Effect of Annealing Prior to Cold Rolling on the Microstructure
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Using Grain Boundary Irregularity to Quantify Dynamic Recrystallization in Ice
Acta Materialia 209 (2021) 116810 Contents lists available at ScienceDirect Acta Materialia journal homepage: www.elsevier.com/locate/actamat Using grain boundary irregularity to quantify dynamic recrystallization in ice ∗ Sheng Fan a, , David J. Prior a, Andrew J. Cross b,c, David L. Goldsby b, Travis F. Hager b, Marianne Negrini a, Chao Qi d a Department of Geology, University of Otago, Dunedin, New Zealand b Department of Earth and Environmental Science, University of Pennsylvania, Philadelphia, PA, United States c Department of Geology and Geophysics, Woods Hole Oceanographic Institution, Woods Hole, MA, United States d Institute of Geology and Geophysics, Chinese Academy of Sciences, Beijing, China a r t i c l e i n f o a b s t r a c t Article history: Dynamic recrystallization is an important mechanical weakening mechanism during the deformation of Received 24 December 2020 ice, yet we currently lack robust quantitative tools for identifying recrystallized grains in the “migration” Revised 7 March 2021 recrystallization regime that dominates ice deformation at temperatures close to the ice melting point. Accepted 10 March 2021 Here, we propose grain boundary irregularity as a quantitative means for discriminating between recrys- Available online 15 March 2021 tallized (high sphericity, low irregularity) and remnant (low sphericity, high irregularity) grains. To this Keywords: end, we analysed cryogenic electron backscatter diffraction (cryo-EBSD) data of deformed polycrystalline High-temperature deformation ice, to quantify dynamic recrystallization using grain boundary irregularity statistics. Grain boundary ir- Grain boundary irregularity regularity has an inverse relationship with a sphericity parameter, , defined as the ratio of grain area Dynamic recrystallization and grain perimeter, divided by grain radius in 2-D so that the measurement is grain size independent. -
Grain Growth During Spark Plasma and Flash Sintering of Ceramic Nanoparticles: a Review Rachman Chaim, Geoffroy Chevallier, Alicia Weibel, Claude Estournes
Grain growth during spark plasma and flash sintering of ceramic nanoparticles: a review Rachman Chaim, Geoffroy Chevallier, Alicia Weibel, Claude Estournes To cite this version: Rachman Chaim, Geoffroy Chevallier, Alicia Weibel, Claude Estournes. Grain growth during spark plasma and flash sintering of ceramic nanoparticles: a review. Journal of Materials Science, Springer Verlag, 2018, vol. 53 (n° 5), pp. 3087-3105. 10.1007/s10853-017-1761-7. hal-01682331 HAL Id: hal-01682331 https://hal.archives-ouvertes.fr/hal-01682331 Submitted on 12 Jan 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. Open Archive TOULOUSE Archive Ouverte (OATAO) OATAO is an open access repository that collects the work of Toulouse researchers and makes it freely available over the web where possible. This is an author-deposited version published in : http://oatao.univ-toulouse.fr/ Eprints ID : 19431 To link to this article : DOI:10.1007/s10853-017-1761-7 URL : http://dx.doi.org/10.1007/s10853-017-1761-7 To cite this version : Chaim, Rachman and Chevallier, Geoffroy and Weibel, Alicia and Estournes, Claude Grain growth during spark plasma and flash sintering of ceramic nanoparticles: a review. -
On a Mathematical Model for Case Hardening of Steel
On a mathematical model for case hardening of steel vorgelegt von Dott.ssa Lucia Panizzi Von der Fakultät II ‚ Mathematik und Naturwissenschaften der Technischen Universität Berlin zur Erlangung des akademischen Grades Doktor der Naturwissenschaften Dr. rer. nat. sowie der Classe di Scienze der Scuola Normale Superiore di Pisa als Diploma di Perfezionamento in Matematica per la Tecnologia e l’Industria genehmigte Dissertation Promotionsausschuss: Berichter/Gutachter: Prof. A. Fasano (Univerisità di Firenze) Berichter/Gutachter: Prof. D. Hömberg (Technische Universität Berlin) Gutachter: Prof. L. Formaggia (Politecnico di Milano) Gutachter: Prof. M. Primicerio (Università di Firenze) Gutachter: Prof. F. Tröltzsch (Technische Universität Berlin) Gutachter: Prof. P. Wittbold (Technische Universität Berlin) Tag der wissenschaftlichen Aussprache: 05.03.2010 Berlin 2010 D83 i Eidesstattliche Versicherung Hiermit