with higher dimen- distribution of crystalline particle in demixing areas. sions and transparent in the infrared have been produced. This process paves the way for a novel approach for production of chalcogenide glasses and glass-ceramics at a lower cost

64 2012 Glass & Optical Materials Division Annual Meeting Abstracts

5:20 PM 8:40 AM (GOMD-SII-044-2012) Crystallization studies of ZBLAN glasses by (GOMD-SII-002-2012) Rare-earth Doped Glasses and Fibers for 2 DSC and in situ TEM Micron Laser L. Leonard, C. Foerster, UTSI, USA; C. Alvarez*, Northwestern University, USA; S. Jiang*, AdValue Photonics Inc, USA R. Weber, Materials Development Inc., USA; A. Petford-Long, Argonne National Thulium-doped fiber laser near 2 micron is of great interest because it Laboratory, USA; J. Johnson, UTSI, USA; S. Schweizer, Fraunhofer Center for combines high efficiency, high output power and retina safety together. Silicon Photovoltaics, Germany Thulium exhibits a unique feature that the slope efficiency can exceed Rare-earth (RE) doped fluorochlorozirconate-based glasses have been the Stokes limit. In this presentation, we mainly focus on highly Tm- developed as a spectral converter for applications in medical diagnostics doped silicate glass fibers. The Tm-doping concentrations varies from and photovoltaics. As well as doping with Eu2+ to produce strong blue 4wt% to 7wt%. Rod-in-tube technique was used to fabricate single- fluorescence upon x-ray or ultraviolet excitation the glasses were addi- mode double glass-cladding fibers. Fiber drawing was carried out on tionally doped with chlorine (by adding BaCl2 to the melt). Post heat our in-house fiber drawing tower, which is optimized for gain fiber fab- treatment of the glasses leads to nucleation and growth of BaCl2 rication. Fibers with a variety of configurations were fabricated for laser nanoparticles within the glass matrix. Upon the thermal treatment efficiency characterization and for demonstrations of single frequency 2 some of the RE ions are incorporated into the particles leading to en- micron fiber laser, Q-switched 2 micron fiber laser, and mode-locked hanced light output. The RE doping significantly affects the BaCl2 crys- fiber laser. tallization, the crystal structure and the particle size. In this work results on differential scanning calorimetry, x-ray diffraction, fluorescence 9:00 AM spectroscopy and in situ transmission electron microscopy investiga- (GOMD-SII-003-2012) Two-dimensional Photonic Crystals on tions will be presented. Hybrid Quantum Dots/ Chalcogenide Thin Films and their Emission Properties 5:40 PM P. Lin*, N. Patel, V. Singh, L. Kimerling, A. Agarwal, J. Scherer, M. Bawendi, MIT, (GOMD-SII-045-2012) Novel Synthesis of Transparent Rare Earth USA; J. Musgraves, K. Richardson, Clemson University, USA; C. Dimas, Masdar Doped Aluminum Oxide Institute of Science and Technology, United Arab Emirates R. J. Pavlacka*, C. Cooper, T. Sanamyan, M. Dubinskiy, G. Gilde, U.S. Army Two dimensional photonics crystals (PhCs) are demonstrated on hybrid Research Laboratory, USA thin films composed of quantum dots (QDs) and chalcogenide glass In this work we report on the synthesis of erbium doped transparent (ChG). Both QD and ChG are first dissolved in amine solvent and then aluminum oxide ceramics with extremely fine microstructures (< 400 spin-coated on silicon wafers. The coated films are annealed to remove nm grain size). This was achieved using a set of novel powder synthesis the residual solvent. The PhC structure is then patterned on the hybrid and sintering approaches designed to enhance the stability of erbium films using dual beam focused ion beam (FIB). The QD/ChG hybrid lattice incorporation and enable full densification with limited grain films have photoluminescence (PL) at near infrared. With PhC struc- growth. Potential mechanisms for erbium incorporation, as well as exci- tures on the hybrid films, strongly enhanced surface PL is calculated tation and absorption spectra will be discussed. compared to unpatterned films. Simulation of the PL intensities is per- formed by two dimensional finite difference time domains (FDTD) cal- culation. We find the surface PL intensities are determined by the struc- Thursday, May 24, 2012 ture parameters of PhCs. Hence, QD/ChG films with PhCs are potential light sources for three dimensional photonic circuits. Symposium II: Optical Materials & Devices 9:20 AM (GOMD-SII-004-2012) GeSbS waveguides on Er-TeO2 for optical Session 1: Active Optical Materials amplication Room: Salon B M. Vanhoutte*, MIT, USA; H. Lin, University of Delaware, USA; V. Singh, P. Lin, Session Chair: Shibin Jiang, AdValue Photonics Inc MIT, USA; J. Hu, University of Delaware, USA; A. Agarwal, L. C. Kimerling, MIT, USA 8:00 AM Er-doped TeO2 has proven to be an excellent light emitter at 1.5μm, (GOMD-SII-001-2012) Ceramic Laser Technology: History and which is the preferred wavelength for optical communications. We in- Status (Invited) vestigate the use of GeSbS strip waveguides on top of Er-TeO2 for the J. S. Sanghera*, W. Kim, G. Villalobos, L. B. Shaw, C. Baker, Naval Research Lab, development of an at 1.5μm. Er-TeO2 thin films are USA; M. Hunt, URF, USA; B. Sadowski, R. Miklos, Sotera Defense Solutions, deposited on SiO2 by means of RF magnetron co-sputtering of Er and USA; J. Frantz, Naval Research Lab, USA; I. D. Aggarwal, Sotera Defense TeO2 in an Ar/O2 plasma. Upon free-space excitation with 488nm light, Solutions, USA the Er-TeO2 thin films show strong, broadband (FWHM = 65nm) pho- The field of transparent ceramic laser materials has seen significant im- toluminescence centered at 1.54μm. Decay lifetimes are as long as 4ms, provements since the first demonstration of lasing in Dy3+:CaF2 ce- which indicates a high photoluminescence quantum yield. GeSbS strip ramic in 1964. Considerable effort has gone into powder synthesis and waveguides are fabricated on top of the Er-TeO2 thin films by means of purification, along with better sintering processes. Consequently lasing thermal evaporation of GeSbS and subsequent lift-off. We achieved low- has been demonstrated in halide, oxide and chalcogenide ceramics. The loss (5.6dB/cm) waveguides on top of TeO2 films without Er, and we use efficiency and laser output power has been steadily increasing, especially pump-probe measurements to investigate the possibility of gain. In con- within the last decade, to the point where 100 KW output power has clusion, we demonstrate that GeSbS waveguides on Er-TeO2 are a now been demonstrated using Nd:YAG. In addition, the ceramic tech- promising candidate for the creation of an optical amplifier at 1.5μm. nology enables fabrication of novel architectures, including undoped claddings and graded doping profiles, as well as high doping levels which are not very practical using traditional single crystal technology. I will present an overview of the history and current status of ceramic laser technology, including recent developments from the author’s lab.

