Relevant bibliographies by topics / Austenite

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  1. Journal articles
  2. Dissertations / Theses
  3. Books
  4. Book chapters
  5. Conference papers
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Academic literature on the topic 'Austenite'

Author: Grafiati
Published: 4 June 2021
Last updated: 30 November 2024

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Journal articles on the topic "Austenite"

1

Lu, Lilin, Jiaqi Ni, Zhixian Peng, Haijun Zhang, and Jing Liu. "Hydrogen Embrittlement and Improved Resistance of Al Addition in Twinning-Induced Plasticity Steel: First-Principles Study." Materials 12, no. 8 (April 24, 2019): 1341. http://dx.doi.org/10.3390/ma12081341.

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Understanding the mechanism of hydrogen embrittlement (HE) of austenitic steels and developing an effective strategy to improve resistance to HE are of great concern but challenging. In this work, first-principles studies were performed to investigate the HE mechanism and the improved resistance of Al-containing austenite to HE. Our results demonstrate that interstitial hydrogen atoms have different site preferences in Al-free and Al-containing austenites. The calculated binding energies and diffusion barriers of interstitial hydrogen atoms in Al-containing austenite are remarkably higher than those in Al-free austenite, indicating that the presence of Al is more favorable for reducing hydrogen mobility. In Al-free austenite, interstitial hydrogen atoms caused a remarkable increase in lattice compressive stress and a distinct decrease in bulk, shear, and Young’s moduli. Whereas in Al-containing austenite, the lattice compressive stress and the mechanical deterioration induced by interstitial hydrogen atoms were effectively suppressed.
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Berecz, Tibor, and Peter J. Szabo. "Crystallographic relations during decomposition of the ferritic phase by isothermal ageing of duplex stainless steel." Journal of Applied Crystallography 46, no. 1 (December 8, 2012): 135–41. http://dx.doi.org/10.1107/s0021889812044536.

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In highly alloyed and duplex stainless steels the range of alloying elements leads to many different phases precipitating at higher temperatures. Duplex stainless steels consist of almost equal ratios of austenite and ferrite, and between 923 and 1273 K the ferrite begins decomposing into secondary austenite (γ2) and the σ phase. Several orientation relations between the austenitic, ferritic and σ phases have been determined by other researchers. The calculation and testing of mathematical expressions for these orientations are important for a close understanding of changes in duplex steel hardness, ductility, and other qualitative measures imposed by annealing or heat ageing. The method described in this article also offers an approach for determining parent phase orientations from inherited orientations in other metallic microstructures. When the orientation relations of adjacent grains calculated from mathematical equations and those measured by electron backscatter diffraction were compared, naturally it was found that the average orientation differs less between grains that inherit matrix structure from common parents. However, it was also found that the degree of difference depended on the variants involved in the orientations. This phenomenon can be explained by features of the microstructure and decomposition of the ferritic phase: initially the microstructure contains only primary austenite (γ1) and ferrite, then after a while it contains [beside primary (γ1) austenite] increasing amounts of secondary (γ2) austenite and the σ phase, and decreasing amounts of ferrite. The presence of two variants of austenite makes it difficult to verify parent relations for secondary (γ2) austenites.
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Feng, Yun Li, Shao Qiang Yuan, and Meng Song. "Microstructure Evolution of Undercooled Austenite during Deformation for Medium-Carbon Si-Mn Steel." Materials Science Forum 704-705 (December 2011): 903–6. http://dx.doi.org/10.4028/www.scientific.net/msf.704-705.903.

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The microstructure evolution of a medium-carbon Si-Mn steel during deformation of undercooled austenite at different degree of deformation, temperatures and strain rates has been investigated by means of a hot compression simulation test, metallographic microscope, scanning electron microscope and transmission electron microscopy. Also, the mechanism of carbide spheroidized during deformed process has been discussed. The experiment results demonstrate that the process of evolution experienced three stages: that is, strain-induced transformation, austenite eutectoid decomposed to carbides and ferrite matrix, and spheroidization of pearlite at the range of A3-Ar3. The austenitic grains would be refined for the extra-product of ferrite above the Ar3. The eutectoid reaction was induced on the grain boundaries of ferrite and non-transformed austenite and deformation bands with the increasing volume of deformation. An optimum combination of deformation temperature and strain rate is important to obtian the dulplex microstructure consisting of ultrafine ferrites and dispersed carbide particles. The fine spheroidized microstructures are obtained while the deformed temperature reaches 650°C with ≥1.0, meanwhile, The carbides precipate in globular and shot-rod shapes. Keywords: Medium-carbon Si-Mn steel, Undercooled austentite, Microstructure evolution, Deformation induced transformation, Carbide spheroidization
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Reis, Adriano Gonçalves, Danieli Aparecida Pereira Reis, Antônio Jorge Abdalla, Antônio Augusto Couto, and Jorge Otubo. "An In Situ High-Temperature X-Ray Diffraction Study of Phase Transformations in Maraging 300 Steel." Defect and Diffusion Forum 371 (February 2017): 73–77. http://dx.doi.org/10.4028/www.scientific.net/ddf.371.73.

