DOCSLIB.ORG

Effects of Selected Minor Alloying Additions on the Structure And

Total Page：16

File Type：pdf, Size：1020Kb

Download full-text PDF Read full-text
Effects of Selected Minor Alloying Additions on the Structure And ABSTRACT AN ABSTRACT OF THE THESIS OF GEORGE J. DOOLEY III for the Doctor of Philosophy in Materials Science presented on May 7, 1969. Title: Effects of Selected Minor Alloying Additions on the Structure and Deformation Characteristics of Beryllium Abstract approved: William D. McMullen Solid solution alloying was employed in an attempt to produce some relatively ductile form of beryllium. If the c/a ratio could be significantly altered, it was felt new or different slip systems could be activated. The following elements were selected on the basis of atomic size, melting point, crystal structure and density for adding to beryllium in amounts of 0. 5, 1.0, 2.0, 3.0, 4.0, 5.0 and 10.0 atomic percentages: boron, manganese and, titanium. All samples were non -consumable arc melted, machined and sectioned for wet chemical, spectrographic, X -ray diffraction and metal - lographic analysis as well as for mechanical (compression) testing. These tests showed all alloy samples exceeded the solubility limits in each respective system. Be4_5B, Be8Mn and Be12Ti'were identified as the second phases in the individual systems. Beryllium -boron alloys ex- hibited an eutectic or peritectic reaction and the eutectic composition in the beryllium -manganese system was established at 22.0 weight percent manganese. The samples Be /0. 5B, Be /1.0Mn and Be /0. 5Ti gave yield strengths of 47, 200 psi, 56, 600 psi and 81, 250 psi respectively in compression testing. These same specimens yielded work hardening rates of 1.07 x 106 psi, 1.3 x 106 psi and 1. 52 x 106 psi respectively. Long wide twins in pure beryllium were accompanied by large amounts of cross -slip. The boron sample displayed long wide twins and also very short narrow twins, no cross -slip and extensive areas with microcracks present. Shorter and narrower twins characterize the manganese specimens. The beryllium- titanium alloys exhibited extremely small twins emanating from particles of second phase Be12Ti; however, the majority of the twins in this system are long, extremely narrow and are seen to be internally con- stricted along the length of the twin. Thése constrictions have been ascribed to a strain relief process which further prevented the twin from growing parallel to its shorter dimension. The near total absence of cross -slip in the three alloy systems was attributed to a lessening of the stacking fault energy as a result of in- creasing the solute concentration. The drop in the stacking fault energy decreases the probability for cross -slip, makes extensive deformation difficult and explains higher yield strengths and work hardening rates. Evidence presented suggests slip occurs prior to gross twin propagation. The relationship betw twinning shear and twin shape suggests for the beryllium- titanium alloys twinning on higher order planes (e. g. , {.1121} or 11122 }) rather than the {1012} twinning normally observed. Effects of Selected Minor Alloying Additions on the Structure and Deformation Characteristics of Beryllium by George Joseph Dooley III A THESIS submitted to Oregon State University in partial fulfillment of the requirements for the degree of Doctor of Philosophy June 1969 APPROVAL SHEET APPROVED: Associate Professor of Mechanical Engineering Head of Department of i chanical Engineering Dean of Graduate School Date thesis is presented May 7, 1969 Typed by Joyce McInnis for George J. Dooley III ACKNOWLEDGMENTS The author would like to express his gratitude to the U.S. Bureau of Mines, Albany, Oregon and to Oregon State University, Corvallis, Oregon, whose cooperative agreement made this research work possible. Although many Bureau of Mines' personnel were helpful throughout the course of this work, particular thanks must be extended to members of the Metals Pro- cessing branch under the direction of Mr. : obert Beall, to members of the Materials Science branch under the direction of Mr. Hal Kelly and to Mr. Jim Wilderman of the drafting section for his work on the figures and draw- ings. Mrs. Joyce McInnis, typist and secretary, deserves more praise than thanks for her efficiency, assistance and good nature during the author's stay at the Bureau of Mines. The majority of the technical guidance for this piece of research was provided by Dr. William McMullen of Oregon State University. His unique personality 'coupled with technical competence provided the latitude necessary for carrying through a research project of this type. His suggestions and guidance gave more directionality to the work and saved many hours time when the author's efforts would perhaps have proceeded along other avenues of approach. The author's sincere appreciation is extended to him for his aid and cooperation. The greatest debt of any must be paid to the author's wife for her patience, hard work and encouragement throughout this somewhat trying academic period