2012 Glass & Optical Materials Division Annual Meeting 65 Abstracts

9:40 AM 11:00 AM (GOMD-SII-005-2012) Structure and nonlinear optical properties of (GOMD-SII-046-2012) Bismuth-doped glass optical fibers: a tellurite thin film glasses challenging active optical material for near IR region R. Morea, D. Munoz-Martin, J. Gonzalo*, J. Fernandez-Navarro, J. Solis, CSIC, E. Dianov*, Fiber Optis Research Center, Russian Federation Spain; G. Jose, A. Jha, University of Leeds, United Kingdom; C. Domingo, CSIC, It has been shown recently that Bi-doped glasses and optical fibers are a Spain very promising active laser medium. Various types of Bi-doped optical We report the third order nonlinear optical response of fibers have been developed and used for the construction of Bi-doped thin films produced by Pulsed Laser Deposition from glasses of the fiber lasers and optical amplifiers. This talk will address the recent re-

TeO 2-WO3-PbO system in a broad range of compositions. Structural sults on the luminescence properties of various Bi-doped optical fibers characterisation of the films was conducted through ion beam analysis and on the development of Bi-doped fiber lasers and optical amplifiers techniques, XPS and Raman spectroscopy. UV-VIS spectroscopy and in extended transmission bands. spectroscopic ellipsometry were used for linear optical characterization. The third order nonlinear optical susceptibility (χ(3)) at 1.3 μm was measured using degenerate four wave mixing (DFWM) technique. Film Symposium III: Cross-Cutting Topics glasses present large linear refractive index (n>2) with reduced absorp- tion (k<10-4) in the visible and IR ranges, while χ(3) is in the range of Session 2: NMR Studies of the Structure of Glass 4 -12 ~10 esu, which is and order of magnitude larger than the value meas- Room: Grand Suites II & III ured for bulk glasses. This increase is correlated to the structural differ- Session Chair: Hellmut Eckert, WWU Münster ences observed in the film with respect to bulk glasses due to the relative enrichment of the heavy metal concentration and increase of the non 8:00 AM bridging oxygen fraction. (GOMD-SIII-026-2012) Q3 site variations in a mixed 10:20 AM potassium/magnesium glass using Magic-Angle Flipping (MAF) NMR (Invited) (GOMD-SII-006-2012) Borogermanate glasses with high rare earth J. H. Baltisberger*, Berea College, USA; E. G. Keeler, D. C. Kaseman, K. J. oxide content: from optical quality to nanostructuring Sanders, P. J. Grandinetti, The Ohio State University, USA V. Sigaev*, V. Savinkov, N. Golubev, S. Lotarev, E. Lopatina, D. Mendeleyev University of Chemical Technology of Russia, Russian Federation In this presentation we will show new data on cation clustering in mixed potassium and magnesium tetra-silicate glasses. We examined the de- Possibility of obtaining of optically homogeneous Ln2O3-B2O3-GeO2 gree of modifier cation clustering in a range of glass compositions with (Ln = La, Yb) glasses and of those glasses with a modified structure is 29Si magic-angle flipping (MAF) NMR at natural abundance. We used discussed. We report fabrication of colorless optical borogermanate CPMG echo train acquisition to enhance sensitivity due to the low iso- glasses containing more than 30 mol.% Tb2O3 and possessing very high topic abundance and NMR frequency. We found that doping the sam- Verdet constant (0.385 arc min/ cm Oe at 632.8 nm wavelength), Er,Yb- ples with Cu(II) reduced the relaxation delay enough to allow a full containing glasses possessing the broadband (about 90 nm) lumines- MAF spectrum to be acquired in 4 to 6 days. In agreement with the pre- cence at 1530 nm in the NIR range and also glasses with high Sm2O3 vious 17O study of this glass by Farnan and coworkers, these glasses ap- content efficiently absorbing radiation around a lasing line of the pear to have significant ordering where the cations cluster as either pure Nd:YAG laser. Gradient heat-treatment and laser irradiation of lan- potassium regions or mixed regions. thanum borogermanate glasses doped by different activators allow modifying of the bulk structure or the surface one at nano-, micro- and 8:40 AM macroscale and fabricating materials with a high second-order optical (GOMD-SIII-027-2012) NMR Studies of Nuclear Waste Materials: nonlinearity, quasi-periodical composite glass/ferroelectric structures Cutting Through Compositional and Morphological Complexity and substantially textured glass-ceramics. (Invited) 10:40 AM S. Kroeker*, University of Manitoba, Canada (GOMD-SII-007-2012) A Non-Equilibrium Processing Route for Nuclear waste disposal demands durable wasteforms capable of retain- Active Optical Waveguides ing radioactive ions. Borosilicate glasses are widely used, but waste load- G. Bernard, W. Wu, J. Padalis, J. Kieffer*, Univ Michigan, USA ing is limited by the solubility of certain ions. Due to the large number of components in waste streams, precipitated phases are complex and In Er3+-doped Waveguide Amplifiers (EDWAs) optical signals are vary in composition and structure. Multinuclear NMR is used to iden- boosted through stimulated photon emissions from this rare-earth ele- tify and quantify devitrification products in heterogeneous model nu- ment. However, the low solubility of Er3+ in silica glasses causes ag- clear waste materials ranging from 5 to 20 oxide components. Paramag- glomeration, which in turn results in non-radiative decay of excitations netic ions complicate NMR analysis but also provide information about and low device efficiency. To eliminate this loss mechanism, better spa- species partitioning. High-temperature magic-angle spinning NMR is tial dispersion of Er3+ must be achieved. To this end we devised a fabri- used to characterize phase transformations and reactions amongst de- cation route for EDWAs away from thermodynamic equilibrium in two vitrification products during cooling, under conditions mimicking respects: through into sol-gel derived low-density sil- those of industrial processes. Double-resonance NMR methods are used ica structures. The resulting spatial distribution of Er3+ is analyzed to study phase separation in glasses which have not crystallized, reveal- using Rutherford backscattering and secondary ion mass spectrometry. ing pre-nucleation sites rich in high field-strength cations. The spectra so measured are analyzed using a ion stopping range simu- lation code we specifically developed for porous structures that exhibit 9:20 AM fractal geometries. The details of the fabrication method, the data analy- (GOMD-SIII-028-2012) Structural basis of durability in a transition sis procedure, and the potential for fabrication of high-efficiency silica metal phosphate glass (Invited) based EDWAs will be discussed. S. Chenu, U. Werner-Zwanziger, C. Calahoo, J. Zwanziger*, Dalhousie University, Canada Alkali phosphate glasses are quite reactive with water but transition metal phosphates can be strikingly durable. We have developed a sodium aluminum phosphate glass that includes zinc and niobium oxide and shows very high durability. Through a series of NMR and Raman experiments we have been able to develop a detailed structural