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An in situ high-temperature X-ray diffraction (HTXRD) study in maraging 300 steel was carried out to study the martensite to austenite transformation and effect of time of exposure in the austenite reversion below austenite start temperature. Solution annealed materials were subjected to controlled heating-holding cycles. The first sample was heated at a rate of 10 oC/min from room temperature to 800 oC, showing that the microstructure is completely martensitic (α’110) until 600 oC. From 650 oC until 800 oC, the microstructure is gradually changing from martensitic to austenitic, showed by the increasing peaks of γ111 and reducing peaks of α’110. At 800 oC the microstructure is completely austenitic (γ111). Another sample was heated at 10 oC/min from room temperature to 600 oC and held for 4 hours. At 600 oC, at 0 h time of exposure, only a martensitic peak was observed. An austenite peak can be observed after some time of exposure at this temperature. The volume fraction of austenite increased with increasing time of exposure at 600 oC, reaching 50/50 volume fraction after 4 hours of exposure. XRD diffraction patterns for the same sample that was held for 4 hours at 600 oC and then cooled down in air to room temperature showed the same intensity of austenite and martensitic peaks found in situ at 600 oC for 4 hours (retained austenite), with the volume fraction of 50/50 of austenite and martensite phases. The HTXRD technique can be used to identify and quantify martensite to austenite transformation and austenite retention.
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Gautam, J. Prakash, A. Miroux, Jaap Moerman, and Leo Kestens. "Tnr Dependent Hot Rolling Microstructure and Texture Development in C-Mn Dual Phase and HSLA Steels." Defect and Diffusion Forum 391 (February 2019): 120–27. http://dx.doi.org/10.4028/www.scientific.net/ddf.391.120.

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No recrystallization of austenite, Tnr, has an important influence on the transformed phase fractions and the final crystallographic texture after hot deformation. This paper investigates the evolution of microstructure and texture components during hot-rolling in two austenitic region based on Tnr along with three different cooling trajectory and coiling in dual-phase steels and high strength low alloys steel. The recrystallization of the austenite, the austenite deformation followed by the austenite-to-ferrite transformation influence the final microstructure and texture in dual phase steels, have been examined by means of optical microscopy, X-ray diffraction (XRD) measurements. Recrystallized and deformed austenite have clearly different texture components and, due to the specific lattice correspondence relations between the parent austenite phase and its transformation products, the resulting ferrite textures are different as well.
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Kawasaki, Yoshiyasu, Yuki Toji, Yokota Takeshi, and Yoshimasa Funakawa. "Effects of Tensile Testing Temperature on Mechanical Properties and Deformation Behavior in Medium Mn Steels." Materials Science Forum 1016 (January 2021): 1823–29. http://dx.doi.org/10.4028/www.scientific.net/msf.1016.1823.