erkläre ich, dass die vorliegende Dissertation: On a mathematical model for case hardening of steel selbständig verfasst wurde. Die benutzten Hilfsmittel und Quellen wurden von mir angegeben, weitere wurden nicht verwendet. ii Erklärung Hiermit erkläre ich, dass die Anmeldung meiner Promotionsabsicht früher nicht bei einer anderen Hochschule oder einer anderen Fakultät beantragt wurde. Teile meiner Dissertation sind darüber hinaus schon veröffentlich worden, welche im Folgenden aufgelistet sind: • D. Hömberg, A. Fasano, L. Panizzi A mathematical model for case hardening of steel. angenommen zur Veröffentlichung in "Mathematical Models and Methods in Applied Sciences" (M3AS), 2009. • P. Krejčí, L. Panizzi. Regularity and uniqueness in quasilinear parabolic systems. angenommen zur Veröffentlichung in "Applications of Mathematics", 2009. iii Compendio Nonostante la disponibilità di numerosi nuovi materiali, l’acciaio rimane il ma- teriale di base della moderna società industriale. L’uso dell’ acciaio con peculiari caratteristiche (durezza, resistenza all’uso, malleabilità etc.) è perciò assai diffuso in molti settori della tecnica. -
UNDERSTANDING and MEASURING DECARBURIZATION Understanding the Forces Behind Decarburization Is the First Step Toward Minimizing Its Detrimental Effects
22 UNDERSTANDING AND MEASURING DECARBURIZATION Understanding the forces behind decarburization is the first step toward minimizing its detrimental effects. George F. Vander Voort, FASM*, Struers Inc. (Consultant), Cleveland ecarburization is detrimental to crostructure of carbon contents close to the maximum depth of decarburization the wear life and fatigue life of the core may be difficult to discern. The is established. Because the carbon dif- steel heat-treated components. MAD determined by hardness traverse fusion rate increases with temperature ADVANCED MATERIALS & PROCESSES | FEBRUARY 2015 2015 FEBRUARY | & PROCESSES MATERIALS ADVANCED D This article explores some factors that may be slightly shallower than that de- when the structure is fully austenitic, cause decarburization while concentrat- termined by quantitative carbon analysis MAD also increases as temperature rises ing on its measurement. In most produc- with the electron microprobe. This is es- above the Ac3. For temperatures in the tion tests, light microscopes are used to pecially true when the bulk carbon con- two-phase region, between the Ac1 and scan the surface of a polished and etched tent exceeds about 0.45 wt%, as the rela- Ac3, the process is more complex. Carbon cross-section to find what appears to be tionship between carbon in the austenite diffusion rates in ferrite and austenite the greatest depth of total carbon loss before quenching to form martensite and are different, and are influenced by both (free-ferrite depth, or FFD) and the great- the as-quenched hardness loses its linear temperature and composition. est depth of combined FFD and partial nature above this carbon level. Decarburization is a serious prob- loss of carbon to determine the maxi- lem because surface properties are infe- mum affected depth (MAD). -
An Introduction to Nitriding
01_Nitriding.qxd 9/30/03 9:58 AM Page 1 © 2003 ASM International. All Rights Reserved. www.asminternational.org Practical Nitriding and Ferritic Nitrocarburizing (#06950G) CHAPTER 1 An Introduction to Nitriding THE NITRIDING PROCESS, first developed in the early 1900s, con- tinues to play an important role in many industrial applications. Along with the derivative nitrocarburizing process, nitriding often is used in the manufacture of aircraft, bearings, automotive components, textile machin- ery, and turbine generation systems. Though wrapped in a bit of “alchemi- cal mystery,” it remains the simplest of the case hardening techniques. The secret of the nitriding process is that it does not require a phase change from ferrite to austenite, nor does it require a further change from austenite to martensite. In other words, the steel remains in the ferrite phase (or cementite, depending on alloy composition) during the complete proce- dure. This means that the molecular structure of the ferrite (body-centered cubic, or bcc, lattice) does not change its configuration or grow into the face-centered cubic (fcc) lattice characteristic of austenite, as occurs in more conventional methods such as carburizing. Furthermore, because only free cooling takes place, rather than rapid cooling or quenching, no subsequent transformation from austenite to martensite occurs. Again, there is no molecular size change and, more importantly, no dimensional change, only slight growth due to the volumetric change of the steel sur- face caused by the nitrogen diffusion. What can (and does) produce distor- tion are the induced surface stresses being released by the heat of the process, causing movement in the form of twisting and bending. -