66 2012 Glass & Optical Materials Division Annual Meeting Abstracts model of this glass and then use it to rationalize the durability. In the Symposium IV: Festschrift to the Glass talk I will outline our model and, time permitting, our computational approaches to Raman and NMR spectra. Research Career of Prof. Delbert E. Day Session 2: NMR Studies of the Structure of Glass 5 Session 3: DTA and DSC Methods for Glass Room: Grand Suites II & III Crystallization Study Session Chair: Annie Pradel, Université Montpellier 2 Room: Salons E, F, & G 10:20 AM Session Chair: Edgar Zanotto, UFSCar (GOMD-SIII-029-2012) Structure of Chalcogenide glasses by 8:00 AM Multinuclear NMR spectroscopy (Invited) (GOMD-SIV-023-2012) On DTA and DSC methods for glass S. Sen*, University of California, Davis, USA crystallization study Chalcogenide glasses are of wide-ranging importance in a variety of E. D. Zanotto*, UFSCar, Brazil technological applications in the areas of photonics, telecommunica- Several methods based on DTA or DSC experiments have been pro- tion, environmental sensing and data storage. These chalcogenides be- posed for the study of glass crystallization kinetics. Prof. Day has made long primarily to the Ge-As-Se-S-Te system with minor metallic com- important contributions to the use of thermal analytical techniques to ponents such as Ga, P, Sb, In and La and many of these constituent characterize glass crystallization kinetics. Since thermal analysis equip- elements are typically not amenable to high-resolution solid-state ment is handy, require only a small amount of sample, and they are NMR. However, in the last two decades, an increasing number of studies much faster than the conventional microscopy and XRD methods, have begun to successfully employ NMR spectroscopic techniques to DTA/DSC techniques have gained wide acceptance. In this symposium obtain unique information on short range order and connectivity in we intend to carry out a serious brainstorming aiming at clarifying what chalcogenide glasses and liquids. Recent literature on this topic will be sort of relevant quantitative information one can get from them. For in- reviewed and the latest work from our laboratory on the applications of stance, is it really possible to determine reliable values of crystal nucle- 31P, 71Ga, 73Ge, 75As, 77Se, 125Te NMR and 75As NQR spectroscopy ation rates, growth rates, overall crystallization kinetics, critical cooling in the structural studies of a wide variety of amorphous and crystalline rates, glass stability parameters, activation enthalpies, solidus and liq- chalcogenides will be discussed. uidus by DTA or DSC? In this introductory talk we will dwell on these 11:00 AM problems and then will let invited speakers to elucidate their most re- cent views on this key issue. (GOMD-SIII-030-2012) A Comparison of 10B, 11B NMR and NQR in Borates (Invited) 8:20 AM S. Feller*, D. Crist, V. Khristenko, K. Tholen, N. Barnes, E. Troendle, M. (GOMD-SIV-024-2012) DTA/DSC Methods for Studying Glass Affatigato, Coe College, USA; D. Holland, T. Kemp, M. E. Smith, University of Formation and crystallization Behavior of Melts and Glasses Warwick, United Kingdom (Invited) Recently, using pulse techniques and a field step magnet, we have been C. S. Ray*, Missouri S&T, USA measuring the full six transition powder patterns for 10B (I = 3) NMR A review of several experimental methods that were developed at the in borate glasses and crystals. We have been determining precise value Missouri S&T using DTA/DSC for studying glass formation and crystal- for the quadrupole coupling constant and asymmetry parameter and lization behavior of melts and glasses is presented. Notable properties their distribution widths in a series of differing intermediate range that help describe the overall crystallization behavior and will be em- structures in these borates. In this review talk we compare these results phasized in this presentation include (1) critical cooling rate for glass to earlier pure NQR data, using both 10B and 11B resonances, from the formation, (2) rates for nucleation and crystal growth and, (3) mecha- Bray group as well as yet earlier wide-line NMR results using just two of nism of the crystallization (surface/bulk) process. The experimental the six transitions. Comparisons to 11B DOR NMR results will also be methods that are traditionally used to measure these properties are presented. An anomaly in the reported distribution widths will be dis- often time consuming, tedious, and sometimes difficult to perform due cussed as well as trends correlated with changing ring structures and the to unfavorable materials characteristics. Compared to the traditional newly obtained quadrupole parameters. This work supported by NSF methods these DTA methods are less time-consuming and straight for- DMR-0904615. ward, require small amounts of sample and does not require any special 10:20 AM sample processing procedures like cutting, grinding, or polishing, while produce results with accuracy similar to those produced by the tradi- (GOMD-SIII-031-2012) NMR and Industrial Glass Research tional methods. (Invited) R. Youngman*, Corning Incorporated, USA 9:00 AM NMR spectroscopy has clearly benefitted research of glasses, in particu- (GOMD-SIV-025-2012) Analysis of Crystallization Kinetics (Invited) lar those having relatively simple compositions based on B, Si, Al and K. F. Kelton*, Washington University, USA other NMR friendly nuclei. Such model systems continue to be critical Differential scanning calorimetry (DSC) methods are frequently used to in growing our understanding of structure/property relations. Com- measure the kinetics of crystallization during glass devitrification. A re- mercially interesting glasses are typically more complex, containing nu- alistic computer model that includes time-dependent nucleation and merous network formers, modifiers and other additives. We will high- cluster size dependent growth rates is used to assess the validity of some light efforts in which even simple NMR approaches can provide commonly used techniques for the analysis of this kinetic data when the invaluable understanding, ranging from thermal history effects to im- glass and the crystallizing phase have the same composition. These stud- portant additives and ultimately to exploring new compositions and ies demonstrate that the commonly-used Kissinger analysis provides an nuclei in which to characterize with NMR. estimate of the activation energy for growth when the nucleation and growth regimes are widely separated, but is invalid otherwise. Modeling based on a coupled-flux model of nucleation for cases when the glass and crystal do not have the same composition demonstrates that the time-dependent nucleation rates can be significantly different from ex- pectations based on the classical theory of nucleation.