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In single-phase austenitic steels, the optimum deformation temperature in the tensile test to obtain high tensile strength-elongation balance (TS×El) and work hardening rate (dσ/dε) depends on control of the stability of austenite. In order to clarify the effects of the deformation temperature in complex phase steels containing austenite, in this study, the effects of the tensile testing temperature on mechanical properties and deformation behavior were investigated in detail using steel A and steel B with a chemical composition of 0.15C-0.5Si-5.0Mn (wt%). Steels A and B consisted of ferrite and retained austenite, but contained different volume fractions of retained austenite, namely, 29 % and 17 % as a result of annealing at 660 °C and 620 °C for 2 h, respectively. The stability of the retained austenite of steel B was higher than that of steel A. In steel A, TS×El and dσ/dε achieved their maximum values at 20 °C, decreased from 20 to 100 °C, and then remained almost unchanged at more than 150 °C. On the other hand, in steel B, TS×El and dσ/dε achieved their maximum values at -40 °C, decreased from -40 to 50 °C and remained almost unchanged at more than 100 °C. These results can be explained by the stability of retained austenite and the transformation rate from retained austenite to martensite. It should be noted that control of the stability of retained austenite and the transformation rate from retained austenite to martensite led to an adjustment of the optimum deformation temperature to achieve the high TS×El and dσ/dε in medium Mn steels, in the same manner as in single-phase austenitic steels.
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Silva Leite, Carla Gabriela, Eli Jorge da Cruz Junior, Mattia Lago, Andrea Zambon, Irene Calliari, and Vicente Afonso Ventrella. "Nd: YAG Pulsed Laser Dissimilar Welding of UNS S32750 Duplex with 316L Austenitic Stainless Steel." Materials 12, no. 18 (September 9, 2019): 2906. http://dx.doi.org/10.3390/ma12182906.

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Duplex stainless steels (DSSs), a particular category of stainless steels, are employed in all kinds of industrial applications where excellent corrosion resistance and high strength are necessary. These good properties are provided by their biphasic microstructure, consisting of ferrite and austenite in almost equal volume fractions of phases. In the present work, Nd: YAG pulsed laser dissimilar welding of UNS S32750 super duplex stainless steel (SDSS) with 316L austenitic stainless steel (ASS), with different heat inputs, was investigated. The results showed that the fusion zone microstructure observed consisted of a ferrite matrix with grain boundary austenite (GBA), Widmanstätten austenite (WA) and intragranular austenite (IA), with the same proportion of ferrite and austenite phases. Changes in the heat input (between 45, 90 and 120 J/mm) did not significantly affect the ferrite/austenite phase balance and the microhardness in the fusion zone.
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Pinedo, Carlos Eduardo, and André Paulo Tschiptschin. "Low temperature plasma carburizing of AISI 316L austenitic stainless steel and AISI F51 duplex stainless steel." Rem: Revista Escola de Minas 66, no. 2 (June 2013): 209–14. http://dx.doi.org/10.1590/s0370-44672013000200011.

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In this work an austenitic AISI 316L and a duplex AISI F51 (EN 1.4462) stainless steel were DC-Plasma carburized at 480ºC, using CH4 as carbon carrier gas. For the austenitic AISI 316L stainless steel, low temperature plasma carburizing induced a strong carbon supersaturation in the austenitic lattice and the formation of carbon expanded austenite (γC) without any precipitation of carbides. The hardness of the carburized AISI 316L steel reached a maximum of 1000 HV due to ∼13 at% carbon supersaturation and expansion of the FCC lattice. For the duplex stainless steel AISI F51, the austenitic grains transformed to carbon expanded austenite (γC), the ferritic grains transformed to carbon expanded ferrite (αC) and M23C6 type carbides precipitated in the nitrided case. Hardness of the carburized case of the F51 duplex steel reached 1600 HV due to the combined effects of austenite and ferrite lattice expansion with a fine and dispersed precipitation of M23C6 carbides.
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Kang, Jun-Yun, Jaecheol Yun, Byunghwan Kim, Jungho Choe, Sangsun Yang, Seong-Jun Park, Ji-Hun Yu, and Yong-Jin Kim. "Micro-Texture Analyses of a Cold-Work Tool Steel for Additive Manufacturing." Materials 13, no. 3 (February 9, 2020): 788. http://dx.doi.org/10.3390/ma13030788.

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Small objects of an alloy tool steel were built by selective laser melting at different scan speeds, and their microstructures were analyzed using electron backscatter diffraction (EBSD). To present an explicit correlation with the local thermal cycles in the objects, prior austenite grains were reconstructed using the EBSD mapping data. Extensive growth of austenitic grains after solidification could be detected by the disagreement between the networks of carbides and austenite grain boundaries. A rapid laser scan at 2000 mm/s led to less growth, but retained a larger amount of austenite than a slow one at 50 mm/s. The rapid scan also exhibited definite evolution of Goss-type textures in austenite, which could be attributed to the growth of austenitic grains under a steep temperature gradient. The local variations in the microstructures and the textures enabled us to speculate the locally different thermal cycles determined by the different process conditions, that is, scan speeds.
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Stone, H. J., M. J. Peet, H. K. D. H. Bhadeshia, P. J. Withers, S. S. Babu, and E. D. Specht. "Synchrotron X-ray studies of austenite and bainitic ferrite." Proceedings of the Royal Society A: Mathematical, Physical and Engineering Sciences 464, no. 2092 (January 29, 2008): 1009–27. http://dx.doi.org/10.1098/rspa.2007.0201.