20. Iron and Steel Part II Copy
USES FOR TYPES OF STEELS • Low carbon steel (0.08 - 0.35 % carbon) is ductile with low brittleness. It is is used for ANCIENT IRON auto body parts, home appliances, tin cans, I beams for construction. AND STEEL • Medium carbon steel (0.35 - 0.5 % carbon) (Part II) is used as crankshaft, gears, railroad axels. (Part II) They are difficult to weld. • High carbon steel (> 0.5 % carbon) is used for railroad wheels and rails, wrenches, steel cable, tools, dies, piano wire etc. BLAST FURNACE CAST IRON (PIG IRON) • Contains 1.5 - 5 % carbon. • Its melting point is 1130 oC. • The metal will shatter with a hard blow. • Carbon in the form of graphite exists as flakes • Graphite serves as a lubricant (excellent bearing material). 1 Cast Grey Iron Blast furnace at Cast Grey Iron Karabük Iron works Cast Gray Iron Graphite flakes THE FINERY CAST IRON OBJECTS THE FINERY Cast cannon 15th. Cent. 2 INDIRECT METHOD OF STEEL BESSEMER PROCESS PRODUCTION (THE BESSEMER PROCESS) Crude cast iron from the blast furnace is remelted in a hearth (the finary) and subjected to a forced draught of air. The excess carbon is oxidized to carbon dioxide. The refined pig iron which is called malleable iron is now ready for final forging. BESSEMER PROCESS FORMS OF IRON CAST IRON Decarburization From Blast Furnace M.P. 1130oC 1,5-4.5 % C Bessemer STEEL Process M.P. 1400o C 0.1-0.9 % C WROUGHT IRON From Bloomery Cementation M.P 1535o C 0.06 % C Carburization 3 DIFFERENCES BETWEEN BLOOMERY ALLOY STEELS AND BLAST FURNACE • Increase in temperature (1300 - 1400oC) • Alloy steel describes steel that contain one or more alloying elements in addition to carbon. -
AISI | Electric Arc Furnace Steelmaking
http://www.steel.org/AM/Template.cfm?Section=Articles3&TEMPLATE=/CM/HTMLDisplay.cfm&CONTENTID=12308 Home Steelworks Home Electric Arc Furnace Steelmaking By Jeremy A. T. Jones, Nupro Corporation SIGN UP to receive AISI's FREE e-news! Read the latest. Email: Name: Join Courtesy of Mannesmann Demag Corp. FURNACE OPERATIONS The electric arc furnace operates as a batch melting process producing batches of molten steel known "heats". The electric arc furnace operating cycle is called the tap-to-tap cycle and is made up of the following operations: Furnace charging Melting Refining De-slagging Tapping Furnace turn-around Modern operations aim for a tap-to-tap time of less than 60 minutes. Some twin shell furnace operations are achieving tap-to-tap times of 35 to 40 minutes. 10/3/2008 9:36 AM http://www.steel.org/AM/Template.cfm?Section=Articles3&TEMPLATE=/CM/HTMLDisplay.cfm&CONTENTID=12308 Furnace Charging The first step in the production of any heat is to select the grade of steel to be made. Usually a schedule is developed prior to each production shift. Thus the melter will know in advance the schedule for his shift. The scrap yard operator will prepare buckets of scrap according to the needs of the melter. Preparation of the charge bucket is an important operation, not only to ensure proper melt-in chemistry but also to ensure good melting conditions. The scrap must be layered in the bucket according to size and density to promote the rapid formation of a liquid pool of steel in the hearth while providing protection for the sidewalls and roof from electric arc radiation. -
CONTROL of DECARBURIZATION of STEEL Paul Shefsiek