2012 Glass & Optical Materials Division Annual Meeting 67 Abstracts

9:40 AM 11:00 AM (GOMD-SIV-026-2012) Crystal growth rates in glasses determined (GOMD-SIV-029-2012) Crystallization of phosphate glasses doped by a single differential scanning calorimetry run by heavy metal oxides studied by thermoanalytical and spectroscopic R. M. Reis*, Federal University of Sao Carlos, Brazil; V. M. Fokin, S.I. Vavilov’s methods State Optical Institute, Russian Federation; E. D. Zanotto, Federal University of L. Koudelka*, I. Rösslerova, Z. Cernosek, P. Mosner, University of Pardubice, Sao Carlos, Brazil Czech Republic We describe a simple and precise technique capable of determining Crystallization of PbO-MoO3-P2O5 and PbO-WO3-P2O5 ternary crystal growth rates, U(T), in a fairly wide temperature range using a glasses was studied in two compositional series in each system. Thermal single DSC run. The method is based on using 50-200μm thick tile- properties were studied by DTA and dilatometry. From these studies shaped samples with rough surfaces so that crystal growth is one-di- glass-forming ability was evaluated and compositional dependences of mensional in the whole crystallization process. Growth rates are calcu- characteristic temperatures in the studied glass series were obtained. lated by U(T)=DSC(T)*L*q, where DSC(T) is the DSC crystallization Crystallization products of annealed glass samples were investigated by peak curve, normalized so that its area is unity, L is half the sample X-ray diffraction and Raman spectroscopy. X-ray diffraction analysis of thickness and q the heating rate. This method has been tested for differ- crystallized glasses revealed the formation of several crystalline phos- ent L and q for three glasses: stoichiometric lithium disilicate and diop- phate compounds and in the samples with a high MoO3 and WO3 con- side, and a non-stoichiometric lithium calcium silicate glass (LCS). Re- tent also the formation of crystalline compounds of Pb(MoO2)2(PO4)2 sults have been compared to literature data and optical microscopy and Pb(WO2)2(PO4)2, respectively. Raman spectra of crystallized sam- measurements. U(T) for the LCS glass is accurate within an order of ples confirmed the results of X-ray diffraction measurements and pro- magnitude due to the non-stoichiometric nature of its crystallization vided also information on the thermal stability of glasses and formation and difficulties in baseline removal, but show excellent agreement for of glass-crystalline phases by the annealing of glasses. both stoichiometric glasses. 11:20 AM 10:20 AM (GOMD-SIV-030-2012) Crystallization Kinetics of Lithium (GOMD-SIV-027-2012) Characterisation of the Crystallisation Aluinosilicate (LAS) glasses Behaviour of Bioactive Glasses with view to Preventing Q. Fu*, R. L. Stewart, J. T. Kohli, Corning Incorporated, USA Crystallisation Using Non Isothermal DTA/DSC Methods A study of the crystallization kinetics was conducted on lithium alumi- R. G. Hill*, A. Al-Noaman, Queen Mary University of London, United Kingdom nosilicate (LAS) glasses containing different amounts of titanium oxide. Glasses were heat treated by isothermally holding at different tempera- Crystallisation of bioactive glasses generally reduces their tures between 700-900°C. Kinetic parameters such as activation energy solubility/bioactivity and inhibits viscous flow sintering, which is im- (Ea) and Avrami constant (n) were determined using differential scan- portant in the fabrication of coatings and scaffolds. The silica content of ning calorimetry (DSC) on isothermally treated glass. Crystalline phases the bioactive glass has often been raised, but this increases the connec- formed in the heat-treated glass-ceramics were detected using X-ray dif- tivity and reduces the bioactivity. This paper will show how non isother- fraction (XRD), and the morphologies of the formed crystals were ob- mal DSC/DTA methods originally pioneered by Delbert Day to deter- served using scanning electron microscropy (SEM). The effects of the mine activation energies for crystallisation can be extended as a nucleating agent (TiO2) on the crystallization kinetics and microstruc- characterisation tool to optimise bioactive glass compositions for vis- tural changes of the resultant glass-ceramics are investigated. cous flow sintering. This strategy has been pursued for multicompoent bioactive glasses based on SiO2-P2O5-CaO-SrO-MgO-ZnO-CoO- 11:40 AM Na2O-K2O. It is found that incorporating small quantities of MgO and (GOMD-SIV-031-2012) Chemical reactivity during HLW glass ZnO particularly inhibit crystallisation and facilitate viscous flow sin- synthesis:impact of Al2O3, MoO3 tering. A. Monteiro*, S. Schuller, M. Toplis, R. Podor, J. Ravaux, N. Clavier, T. Charpentier, CEA, France 10:40 AM (GOMD-SIV-028-2012) Crystallization behavior of bioactive glasses In the French industrial HLW vitrification process, a complex mixture using differential thermal analysis of oxides and nitrates resulting from calcination of actinides and fission product solutions (calcine) is vitrified by chemical reaction with an alu- J. Massera*, S. Fagerlund, L. Hupa, M. Hupa, Åbo Akademi, Finland mino-borosilicate glass frit. As such, formation of the final glass involves Detailed understanding of glass crystallization is important for the a complex succession of intermediate steps, including impregnation,sat- manufacture of novel glass-ceramics and related products via thermal uration, crystallization and dissolution. For simplified glass composi- treatments in particular for medical applications. Products manufac- tions enriched in Al2O3 and MoO3, nepheline or molybdates may be tured at high temperature from the bioactive glasses 45S5, S53P4, 13-93 formed during glass synthesis. Some of them could affect the glass dura- and 1-98 have been studied extensively in vitro and in vivo. However, lit- bility, so it is essential to determine their crystallization conditions in tle effort has been devoted to understand the crystallization mecha- order to avoid them in the final glass. DTA-TGA, ESEM, 29Si,11B,27Al nisms of these glasses. Differential thermal analysis was used to charac- MAS RMN and Raman spectroscopy experiments shown that chemical terize the crystallization kinetics in terms of the activation energy, reactivity kinetic is influenced by the nature of crystalline phases in the Johnson-Mehl-Avrami exponent, and nucleation-like curves. Non- calcine. The stability of crystalline phases in the interfacial reactive zone isothermal experimental procedure was applied to validate the JMA between glass frit and calcine is controlled by a local saturation in Na2O, model. The liquidus temperatures given by the thermograms were com- Al2O3, MoO3. pared with the values suggested by the observations from isothermal ex- periments and fiber drawing processes. The applicability of thermal analysis to estimate hot working and sintering parameters for bioactive glasses will be discussed in detail.