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High-resolution synchrotron X-ray diffraction has been used to conduct in situ studies of the temporal evolution of phases during the isothermal growth of bainite. Two populations of austenitic material were identified: one corresponding to the initial austenite and the other to the carbon-enriched austenite associated with the bainitic ferrite. The observed lattice parameters and the asymmetry of the peaks from the residual austenite have been interpreted in terms of the carbon partitioning due to the transformation. The results are contrasted with an earlier study in which the austenite unit cell appeared to split into two distinct densities prior to the onset of transformation.
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Dissertations / Theses on the topic "Austenite"

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Del, Sant Ricardo. "Estudo da transformação da austenita retida em martensita induzida por deformação plástica em aços multifásicos /." Guaratinguetá : [s.n.], 2010. http://hdl.handle.net/11449/103753.

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Orientador: Tomaz Manabu Hashimoto
Banca: Marcelo dos Santos Pereira
Banca: Alfeu Saraiva Ramos
Banca: Jorge Otubo
Banca: Rosinei Batista Ribeiro
Resumo: Os aços multifásicos constituídos de ferrita, bainita, austenita retida e martensita apresentam combinações muito atrativas de resistência e tenacidade. Há ainda um potencial adicional de melhorias de propriedades mecânicas quando a fração de austenita retida for alta, conferindo alta conformabilidade pelo efeito TRIP. Neste contexto, é fundamental a análise qualitativa e quantitativa das fases, especialmente de austenita retida e sua transformação em martensita induzida por deformação. Este trabalho enfoca a transformação da austenita retida em martensita por deformação em tração monotônica em um aço AISI 4340 com estrutura multifásica. Os resultados confirmam a transformação da austenita retida em martensita atingindo cerca de 80% de transformação. As frações volumétricas de austenita retida antes e após a deformação foram estimadas por duas técnicas. A primeira foi feita por análise de imagens em microscopia óptica e a segunda por magnetização de saturação, tendo em vista o caráter paramagnético desta fase. As frações estimadas pelas duas técnicas foram comparadas, concluindo-se que o método magnético deve ser reavaliado, tendo sido proposto um fator de correção na equação básica deste processo e presenta na literatura.
Abstract: The multiphase steels made of ferrite, bainite, retained austenite and martensite present very attractive combinations and toughness. There is still an additional potential of improvement of the mechanical properties when the fraction of retained austenite is high allowing high conformability by the TRIP effect. In this context the qualitative and quantitative analysis of the phases is essentual specially from retained austenite and its transformation in martensite induced by deformation. This work focus on the transformation of retained austenite in martensite by the deformation in monotonic traction in one steel AISI 4340 with multiphasic structure. The results confirm the transformation of retained in martensite reaching about 80% of transformation. The volumetric of retained austenite before and after the deformation were estimated by two technique: the first was made by the anllysis of images in optic microscopy and the second by magnetization of saturation taking into consideration the paramagnetica character of this phase. The estimated fraction by the two technique were compared leading to the conclusion that the magnetic method must be evaluated again using a proposed factor of correction in the basic equation of this process and present in the literature.
Doutor
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2

Singh, Shiv Brat. "Phase transformations from deformed austenite." Thesis, University of Cambridge, 1998. http://ethos.bl.uk/OrderDetails.do?uin=uk.bl.ethos.246513.

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Evteev, Alexander V., Elena V. Levchenko, Irina V. Belova, and Graeme E. Murch. "Carbon diffusion in austenite: computer simulation and theoretical analysis: Carbon diffusion in austenite: computer simulation andtheoretical analysis." Diffusion fundamentals 6 (2007) 16, S. 1-2, 2007. https://ul.qucosa.de/id/qucosa%3A14190.

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4

Leguen, Claire. "Prior Austenite Grain Size Controlled by Precipitates." Phd thesis, INSA de Lyon, 2010. http://tel.archives-ouvertes.fr/tel-00511322.