CONTROL OF DECARBURIZATION OF STEEL Paul Shefsiek Introduction Historically, heating steel for forming, forging or rolling, was done in electrical resistance or natural gas heated furnaces. It was inevitable that these furnaces contained Oxygen and Decarburization of the steel surface occurred. This decarburization was either ignored or minimized by coating the steel with “ stopoff “. Also, this decarburization was minimized through the use nitrogen atmosphere furnaces. But, decarburization could not be reduced to acceptable limits until the Chemical Potential of the Carbon in the furnace atmosphere matched the dissolved Carbon in the steel. The Furnace Industry that provides Equipment for the processing of steel, because of the temperature ranges involved, divided itself into two categories, namely, Reheat and Heat Treating. Each has its own special Technology. But, because of this division, quite often one division does not know the Technology of the other. In some cases this has been unfortunate. If the Reheat side of the Industry had the Carburizing Technology of the Heat Treating side, this Technology could have been applied to applications where preventing Decarburizing was a requirement. Therefore, the purpose of the following discussion is to separate out that part of Carburizing Technology that is applicable to preventing Decarburization in Reheat applications. Fundamentals Control of the Decarburization of Steel has been standardized to the monitoring of - The Metal Temperature (Furnace Temperature) - The Atmosphere Concentration of Carbon Monoxide (CO) - The Atmosphere Concentration of Carbon Dioxide (CO2). Knowing the values of these three (3) parameters and the knowledge of - Saturated Austenite in Iron - The Alloy Content of the Steel - The Equilibrium Constant for the Controllable Chemical Reaction between the Steel and the Gas Atmosphere it can be determined if the Atmosphere will prevent Decarburization of the Steel. -
1.1%Mn--0.05%C Steel Sheets by Silicon Dioxide and Development Of
Materials Transactions, Vol. 44, No. 6 (2003) pp. 1096 to 1105 #2003 The Japan Institute of Metals Decarburization of 3%Si–1.1%Mn–0.05%C Steel Sheets by Silicon Dioxide and Development of {100}h012i Texture* Toshiro Tomida Corporate Research & Development Laboratories, Sumitomo Metal Industries, Ltd., Amagasaki 660-0891, Japan Decarburization of silicon steel sheets by annealing with oxide separators has been found to cause a high degree of {100}-texture development. Cold-rolled Fe–3%Si–1.1%Mn–0.05%C sheets of 0.35 mm thickness were laminated with separators containing SiO2. They were then annealed under a reduced pressure at about 1300 K in a ferrite and austenite two phase region. It has been observed that carbon concentration notably decreases down to 0.001% during the lamination annealing. Thus an almost complete decarburization of sheet steels was possible, whereas no oxidation of silicon as well as manganese and iron occurred. Associated with decarburization, columnar ferrite grains grew inward from sheet surfaces due to the phase transformation from austenite to ferrite. A {100}h012i texture dramatically developed in the columnar grains. Fully decarburized materials consisted of grains of 0.6 mm diameter, more than 90% of which were closely aligned with {100}h012i orientation. Another aspect of great interest in the grain structure after decarburization was that there existed convoluted domains of a few mm in width, in which dozens of grains were oriented in a single variant of the texture, (100)[012] or (100)[021]. The decarburization is considered to be caused by the thermo-chemical reaction, 2C+SiO2!Si+2CO. -
7313200007 DEC Permit Conditions FINAL Page 1 PERMIT Under The
Facility DEC ID: 7313200007 PERMIT Under the Environmental Conservation Law (ECL) IDENTIFICATION INFORMATION Permit Type: Air Title V Facility Permit ID: 7-3132-00007/00028 Effective Date: 06/07/2016 Expiration Date: 06/06/2021 Permit Issued To:CRUCIBLE INDUSTRIES LLC 575 STATE FAIR BLVD SYRACUSE, NY 13209 Contact: James Vreeland Crucible Industries LLC 575 State Fair Blvd Solvay, NY 13209 (315) 470-9234 Facility: CRUCIBLE INDUSTRIES 575 STATE FAIR BLVD GEDDES, NY 13209 Contact: James Vreeland Crucible Industries LLC 575 State Fair Blvd Solvay, NY 13209 (315) 470-9234 Description: Promulgation of 40 CFR 63, YYYYY requires all sources to obtain a Title V facility operating permit. Therefore, a Title V permit must be issued for this source; otherwise the source is a synthetic minor. By acceptance of this permit, the permittee agrees that the permit is contingent upon strict compliance with the ECL, all applicable regulations, the General Conditions specified and any Special Conditions included as part of this permit. Permit Administrator: ELIZABETH A TRACY 615 ERIE BLVD WEST SYRACUSE, NY 13204-2400 Authorized Signature: _________________________________ Date: ___ / ___ / _____ DEC Permit Conditions FINAL Page 1 Facility DEC ID: 7313200007 Notification