of life. Her willingness (and often insistence) , ;. tine and and research efforts on the part of the author before their personal while family obligations was indicative of the continuing support received have been working as a graduate student. Without her aid the work would less enjoyable, less meaningful and certainly much less rewarding. TABLE OF CONTENTS Page INTRODUCTION 1 THEORETICAL BACKGROUND 8 REVIEW OF LITERATURE 30 MATERIALS 97 APPARATUS AND EXPERIMENTAL PROCEDURES 102 Weighing and Compacting 102 Nonconsumable Arc Melting 103 Machining and Sectioning 108 Metallographic Analyses 109 X -ray Diffraction Analysis 110 Chemical and Spectrographic Analyses 112 Compression Testing 113 EXPERIMENTAL RESULTS 116 X-ray Diffraction 116 Metallography 118 Mechanical Deformation 124 Slip and Twinning 128 DISCUSSION AND CONCLUSIONS 151 SUMMARY 169 TABLE OF CONTENTS (Continued) Page SUGGESTIONS FOR FUTURE WORK 172 BIBLIOGRAPHY 175 LIST OF FIGURES Figure Page 1 Planes in an hexagonal lattice with a common [1210j direction 9 2 Important planes and directions in an hexagonal close packed metal 11 3 Crystallographic directions and planes in hexagonal close packed beryllium 12 4 Slips, fracture and twin planes in beryllium 14 5 Effect of temperature on the critical stress for (0001) slip and (1010) slip 15 6 The compounds of beryllium 83 7 Nonconsumable arc melting button furnace 104 8 Second phase Be4_5B in beryllium -boron alloys 120 9 Eutectic phase in Be /4. 0VM 122 10 Be8Mn phase in Be/ 1. 0Mn 125 11 Be12Ti phase in Be/ 0. 5Ti 126 12 -A Microstructure of deformed pure beryllium 130 12 -B 12 -C Typical deformation twins in pure beryllium 131 13 Straight slip lines in pure beryllium 132 14 Crow: slip in pure beryllium 133 15 Slip lines crossing twins in pure beryllium 134 LIST OF FIGURES (Continued) Figure Page, 16 Typical deformation twins in Be/ 0.5B 136 17 Microcracks in Be/0. 5B 138 18 Curved twins in Be/0. 5B 139 19 Representative deformation twins in Be/1. OMn 140 20 Very narrow twins in Be/1. OMn 141 21 Twin intersections in Be/1. 01\Tri 143 22 Extensive twinning in Be/1. Clitin 144 23 Short twins and second phase in Be/ O. 5Ti 145 24 Narrow twins in Be/0. 5Ti 146 25 Slip lines in Be/0. 5Ti 14 8 26 Irregular twins in Be/ O. 5Ti - 149 27 Slip crossing twins in Be/0. 5Ti 150 LIST OF TABLES Table Page I Modes of slip in hexagonal metals 22 II Beryllium deformation behavior 40 III Microstructure of binary beryllium alloys as melted 74 IV Beryllium starting material analysis 100 V Alloying element analysis 101 VI Alloy compositions after arc -melting of samples used in compression testing experiments 124 VII Work hardening rates and yield strengths for beryllium alloys 127 EFFECTS OF SELECTED MINOR ALLOYING ADDITIONS ON THE STRUCTURE AND DEFORMATION CHARACTERISTICS OF BERYLLIUM INTRODUCTION The potential of the metal, beryllium, has been recognized for some time. Its notable characteristics are low density, high elastic modulus and its high strength -to- weight ratio (61). Its density (1. 848 grams per cubic centimeter) approaches that of magnesium, yet beryllium melts some 600° C higher than magnesium. Its elastic modulus is approximately 140 percent that of iron, however, it is less than one -fourth as heavy. Its electrical conductivity is approximately 40 percent that of pure copper (2). But, use of pure beryllium in industrial applications has never signifi- cantly materialized. Beryllium has not realized its full potential in indus- trial applications because of its lack of so- called third -dimensional ductil- ity. The term "third- dimensional ductility" infers that plates and sheets of beryllium can be successfully fabricated, but these structures are in- capable of supporting any bending or any significant forces perpendicular to their major plane of symmetry. Efforts to fabricate beryllium by con- ventional means of fusion, casting and extrusion, have been only partially successful. It is possible to limitedly manipulate the ductility of beryllium, but each particular application requires a careful study of the fabrication methods so as to produce optimum ductility in a specific direction by a 2 compromise of the ductilities in the other directions. This fact is physical evidence for the known anisotropy of beryllium. Beryllium has other features not related to the ductility aspect which make it a valuable material. These will not be of interest in this work; however, they should be mentioned for the sake of completeness. Beryllium is characterized by some outstanding nuclear properties. It has an extremely low neutron capture cross section and a high neutron scattering cross section which make it useful as a moderator and reflector for thermal nuclear -power reactors. During the last few years emphasis in the application of beryllium has shifted from nuclear applications to so- called "space applications" and the latest development of beryllium has been in connection with the various rocket, missile, and aircraft projects. Nevertheless, two main factors have delayed a wider application of beryllium in industry.