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During this study, the correlation between the evolution of the prior austenitic grain size and of the precipitation state during thermal treatment performed on steels is presented. To do this, the precipitation state has been finely characterized. Precipitate volume fractions were measured by plasma spectroscopy. Transmission Electron Microscopy (TEM) was used to determine the precipitate size distributions (HAADF images) and the precipitate chemical composition (EDX, EELS for carbon and nitrogen). In order to treat ELLS spectra obtained on complex carbonitrides (V,Nb,Ti)(C,N), a routine based on the Least Mean square Fitting have been developed. Results obtained with this method are in gopd agreement with those obtained by EDX analysis for metallic elements (Nb, V, Ti, ...). Then, grain size distributions were determined using a special etching called "Bechet-Beaujard", which reveals the prior austenite grain boundaries. Two alloys have been characterized in this study. (i) A model alloy, the FeVNbCN, which presents two precipitate types, NbC and VCN. This alloy was chosen to study the role of nitrogen on the precipitation state during reversion treatments. A model predicting the precipitation kinetics, coupled with a model for grain growth, give a good agreement with experimental results on grain sizes, precipitate sizes and on precipitate volume fraction. (ii) An industrial steel, the 16MnCr5+Nb was also studied. This alloy exhibits the presence of AlN and NbC precipitates. The correlation obtained between the Prior Austenite Grain Size and the evolution of the precipitation state shows that a large volume fraction of small precipitates allows a great pinning of grain boundaries. Finally, during thermo-mechanical treatments performed in the industry, some large grains may grow faster than smaller grains, leading to the so-called abnormal grain growth. This kind of growth can lead to undesirable mechanical instabilities. We have developed a criterium for abnormal grain growth which predicts the risk of such growth for a given precipitation state. This model presents a good agreement with all experimental results for both studied alloys.
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Stormvinter, Albin. "Low Temperature Austenite Decomposition in Carbon Steels." Doctoral thesis, KTH, Metallografi, 2012. http://urn.kb.se/resolve?urn=urn:nbn:se:kth:diva-100993.

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Martensitic steels have become very important engineering materials in modern society. Crucial parts of everyday products are made of martensitic steels, from surgical needles and razor blades to car components and large-scale excavators. Martensite, which results from a rapid diffusionless phase transformation, has a complex nature that is challenging to characterize and to classify. Moreover the possibilities for modeling of this phase transformation have been limited, since its thermodynamics and kinetics are only reasonably well understood. However, the recent development of characterization capabilities and computational techniques, such as CALPHAD, and its applicability to ferrous martensite has not been fully explored yet. In the present work, a thermodynamic method for predicting the martensite start temperature (Ms) of commercial steels is developed. It is based mainly on information on Ms from binary Fe-X systems obtained from experiments using very rapid cooling, and Ms values for lath and plate martensite are treated separately. Comparison with the experimental Ms of several sets of commercial steels indicates that the predictive ability is comparable to models based on experimental information of Ms from commercial steels. A major part of the present work is dedicated to the effect of carbon content on the morphological transition from lath- to plate martensite in steels. A range of metallographic techniques were employed: (1) Optical microscopy to study the apparent morphology; (2) Transmission electron microscopy to study high-carbon plate martensite; (3) Electron backscattered diffraction to study the variant pairing tendency of martensite. The results indicate that a good understanding of the martensitic microstructure can be achieved by combining qualitative metallography with quantitative analysis, such as variant pairing analysis. This type of characterization methodology could easily be extended to any alloying system and may thus facilitate martensite characterization in general. Finally, a minor part addresses inverse bainite, which may form in high-carbon alloys. Its coupling to regular bainite is discussed on the basis of symmetry in the Fe-C phase diagram.

QC 20120824


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Tafteh, Reza. "Austenite decomposition in an X80 linepipe steel." Thesis, University of British Columbia, 2011. http://hdl.handle.net/2429/34583.