68 2012 Glass & Optical Materials Division Annual Meeting Author Index

* Denotes Presenter

A Boolchand, P...... 25, 46, 53 Davis, M.J.* ...... 57 Abell, J...... 44 Boolchand, P.* ...... 53 Day, D.E...... 33, 35, 42, 51 Abouraddy, A.F...... 39, 49 Bornstein, K.* ...... 30 Day, T...... 51 Abouraddy, A.F.* ...... 49 Bozdogan, O...... 47 de Camargo, A...... 64 Achanta, V...... 40 Bradt, R.C.* ...... 37 De Ligny, D...... 64 Adamietz, F...... 25, 37, 64 Bragatto, C.B.* ...... 35 de Ligny, D...... 42, 61 Adjei-Acheamfour, M...... 40, 63 Brandt, H...... 32 de Lima, F...... 64 Affatigato, M...... 26, 47, 60, 67 Brennan, C...... 36 Deenamma, V...... 43 Affatigato, M.* ...... 27 Broglia, G...... 50 Delaizir, G...... 64 Agarwal, A...... 45, 65 Brow, R...... 36, 41, 62 Delevoye, L...... 29, 34 Agarwal, A.M...... 44 Brow, R.K...... 33, 34, 35, 36, 38, 40, 41, 47 Deschamps, M...... 63 Agarwal, A.M.* ...... 44 Buchheit, E.M.* ...... 36 Deschamps, T...... 42 Aggarwal, I.D...... 65 Bureau, B...... 59 Deters, H...... 64 Ahline, T...... 27 Burger, E...... 57 Deubener, J...... 42 Ahmed, I.* ...... 52 Burov, E...... 50 Dianov, E.* ...... 66 Aitken, B...... 25, 34, 53, 59 Busch, R.* ...... 54 Dierolf, V...... 31, 39 Aitken, B.* ...... 58 Bychkov, E...... 26 Dijkhuis, J.I...... 31 Akkopru Akgun, B...... 40 Byrn, S.R...... 30 Dillmann, P...... 57 Akrobetu, R...... 39 Dimas, C...... 45, 65 Alderman, O...... 62 C Diwan, M...... 31 Allan, D.C...... 60 Cabral, A.A.* ...... 41 Domingo, C...... 66 Al-Noaman, A...... 68 Cadars, S...... 63 Dong, S...... 30 Alvarez, C.* ...... 65 Cai, Y...... 45 Dongol, R...... 27 Amoroso, J.W...... 32 Calahoo, C...... 66 Dongol, R.* ...... 31 Amoureux, J...... 34 Calvez, L...... 26, 64 Drabold, D...... 36 Angeli, F...... 61 Camacho-Aguilera, R...... 45 Du, J...... 34, 48 Anheier, N.* ...... 44 Canedy, C.L...... 44 Du, J.* ...... 29 Arai, Y.* ...... 62 Cardinal, T...... 25 Dubinskiy, M...... 65 Arnold, C...... 32 Carvalho, A.M...... 41 Dupree, R...... 62 Arnold, C.B.* ...... 33, 44 Casasola, R...... 41 Durucan, C...... 40 Ayrinhac, S...... 64 Casse, B.D.F...... 44 Durupthy, O...... 50 Caulier, O...... 26 Dussauze, M...... 25, 37, 59, 64 B Célarié, F...... 53 Bag, S...... 28 Cernosek, Z...... 68 E Bagga, R.* ...... 40 Chakraborty, S.* ...... 25 Ebert, W.* ...... 55 Bajpai, R.K...... 61 Champagnon, B...... 64 Ebert, W.L...... 61 Baker, B.* ...... 26 Champagnon, B.* ...... 42, 50 Eckert, H...... 63 Baker, C...... 65 Chanéac, C...... 50 Eckert, H.* ...... 45, 58, 64 Balda, R...... 39 Changstrom, J...... 51 Edwards, T...... 46 Ballato, J.* ...... 49, 50 Charpentier, T...... 61, 68 Ellison, A.J...... 26, 56 Baltisberger, J.H...... 37 Chauhan, D.S...... 33, 34, 52 Epping, J...... 45 Baltisberger, J.H.* ...... 66 Chen, G...... 36 Erdmann, R.G...... 60 Banaei, E...... 49 Chen, G.* ...... 30 Erdmann, R.G.* ...... 60 Banba, T...... 38 Chen, P...... 53 Ertap, H...... 47 Barboux, P...... 61 Cheng, X.* ...... 36 Barnes, N...... 67 Chenu, S...... 66 F Barney, E...... 62 Cherry, B...... 30 Faeghi nia, A.* ...... 39 Barta, B.* ...... 64 Chrisey, D.B...... 27 Fagerlund, S...... 68 Barthel, E...... 42 Christensen, R...... 41, 63 Falconieri, M.M...... 40 Bauchy, M...... 48 Christensen, R.* ...... 27, 47 Falk, M...... 52 Bauchy, M.* ...... 57 Christensesn, R.B...... 51 Fargin, E...... 37, 64 Bauer, U...... 42 Chu, T.G...... 42 Faske, S...... 45 Bawendi, M...... 65 Chun, J...... 28, 38 Fayon, F...... 63 Beal, R...... 32 ChunTeng, L.* ...... 39 Feller, S...... 26, 27, 47, 60 Beaudoux, X...... 55 Clark, A.N.* ...... 42 Feller, S.* ...... 67 Beckman, S.P...... 59 Clark, S...... 53 Fernandez, J...... 39 Behrends, F...... 45, 58 Clavier, N...... 68 Fernandez-Navarro, J...... 39, 66 Behrens, H...... 42 Contini, V...... 40 Ferrand, K.* ...... 61 Ben Amara, O...... 50 Cooper, C...... 65 Ferraro, P.A.* ...... 64 Benmore, C...... 29, 41 Cormack, A...... 37 Ferreira, J...... 40 Benmore, C.J...... 30, 46 Cormack, A.N...... 43 Ferreira, J.M...... 28, 52 Benmore, C.J.* ...... 30 Cormier, L.* ...... 46 Ferrer, A...... 26 Bernacki, B...... 44 Cornelius, L.K...... 26 Fletcher, L.B...... 34 Bernard, G...... 66 Courtens, E...... 56 Flikkema, E...... 43 Berthelot, A...... 50 Crawford, C.L.* ...... 61 Florian, P...... 63 Bertry, L...... 50 Crist, D...... 67 Foerster, C...... 65 Bewley, W.W...... 44 Crum, J...... 29, 57 Fokin, V.M...... 68 Bhosle, S...... 53 Currie, S...... 58 Foret, M...... 56, 64 Bialecka, K...... 32 Forler, N...... 34 Bischoff, C...... 54 D Fortner, J.A.* ...... 61 Bischoff, C.* ...... 25, 59 Dahal, B...... 26 Fox, K.M...... 32 Blouin, V.Y...... 60 Dalba, G...... 27 Foy, P...... 49, 50 Böhmer, R...... 40 Danto, S...... 59 Franta, B...... 27 Böhmer, R.* ...... 63 Dargaud, O...... 46 Frantz, J...... 65 Bond, K.* ...... 32 Dash, P.* ...... 47 Fryxell, G.E...... 28