Load more

Recommended publications
  • Some Aspects of Cross-Slip Mechanisms in Metals and Alloys Daniel Caillard, J.L
    Some aspects of cross-slip mechanisms in metals and alloys Daniel Caillard, J.L. Martin To cite this version: Daniel Caillard, J.L. Martin. Some aspects of cross-slip mechanisms in metals and alloys. Journal de Physique, 1989, 50 (18), pp.2455-2473. 10.1051/jphys:0198900500180245500. jpa-00211074 HAL Id: jpa-00211074 https://hal.archives-ouvertes.fr/jpa-00211074 Submitted on 1 Jan 1989 HAL is a multi-disciplinary open access L’archive ouverte pluridisciplinaire HAL, est archive for the deposit and dissemination of sci- destinée au dépôt et à la diffusion de documents entific research documents, whether they are pub- scientifiques de niveau recherche, publiés ou non, lished or not. The documents may come from émanant des établissements d’enseignement et de teaching and research institutions in France or recherche français ou étrangers, des laboratoires abroad, or from public or private research centers. publics ou privés. J. Phys. France 50 (1989) 2455-2473 15 SEPTEMBRE 1989, 2455 Classification Physics Abstracts 62.20H Some aspects of cross-slip mechanisms in metals and alloys D. Caillard (1) and J. L. Martin (2) (1) Laboratoire d’Optique Electronique du CNRS, B.P. 4347, F-31055 Toulouse Cedex, France (2) Institut de Génie Atomique, Ecole Polytechnique Fédérale de Lausanne, CH-1015 Lausanne, Switzerland (Reçu le 6 mars 1989, accepté sous forme définitive le 24 mai 1989) Résumé. 2014 Des modèles ont été proposés pour décrire le glissement dévié des dislocations dans les métaux de structure CFC et HC. On montre comment ces modèles se sont développés et comment des résultats expérimentaux récents confirment leurs prédictions.
    [Show full text]
  • ABSTRACT SECOND ORDER PYRAMIDAL SLIP in ZINC SINGLE CRYSTALS K. H. Adams,* R. C. Blish and T. Vreeland, Jr. W. M. Keck Laborator
    CALT-473-18 SECOND ORDER PYRAMIDAL SLIP IN ZINC SINGLE CRYSTALS K. H. Adams,* R. C. Blish and T. Vreeland, Jr. W. M. Keck Laboratory of Engineering Materials California Institute of Technology Pasadena, California (U.S.A.) ABSTRACT Measurements of strain, dislocation mobility and dislocation density have been made in 99.999% zinc single crystals stressed at room temperatur~ j_n comp.!:_ession along the hexagonal axis, [0001]. Slip bands on the <1213) { 1212 }, second order pyramidal system were observed. Etch pit observations indicate that the average dislocation density increases linearly with strain. The velocity of edge dislocations in slip bands obeys the relation v = v (-rh )n with v = 1 in/sec , 0 0 n = 8.7 , -r = 870 lb/in2 , and -r the resolved sheRr stress in lb/in2 • These observRtions together with measurements of the strain-rate sensitivity of the flow stress show that the stress dependence of the density of moving dislocations is more important than the stress dependence of the dislocation velocity as they affect the strain-rate sensitivity. INTRODUCTION The stress dependence of the mobility of basal dislocations in zinc single crystals has recently been reported by Adams et al. [1]. The same experimental techniques have been applied in a study of the <1213> { 1212 }, second order pyramidal slip system. The <1213) { 1212 } slip system was originally confirmed as a nonbasal slip system in zinc * Present Address: Department of Mechanical Engineering, Tulane University, New Orleans, La. (U.S.A.). by Rosenbaum [2] from etch pit and slip line observations. Additional supporting evidence has been provided by Price [3] from electron microscope observations of the formation and climb of dislocation loops in the <12l3) { 1212 } slip system.