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The final microstructure and resulting mechanical properties in the heat-affected zone (HAZ) of welded linepipes are predominantly determined by austenite decomposition during cooling after welding processes. Thus, a full understanding of continuous cooling transformation of austenite is a key step toward improving the overall performance of linepipes. The main objective of the current study is to investigate the influence of cooling rate, prior austenite grain size and niobium content of austenite on austenite decomposition kinetics and the resulting microstructures for an X80 linepipe steel. To consider the significant effect of the niobium solid solution level on the transformation of austenite, two thermal histories were developed. For the first case, Nb was dissolved in solid solution prior to austenite decomposition. In contrast, the second scenario involved the formation of Nb(C,N) precipitates prior to austenite decomposition, i.e. leaving a low level of Nb in solid solution. Austenite grain growth studies were conducted to obtain grain sizes similar to those observed in the HAZ of the girth-welded steel, i.e. 5-80μm. Furthermore, employing appropriate thermal cycles, continuous cooling transformation (CCT) tests were conducted to examine the effect of niobium condition, austenite grain size and cooling rate on austenite decomposition behavior of the steel. Cooling rates varied in the range of 3−100ºC/s and dilation measurements were utilized to capture the transformation kinetics of austenite upon cooling. The resulting microstructures, which usually consist of ferrite, bainite and martensite-austenite (MA) constituents, were examined using optical microscopy. They were revealed using appropriate etchants and the corresponding phase volume fractions were subsequently measured in accordance with ASTM standards. Hardness measurements were also conducted on CCT samples.
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Kaya, Ali Arslan. "Decomposition of austenite in high chromium steels." Thesis, University of Oxford, 1993. http://ethos.bl.uk/OrderDetails.do?uin=uk.bl.ethos.316869.

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Del, Sant Ricardo [UNESP]. "Estudo da transformação da austenita retida em martensita induzida por deformação plástica em aços multifásicos." Universidade Estadual Paulista (UNESP), 2010. http://hdl.handle.net/11449/103753.

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Os aços multifásicos constituídos de ferrita, bainita, austenita retida e martensita apresentam combinações muito atrativas de resistência e tenacidade. Há ainda um potencial adicional de melhorias de propriedades mecânicas quando a fração de austenita retida for alta, conferindo alta conformabilidade pelo efeito TRIP. Neste contexto, é fundamental a análise qualitativa e quantitativa das fases, especialmente de austenita retida e sua transformação em martensita induzida por deformação. Este trabalho enfoca a transformação da austenita retida em martensita por deformação em tração monotônica em um aço AISI 4340 com estrutura multifásica. Os resultados confirmam a transformação da austenita retida em martensita atingindo cerca de 80% de transformação. As frações volumétricas de austenita retida antes e após a deformação foram estimadas por duas técnicas. A primeira foi feita por análise de imagens em microscopia óptica e a segunda por magnetização de saturação, tendo em vista o caráter paramagnético desta fase. As frações estimadas pelas duas técnicas foram comparadas, concluindo-se que o método magnético deve ser reavaliado, tendo sido proposto um fator de correção na equação básica deste processo e presenta na literatura.
The multiphase steels made of ferrite, bainite, retained austenite and martensite present very attractive combinations and toughness. There is still an additional potential of improvement of the mechanical properties when the fraction of retained austenite is high allowing high conformability by the TRIP effect. In this context the qualitative and quantitative analysis of the phases is essentual specially from retained austenite and its transformation in martensite induced by deformation. This work focus on the transformation of retained austenite in martensite by the deformation in monotonic traction in one steel AISI 4340 with multiphasic structure. The results confirm the transformation of retained in martensite reaching about 80% of transformation. The volumetric of retained austenite before and after the deformation were estimated by two technique: the first was made by the anllysis of images in optic microscopy and the second by magnetization of saturation taking into consideration the paramagnetica character of this phase. The estimated fraction by the two technique were compared leading to the conclusion that the magnetic method must be evaluated again using a proposed factor of correction in the basic equation of this process and present in the literature.
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Carvalho, Leandro Gomes de. "Estudo dilatométrico das transformações de fase em aços maraging M300 e M350." Universidade de São Paulo, 2011. http://www.teses.usp.br/teses/disponiveis/3/3133/tde-26032012-112344/.