2011 Glass & Optical Materials Division Annual Meeting 69 Author Index

Fu, Q.* ...... 68 Hrma, P...... 33, 38 King, E.A...... 60 Furman, E...... 47 Hsiwen, Y...... 39 King, E.A.* ...... 60 Hsu, J.* ...... 33 Knorr, B...... 39 G Hu, J...... 32, 33, 44, 45, 65 Knorr, B.* ...... 39 Galbraith, J.* ...... 59 Huang, L...... 42, 44 Kob, W.* ...... 47 Gallo, L.* ...... 35 Huang, L.* ...... 42 Koch, R.J.* ...... 25 Gao, Y...... 53 Huang, P.* ...... 38 Kohli, J.T...... 68 Gaudio, S.J.* ...... 54 Hubert, M.* ...... 64 Kokou, L...... 29 George, J.* ...... 36, 62 Hunt, M...... 65 Kolan, K.* ...... 42 Ghussn, L...... 35, 45 Hupa, L...... 68 Komatsu, T.* ...... 27 Ghussn, L.* ...... 40 Hupa, L.* ...... 52 Kono, Y...... 38 Giammarco, J...... 44 Hupa, M...... 68 Koontz, E.* ...... 60 Gilbert, M.* ...... 36 Kordesch, M...... 36 Gilde, G...... 65 I Korngruen, M.* ...... 37 Gin, S...... 61 Icenhower, J.* ...... 55 Kotakoski, J...... 38 Gin, S.* ...... 55, 57 Im, C...... 62 Koudelka, L.* ...... 68 Glebov, L.B...... 56 Inaba, S.* ...... 30 Kovalskyy, A...... 36, 37 Glebova, L...... 56 Inoue, H...... 28 Kovalskyy, A.* ...... 58 Goel, A.* ...... 28, 33, 52 Inoue, H.* ...... 46 Kowal, T...... 52 Goetschius, K...... 36 Ispas, S...... 47 Kozdras, A...... 54 Goetschius, K.* ...... 35 Ito, S...... 30 Kozmidis-Petrovic, A.F.* ...... 48 Golovchak, R...... 54 Iwadate, Y...... 32 Krasheninnikov, A...... 38 Golovchak, R.* ...... 57 Kreski, P.K.* ...... 37, 43 Golubev, N...... 27, 66 J Kroeker, S...... 26 Gonzalo, J.* ...... 39, 66 Jacobsen, S.D...... 42 Kroeker, S.* ...... 66 Goodwin, F...... 61 Jain, H...... 31, 39, 40, 41, 50, 56, 58 Krol, D.M...... 31 Goyal, A...... 40 Jain, H.* ...... 52, 54 Krol, D.M.* ...... 34 Grandinetti, P.J...... 37, 66 Jaque, D...... 26 Krümpelmann, J.* ...... 50 Grant, D...... 52 Jegou, C...... 55 Kurasch, S...... 38 Gray, S...... 53 Jensen, K.F.* ...... 32, 62 Kurkjian, C.R...... 47 Greaves, G.N...... 43 Jha, A...... 66 Kwon, W...... 54 Greaves, N.* ...... 54 Jiang, H...... 41 Gribble, N...... 62 Jiang, S.* ...... 65 L Grisenti, R...... 27 JianShian, L...... 39 Labadie, L...... 44 Grobnic, D...... 26 Jing, Z...... 38 Lacroix, R...... 42 Guerette, M...... 42 Johnson, C...... 53 Lanagan, M.T...... 47 Guerette, M.* ...... 42 Johnson, J...... 65 Laorodphan, N...... 62 Guery, G.* ...... 25 Johnson, J.* ...... 53 Larink, D...... 58, 63 Guin, J...... 62 Jollivet, P...... 61 Laurent, D...... 40 Gulbiten, O.* ...... 35 Jose, G...... 66 Le Coq, D.* ...... 26 Gunapala, E...... 41 Jovari, P...... 59 Le Floch, S...... 42 Gunasekera, K...... 53 Jung, S...... 42 Le Garrec, B...... 37, 64 Gunasekera, K.* ...... 53 Jung, S.B.* ...... 51 Le Roux, S.* ...... 47, 48, 59 Guo, X...... 56 Jurdyc, A...... 50 Lee, J...... 62 Guo, X.* ...... 60 Lee, P.* ...... 38 Gupta, N...... 50 K Lee, S.* ...... 43 Gupta, P...... 39 Kadaksham, A...... 61 Lee, Y...... 54 Kahn, B...... 64 Lemesle, T...... 34 H Kaiser, U...... 38 Lemmens, K...... 61 Habasaki, J.* ...... 50 Kalkan, B...... 53 Leonard, L...... 65 Han, K.* ...... 62 Kamitsos, E.I.* ...... 45 Lepry, W.* ...... 29 Hanggodo, S...... 64 Kana Kana, J.* ...... 32 Lepry, W.C...... 28 Hannon, A...... 29, 62 Kanatzidis, M...... 28 Lesher, C.E...... 42, 54 Harper, T.A.* ...... 36 Kang, Z...... 64 Letz, M...... 48 Harris-Jones, J...... 61 Karabulut, M.* ...... 47 Leu, M...... 42 Harrison, M.* ...... 62 Kaseman, D.C...... 66 Lewis, R...... 30 Hawkins, T...... 49, 50 Kaseman, D.C.* ...... 34 Lezzi, P.J...... 51 Hayden, J.S...... 57 Kassir-Bodon, A...... 42 Li, C.* ...... 46 He, H...... 55 Kaufman, J.J...... 49 Li, W.* ...... 57 He, Y...... 38 Keeler, E.G...... 37, 66 Liezers, M...... 33 Heffner, W.R...... 37 Kelton, K.F.* ...... 67 Lin, H...... 32, 33, 65 Hensley, J.M...... 44 Kemp, T...... 67 Lin, H.* ...... 44 Hiet, J...... 63 Kermouche, G...... 42 Lin, P...... 65 Higa, O...... 37 Kerner, R...... 46 Lin, P.* ...... 45, 65 Hill, R.G.* ...... 51, 68 Khristenko, V...... 67 Lionel, M.* ...... 34 Hilmas, G...... 42 Kieffer, J...... 43 Lipatyev, A...... 27 Hinsch, A...... 32, 62 Kieffer, J.* ...... 66 Liu, H...... 41 Hoeland, W.* ...... 51 Kim, C...... 33 Liu, S.* ...... 41 Hogue, C.L...... 57 Kim, C.S...... 44 Liu, X.* ...... 35 Holland, D...... 67 Kim, D...... 33 Loayza-Aguirre, R...... 32 Holland, D.* ...... 62 Kim, J...... 62 Lopatina, E...... 66 Honma, T...... 27 Kim, M...... 44 Lotarev, S...... 64, 66 Hoppe, U.* ...... 29 Kim, S...... 54 Lotarev, S.* ...... 27 Hosono, H.* ...... 27 Kim, W...... 65 Lower, N.P...... 47 Houet, Y...... 40 Kim, Y.* ...... 54 Loy, D.A.* ...... 29 Hovden, R...... 38 Kimerling, L...... 45, 65 Lu, C...... 44 Hrdina, K...... 26 Kimerling, L.C...... 44, 65 Lu, C.* ...... 32