of Other State Permittee Obligations Item A: Permittee Accepts Legal Responsibility and Agrees to Indemnification The permittee expressly agrees to indemnify and hold harmless the Department of Environmental Conservation of the State of New York, its representatives, employees and agents ("DEC") for all claims, suits, actions, and damages, to the extent attributable to the permittee's acts or omissions in connection with the compliance permittee's undertaking of activities in connection with, or operation and maintenance of, the facility or facilities authorized by the permit whether in compliance or not in any compliance with the terms and conditions of the permit. -
A Novel Decarburizing-Nitriding Treatment of Carburized/Through-Hardened Bearing Steel Towards Enhanced Nitriding Kinetics and Microstructure Refinement
coatings Article A Novel Decarburizing-Nitriding Treatment of Carburized/through-Hardened Bearing Steel towards Enhanced Nitriding Kinetics and Microstructure Refinement Fuyao Yan 1, Jiawei Yao 1, Baofeng Chen 1, Ying Yang 1, Yueming Xu 2, Mufu Yan 1,* and Yanxiang Zhang 1,* 1 School of Materials Science and Engineering, Harbin Institute of Technology, Harbin 150001, China; [email protected] (F.Y.); [email protected] (J.Y.); [email protected] (B.C.); [email protected] (Y.Y.) 2 Beijing Research Institute of Mechanical & Electrical Technology, Beijing 100083, China; [email protected] * Correspondence: [email protected] (M.Y.); [email protected] (Y.Z.); Tel.: +86-451-86418617 (M.Y.) Abstract: Decarburization is generally avoided as it is reckoned to be a process detrimental to material surface properties. Based on the idea of duplex surface engineering, i.e., nitriding the case-hardened or through-hardened bearing steels for enhanced surface performance, this work deliberately applied decarburization prior to plasma nitriding to cancel the softening effect of decarburizing with nitriding and at the same time to significantly promote the nitriding kinetics. To manifest the applicability of this innovative duplex process, low-carbon M50NiL and high-carbon M50 bearing steels were adopted in this work. The influence of decarburization on microstructures and growth kinetics of the nitrided layer over the decarburized layer is investigated. The metallographic analysis of the nitrided layer thickness indicates that high carbon content can hinder the growth of the nitrided Citation: Yan, F.; Yao, J.; Chen, B.; layer, but if a short decarburization is applied prior to nitriding, the thickness of the nitrided layer Yang, Y.; Xu, Y.; Yan, M.; Zhang, Y. -
Feasibility of Solid-State Steelmaking from Cast Iron -Decarburization of Rapidly Solidified Cast Iron
ISIJ International, Vol. 52 (2012), No. 1, pp. 26–34 Feasibility of Solid-state Steelmaking from Cast Iron -Decarburization of Rapidly Solidified Cast Iron- Ji-Ook PARK, Tran Van LONG and Yasushi SASAKI Graduate Institute of Ferrous Technology (GIFT), Pohang University of Science and Technology (POSTECH), Hyoja-dong, Pohang, 790-784 South Korea. (Received on September 6, 2011; accepted on September 29, 2011) To meet the unprecedented demand of environmental issues and tightened production cost, steel industry must develop the disruptively innovative process. In the present study, totally new steelmaking process of ‘Solid State Steelmaking’ (or S3 process) without BOF process or liquid state oxidation process is proposed. The overview of the new process is as follows: (1) High carbon liquid iron from the ironmak- ing processes is directly solidified by using a strip casting process to produce high carbon thin sheets. (2) Then, the produced cast iron sheet is decarburized by introducing oxidizing gas of H2O or CO2 in a con- tinuous annealing line to produce low carbon steel sheets. The most beneficial aspect of the S3 process is the elimination of several steps such as BOF, and secondary refinement processes and no formation of inclusions. To investigate the feasibility of S3 process, the cast iron strips with various high carbon content produced by a centrifugal slip casting method are decarburized at 1 248 K and 1 373 K by using H2O–H2 gas mixture and its kinetics of the decarburization is investigated. In the decarburization process, the car- bon diffusion through the decarburized austenite phase but not the decomposition of cementite is the rate controlling step of the decarburizing process.