    [Show full text]
  • Dislocations and Plastic Deformation in Mgo Crystals: a Review
    Dislocations and Plastic Deformation in MgO Crystals: A Review Jonathan Amodeo, Sébastien Merkel, Christophe Tromas, Philippe Carrez, Sandra Korte-Kerzel, Patrick Cordier, Jérome Chevalier To cite this version: Jonathan Amodeo, Sébastien Merkel, Christophe Tromas, Philippe Carrez, Sandra Korte-Kerzel, et al.. Dislocations and Plastic Deformation in MgO Crystals: A Review. Crystals, MDPI, 2018, 8 (6), pp.1-53. 10.3390/cryst8060240. hal-01807690 HAL Id: hal-01807690 https://hal.archives-ouvertes.fr/hal-01807690 Submitted on 5 Jun 2018 HAL is a multi-disciplinary open access L’archive ouverte pluridisciplinaire HAL, est archive for the deposit and dissemination of sci- destinée au dépôt et à la diffusion de documents entific research documents, whether they are pub- scientifiques de niveau recherche, publiés ou non, lished or not. The documents may come from émanant des établissements d’enseignement et de teaching and research institutions in France or recherche français ou étrangers, des laboratoires abroad, or from public or private research centers. publics ou privés. Distributed under a Creative Commons Attribution| 4.0 International License crystals Review Dislocations and Plastic Deformation in MgO Crystals: A Review Jonathan Amodeo 1,* ID ,Sébastien Merkel 2,3 ID , Christophe Tromas 4 ID , Philippe Carrez 2 ID , Sandra Korte-Kerzel 5, Patrick Cordier 2 ID and Jérôme Chevalier 1 1 Université de Lyon, INSA-Lyon, CNRS, MATEIS UMR5510, F-69621 Villeurbanne, France; [email protected] 2 Université de Lille, CNRS, INRA, ENSCL,
    [Show full text]
  • Mechanisms in Creep and Anelastic Recovery of Face- Centered Cubic Alloys
    Review: mechanisms in creep and anelastic recovery of face- centered cubic alloys Kun Gao MT 11.14 Supervisor: Dr.ir. Hans van Dommelen Eindhoven University of Technology Department of mechanical engineering 1 Abstract In order to understand anelastic recovery behavior of Al-Cu thin films in RF-MEMS, this literature report firstly reviews creep behavior of face-centered cubic (f.c.c.) alloys and corresponding mechanisms including grain boundary sliding, dislocation glide and climb. In addition, the Orowan process, the Friedel process and thermal detachment, which are important in precipitate- strengthened alloys, are also discussed. Then, relations between these mechanisms and the anelastic recovery are investigated. In the second part, some creep models based on the mechanisms in the first part are presented. The conclusions of this report are as follows: grain boundary sliding due to diffusion is not involved in the anelastic recovery; dislocation glide encumbered by the Orowan stress and the Friedel stress is a possible mechanism in the room-temperature anelastic recovery; the driving force may originate from unbowing of bowed dislocations and dislocation pile-up. At high temperature, dislocation climb may determine creep rate due to active diffusion. Besides climbing, dislocations can also bypass particles by cross-slip, which will occur if internal stress increases, and thermal detachment that appears to be strong for small particles. For modeling the anelasitc behavior, the power law is very flexible and it is feasible to include some internal variables for the sake of a stronger physical meaning. In addition, building up direct relations between the strain rate and internal variables is also a good choice.
    [Show full text]
  • Deformation of Single Crystals
    Deformation of Single Crystals When a single crystal is deformed under a tensile stress, it is observed that plastic deformation occurs by slip on well‐defined parallel crystal planes. Sections of the crystal slide relative to one another, changing the geometry of the sample as shown in the diagram. Slip always occurs on a particular set of crystallographic planes, known as slip planes. Slip always takes place along a consistent set of directions within these planes –these are called slip directions. The combination of slip plane and slip direction together makes up a slip system. Slip systems are usually specified using the Miller index notation. For example, cubic close‐packed metals slip on 1 1 0{} 1 1 1 The slip direction must lie in the slip plane. Slip occurs by dislocation motion. To move dislocations, a certain stress must be applied to overcome the resistance to dislocation motion. Slip occurs when the shear stress acting in the slip direction on the slip plane reaches some critical value. This critical shear stress is related to the stress required to move dislocations across the slip plane. The tensile yield stress of a material is the applied stress required to start plastic deformation of the material under a tensile load. We want to relate the tensile stress applied to a sample to the shear stress that acts along the slip direction. resolved_____actingforce on slipF cos planeλ F τ = =cos =φ λ cos=cos σ φ cos λ R area of___ slip plane A A cosφ It is found that the value of τR at which slip occurs in a given material with specified dislocation density and purity is a constant, known as the critical resolved shear stress τC.
    [Show full text]