70 2012 Glass & Optical Materials Division Annual Meeting Author Index

Lubberden, W...... 27 Morris, S...... 49, 50 Prokhorenko, O.A.* ...... 28, 40, 48 Lucas, P...... 35, 60 Mosner, P...... 68 Puls, S...... 45 Lucas, P.* ...... 59 Mountjoy, G.* ...... 43, 48 Lumeau, J.* ...... 56 Mu, R...... 39 Q Luo, H...... 57 Mueller, K.* ...... 55 Qiao, H...... 44 Luzinov, I...... 44 Mueller, K.T...... 55 Mugoni, C.* ...... 41, 50 R M Muller, D...... 38 Raguenet, B...... 58 Ma, L.* ...... 35 Munhollon, T.* ...... 60 Rahaman, M.N...... 35 Maass, P...... 43, 51 Munoz-Martin, D...... 66 Rajbandhari, P...... 34 Maass, P.* ...... 45 Murphy, K.* ...... 55 Rani, N.* ...... 61 Maeda, T.* ...... 38 Musgraves, J...... 33, 65 Rao, A...... 50 Magon, C...... 64 Musgraves, J.* ...... 59 Ravaux, J...... 64, 68 Maldonis, J...... 26 Musgraves, J.D...... 44 Ray, C.S...... 33 Malki, M...... 25, 46 Ray, C.S.* ...... 67 Mamedov, G...... 47 N Rebiscoul, D...... 57 Mamedov, S...... 53 Nadler, J.H...... 64 Reis, R.M...... 45 Mao, A.* ...... 25 Nardou, E...... 50 Reis, R.M.* ...... 68 Mao, Q...... 38 Nasikas, N...... 46 Reis, S.T...... 34 Marasinghe, K.* ...... 41 Navrotsky, A...... 38, 53 Reis, S.T.* ...... 37 Marei, M...... 52 Neeway, J.J...... 56 Rekhson, S.M.* ...... 54 Marple, M...... 54 Neeway, J.J.* ...... 61 Rey, C.A...... 30 Marra, J...... 32 Neff, D...... 57 Rheinberger, V.M...... 51 Marra, J.* ...... 33 Neuville, D...... 63 Ribes, M...... 58 Martel, L...... 63 Newkirk, J.W...... 33 Rice, R...... 49, 50 Martens, R...... 37 Ngai, K.L...... 50 Richardson, K...... 25, 33, 44, 59, 65 Martin, S...... 58, 63 North, J...... 26 Riedel, R...... 38, 53 Martin, S.W...... 25, 59 Novak, J.W...... 59 Riley, B...... 29 Martin, S.W.* ...... 51, 54 Novak, S...... 33 Riley, B.J...... 25, 33 Martinelli, J.R...... 41 Riley, B.J.* ...... 28 Martinet, C...... 42 O Rincón, J...... 41 Marzillier, J...... 52 Oelgoetz, J...... 58 Rinke, M...... 58 Masselin, P...... 26 Ogawa, K...... 27 Ritzberger, C...... 51 Massera, J.* ...... 68 Ogbuu, O...... 33 Robinson, M.J...... 28 Massiot, D.* ...... 63 Ohkubo, T.* ...... 32 Rocca, F...... 27 Massobrio, C...... 47, 53, 59 Ohmori, H...... 38 Rodas, A.D...... 37 Masuno, A...... 46 Olson, G...... 51, 63 Rodrigues, A...... 35 Masuno, A.* ...... 28 Rodrigues, A.M...... 41 Matyas, J...... 29 P Rodriguez, C.P...... 25, 33 Matyas, J.* ...... 28 Padalis, J...... 66 Rodriguez, V...... 25, 37, 64 Mauro, J.C...... 42, 43, 56, 60 Pan, Z.* ...... 39 Roling, B...... 50 Mauro, J.C.* ...... 57 Panczer, G...... 61 Romero, M...... 41 McCloy, J.* ...... 25 Pandey, A.K.* ...... 33 Rosciano, F...... 50 McCloy, J.S...... 33 Pandey, P.C...... 33, 52 Rösslerova, I...... 68 McDonough, C...... 39 Pandey, P.C.* ...... 34 Rosson, R...... 64 McMillen, C...... 49, 50 Pantano, C...... 29, 55 Rouxel, T.* ...... 53, 60 Mear, F...... 34 Pantano, C.G...... 34, 47, 55, 62 Rudd, C.D...... 52 Mellott, N.P.* ...... 40 Papatheodorou, G...... 46 Rufflé, B.* ...... 31, 56, 64 Menguy, N...... 46 Parameswaran, K.M...... 44 Ruiz de la Cruz, A...... 26 Mera, G...... 38, 53 Parise, J.B...... 46 Rupasinghe, M...... 38 Meyer, J...... 38 Parrish, C...... 26 Ryan, J...... 56, 57 Meyer, J.R...... 44 Parsons, A.J...... 52 Ryan, J.* ...... 56 Michaelis, V...... 26 Passlick, C...... 53 Ryan, J.V...... 55, 61 Michel, J...... 45 Pastouret, A...... 50 Rygel, J...... 29 Michelin, A...... 57 Patel, N...... 45, 65 Rygel, J.L.* ...... 34 Micoulaut, M...... 25, 46, 53, 57 Patriarche, G...... 46 Micoulaut, M.* ...... 48, 52 Pavic, L...... 29 S Miehe, G...... 53 Pavlacka, R.J.* ...... 65 Saad, M...... 52 Miguel, A...... 39 Pedesseau, L...... 47 Sabry, M...... 52 Mihailov, S.J...... 26 Pellerin, N...... 63 Sadowski, B...... 65 Miklos, R...... 65 Pérez, J.* ...... 41 Saito, Y...... 46 Mitroshkov, A.V...... 56 Petford-Long, A...... 65 Saiyasombat, C.* ...... 39, 40, 56 Mitsui, S...... 38 Petkov, V...... 48 Sakakura, M...... 31 Miura, K...... 31 Pierce, D.* ...... 38 Sakamaki, T...... 38 Mogus-Milankovic, A.* ...... 29 Pierce, E.* ...... 40, 55 Samaranayake, V.A...... 38 Mohajerani, A.* ...... 31 Pillonnet, A...... 50 San Miguel, A...... 42 Molières, E.* ...... 61 Podhajsky, K...... 60 Sanamyan, T...... 65 Moll, J...... 26 Podila, R...... 50 Sanders, K.J...... 66 Montagne, L...... 29 Podor, R...... 64, 68 Sanders, K.J.* ...... 37 Monteiro, A.* ...... 68 Pokorny, R...... 38 Sanghera, J.S.* ...... 49, 65 Monteiro, A.A...... 25 Pollpeter, B...... 26 Santic, A...... 29 Montorsi, M...... 41, 50 Ponader, C.W.* ...... 26 Sarker, S...... 62 Montouillout, V...... 63 Potter, B...... 32 Savinkov, V...... 66 Moore, L.* ...... 26 Potuzak, M...... 42, 57 Savytskyy, D.* ...... 39 Morea, R...... 39, 66 Pradel, A.* ...... 58 Saxton, S.A...... 56 Morgan, S...... 39 Prakash, A.* ...... 52 Scannell, G...... 42 Morin, E.* ...... 35 Prasai, B.* ...... 36 Scherer, C.* ...... 48

2012 Glass & Optical Materials Division Annual Meeting 71 Author Index

Scherer, D.M...... 44 Strachan, D.M...... 28, 61 Washton, N.M...... 55 Scherer, J...... 65 Striepe, S...... 42 Watanabe, Y...... 28 Schiefelbein, S...... 26 Su, X.* ...... 27 Weber, R...... 46, 53, 65 Schlesinger, M.E...... 33, 35 Sundaram, S...... 32 Weber, R.* ...... 30 Schmid, F...... 48 Sundaram, S.K...... 25, 30, 31 Weber, W...... 30 Schnell, S.* ...... 36 Sundararajan, M...... 30 Weigel, C...... 64 Schreiber, D...... 57 Suzuki, F...... 27 Werner-Zwanziger, U...... 66 Schreiber, D.A...... 56 Swarnakar, A.K.* ...... 51, 63 Widgeon, S.* ...... 38, 53 Schreiber, D.K.* ...... 56 Wilde, J...... 62 Schuch, M...... 43, 51 T Wilhelm, A...... 59 Schuller, K...... 25, 59 Tailor, A.N...... 30 Wilkinson, J...... 33, 44 Schuller, S...... 68 Takada, A.* ...... 47 Windisch, C...... 25 Schweiger, M...... 51 Tan, X...... 55 Windisch, C.F...... 33 Schweiger, M.J...... 33 Tandia, A.* ...... 43 Wondraczek, L.* ...... 63 Schweizer, S...... 53, 65 Tang, D...... 28 Wright, A.C.* ...... 29, 30 Scotchford, C.A...... 52 Tang, Z.* ...... 47 Wu, J...... 35, 63 Sebeck, K.* ...... 43 Tao, G.* ...... 39, 49 Wu, W...... 66 Sellappan, P...... 53 Taylor, L.S...... 30 Sen, S...... 25, 34, 38, 42, 53, 54 Taylor, P...... 51 X Sen, S.* ...... 46, 53, 67 Teisseire, J...... 42 Xiang, Y.* ...... 48 Serbena, F.C.* ...... 45 Teki, R.* ...... 61 Shabahang, S...... 39, 49 Teng, Z...... 39 Y Sharma, G...... 40 Terashima, T.* ...... 30 Yada, C...... 50 Shaw, L.B...... 65 Teulé, F...... 30 Yamagata, C...... 37 Shelby, J.E.* ...... 45 Tholen, K...... 67 Yang, H...... 28 Shen, G...... 38 Thompson, L...... 63 Yang, R...... 41 Shimotsuma, Y...... 31 Thompson, L.M.* ...... 58 Yang, Z...... 59 Short, R...... 62 Ting, Q...... 43 Yarger, J.L...... 30 Shoulders, T.* ...... 59 Toma, L...... 53 YeeShin, C...... 39 Shrivastava, J.P...... 61 Tomozawa, M...... 27, 30, 46 Yoshimoto, K...... 28 Sidebottom, D.L.* ...... 51 Tomozawa, M.* ...... 51 Yoshiyagawa, M...... 51 Siegel, J...... 26 Toplis, M...... 68 Yosinski, S...... 27 Sigaev, V...... 27, 64 Trachenko, K.* ...... 60 Youngman, R...... 58 Sigaev, V.* ...... 66 Tran, H...... 31, 64 Youngman, R.* ...... 34, 67 Siligardi, C...... 41, 50 Trebosc, J...... 34 Youngman, R.E...... 26, 42, 57 Silly, G...... 58 Tricot, G...... 34, 58 Yu, T.* ...... 38 Singh, D...... 40 Troendle, E...... 67 Yuan, F.* ...... 44 Singh, G...... 40 Trott, C.R.* ...... 43 Yuce, B...... 47 Singh, N...... 40 Troy, N...... 34 Yue, Y...... 42, 57, 60 Singh, R...... 50 Troy, N.* ...... 31 Yuhas, B.D.* ...... 28 Singh, V...... 45, 65 Tumber, S.K...... 30 Yukimitu, K...... 25 Singh, V.* ...... 44 Skakalova, V...... 38 V Z Skinner, L...... 29, 41 Vacher, R...... 64 Zanotto, E...... 35 Skinner, L.B.* ...... 46 Vafaei fard, M...... 39 Zanotto, E.D...... 45, 68 Smedskjaer, M.M...... 57 Van der Biest, O...... 51, 63 Zanotto, E.D.* ...... 67 Smedskjaer, M.M.* ...... 42, 56 Vandembroucq, D...... 31 Zapol, P.* ...... 55 Smektala, F.* ...... 49 Vanhoutte, M...... 45 Zha, Y...... 44 Smelser, C.W.* ...... 26 Vanhoutte, M.* ...... 65 Zhang, H...... 31 Smith, C...... 26 Varshneya, A.K...... 37, 43 Zhang, T.* ...... 28 Smith, C.* ...... 36, 41 Vasconcelos, F...... 34 Zhang, X...... 64 Smith, M.E...... 67 Velez, M...... 42 Zhao, Q...... 42 Soleilhavoup, A...... 61 Velez, M.* ...... 38 Zhou, X...... 43 Solis, J...... 66 Veurman, W...... 32, 62 Zhou, Z...... 54 Solis, J.* ...... 26, 31 Vieira, H.* ...... 41 Zhou, Z.* ...... 43 Son, H...... 62 Vienna, J...... 25 Zhu, L...... 49, 50 Sonneville, C...... 42 Vienna, J.* ...... 32 Zhu, Z...... 56 Souquet, J...... 35 Vignarooban K.* ...... 46 Zou, Q...... 28 Spalla, O...... 61 Vigouroux, H.* ...... 37, 64 Zou, Y...... 44 Srivastava, A...... 38 Villalobos, G...... 65 Zou, Y.* ...... 32, 33 Stafsudd, O...... 50 Vlcek, M...... 58 Zwanziger, J...... 59 Stamboulis, A...... 51, 63 Vlcek, M.* ...... 58 Zwanziger, J.* ...... 66 Stebbins, J...... 35 Vogel, M.* ...... 63 Zwanziger, J.W...... 31 Stebbins, J.F...... 58 von Zimmermann, M...... 29 Stebbins, J.F.* ...... 63 Vouagner, D...... 50, 64 Steefel, C...... 55 Vurgaftman, I...... 44 Steele, C...... 62 Stewart, R.L...... 60, 68 W Stinzianni, E...... 61 Wachtel, P...... 59 Stoecker, W.V...... 51 Wagner, B...... 64 Stolen, R...... 49 Walder, B.J.* ...... 37 Stone, A...... 39 Waldman, M...... 44 Stone, A.* ...... 31 Walker, R.B...... 26 Storek, M...... 63 Wang, S...... 52 Storek, M.* ...... 40 Wang, Y...... 38, 41, 42 Stoyanov, E...... 38, 53 Wanninkhof, P...... 40 Strachan, D.* ...... 57 Ward, N...... 37

72 2012 Glass & Optical Materials Division Annual Meeting Meetings & Expositions of The American Ceramic Society 2012–2013

June 10 – 12, 2012 June 2 – 7, 2013 3rd Advances in Cement-based Materials PACRIM 10 - The 10th Pacific Rim Conference The University of Texas at Austin on Ceramic and Glass Technology Austin, Texas, USA including GOMD 2013 www.ceramics.org/cements2012 Hotel Del Coronado San Diego, California, USA July 16 – 19, 2012 www.ceramics.org/pacrim10 4th International Congress on Ceramics, including 3rd Ceramic Leadership Summit Track August 4 – 7, 2013 Sheraton Chicago Hotel & Towers ICCPS-13: International Conference on Ceramic Chicago, Illinois, USA Processing Science www.ceramics.org/icc4 Hilton Portland & Executive Tower Portland, Oregon, USA September 10 – 13, 2012 Innovations in Biomedical Materials September 10 – 13, 2013 Hilton North Raleigh-Midtown UNITECR 2013 - The Unified Technical Raleigh, North Carolina, USA Conference of Refractories www.ceramics.org/biomaterials2012 The Fairmont Empress & Victoria Conference Centre October 7 – 11, 2012 Victoria, British Columbia, Canada MS&T’12 and ACerS 114th Annual Meeting www.unitecr2013.org David L. Lawrence Convention Center Pittsburgh, Pennsylvania, USA October 27 – 31, 2013 www.matscitech.org MS&T’13: Materials Science & Technology Conference and Exhibition, combined with January 23 – 25, 2013 ACerS 115th Annual Meeting Electronic Materials and Applications The Palais des congrès de Montréal DoubleTree by Hilton Orlando at Sea World Montréal, Québec, Canada Orlando, Florida, USA www.ceramics.org/ema2013

January 27 – February 1, 2013 37th International Conference and Expo on Advanced Ceramics and Composites - ICACC’13 Hilton Daytona Beach Resort and Ocean Center Daytona Beach, Florida, USA www.ceramics.org/daytona2013