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Os aços maraging são aços de baixo teor de carbono com estrutura martensítica (CCC), que são endurecidos pela precipitação de fases intermetálicas. O objetivo deste trabalho é estudar as transformações de fases desses aços: precipitação, reversão da martensita para a austenita e transformação martensítica. Nesse trabalho, foram caracterizadas uma corrida de aço maraging da série 300 e três corridas da série 350, usando diversas técnicas complementares: microscopia ótica, microscopia eletrônica de varredura com análise dispersiva de energia, microdurômetro, difração de raios-X, ferritoscópio e dilatometria. Os resultados obtidos mostraram que as corridas com maiores teores de cobalto e titânio apresentaram maiores valores de microdureza nos estados solubilizado e envelhecido. Por outro lado, medidas dilatométricas mostraram que há uma influência significativa tanto da composição química, quanto da taxa de aquecimento nas reações de precipitação e reversão da martensita para a austenita. No entanto, a transformação martensítica mostrou-se dependente apenas da taxa de aquecimento.
Maraging steels are steels with a low carbon martensitic structure (BCC), which are hardened by precipitation of intermetallic phases. The aim of this work is to study the phase transformations of these steels: precipitation, martensite to austenite reversion and martensitic transformation. In this study, one cast of 300 grade and three casts of 350 grade were characterized using several complementary techniques: optical microscopy, scanning el ectron microscopy with energy dispersive analysis, microhardness, X-ray diffraction, ferritoscope and dilatometry. The results showed that the casts with higher concentrations of cobalt and titanium showed higher microhardness in the solution annealed and aged states. On the other hand, dilatometry measurements showed that there is a significant influence of both the chemical composition and the heating rate on the reactions of precipitation and reversion of martensite to austenite. However, the martensitic transformation was dependent solely on the heating rate.
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10

Riehm, Derek J. "Kinetics of the pearlite to austenite reversion transformation." Thesis, University of British Columbia, 1990. http://hdl.handle.net/2429/29739.

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The pearlite-to-austenite reversion transformation kinetics under isothermal and continuous heating conditions in a eutectoid plain-carbon steel have been measured, using a dilatometric technique on a Gleeble 1500 Thermomechanical Simulator. The isothermal data was characterized in terms of the transformation start time at temperature for the onset of the P→ γ transformation, and in terms of the Avrami parameters n and b. Under the assumption that the P→ γ transformation was additive, the Scheil equation was applied to the measured isothermal transformation start data to predict the onset of the transformation on continuous heating, and the isothermal phase transformation kinetics were used to predict the continuous heating kinetics. It was found that the kinetic model significantly underpredicted the transformation start time during continuous heating. This was attributed to the large experimental error inherent in the estimation of the isothermal transformation start time, t[formula omitted]. The model's continuous heating kinetic predictions were excellent at low heating rates, but it tended to overpredict the kinetics at higher heating rates. The problem was traced to an observed difference between the measured temperature and the programmed temperature during the high heating rate tests. When the model was modified to incorporate the actual temperature profile, its prediction of the kinetics was considerably improved. Thus the austenite reversion transformation was concluded to be experimentally additive. An average Avrami n value of 2.2 suggested that austenite was nucleating on pearlite colony corners and edges. This conclusion was verified with optical and scanning electron microscopy. Previously published data, which indicated that the pearlite-to-austenite transformation is isokinetic, was found to be based on questionable assumptions. Metallographic information suggests, however, that the nucleation sites are saturated early in the reaction. Furthermore, the isothermal austenite formation data generated in this work was found to meet the effective site saturation criterion for additivity, implying that the austenitization process would be expected to be additive. The effect of starting microstructure was evaluated by performing isothermal and continuous heating tests on two different pearlitic microstructures. It was found that, in agreement with published results, the transformation rate varied in inverse proportion with the pearlite spacing and colony size.
Applied Science, Faculty of
Materials Engineering, Department of
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Books on the topic "Austenite"

1

Jeleńkowski, Jerzy. Przemiana martenzytu w austenit w stopach Fe-(23-26) Ni-(2-3)ti-(Nb) z dodatkami aluminium lub molibdenu. Warszawa: Oficyna Wydawnicza Politechniki Warszawskiej, 1996.

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N, Gotalʹskiĭ I͡U. Svarka perlitnykh staleĭ austenitnymi materialami. 2nd ed. Kiev: Nauk. dumka, 1992.

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Ibraheem, A. K. Precipitation in the austenite of microalloyed low carbon steel. Manchester: UMIST, 1995.

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Buddy, Damm E., Merwin Matthew J, Iron and Steel Society of AIME. Product Physical Metallurgy Committee., and Minerals, Metals and Materials Society. Materials Processing and Manufacturing Division. Phase Transformations Committee., eds. Austenite formation and decomposition: Proceedings of symposia : held at the Materials, Science & Technology 2003 Meeting in Chicago, Illinois, USA, November 9-12, 2003. Warrendale, Pa: TMS, 2003.

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Janus, Andrzej. Kształtowanie struktury odlewów z austenitycznego żeliwa Ni-Mn-Cu: Forming cast structure of austenitic nickel-manganese-copper cast iron. Wrocław: Oficyna Wydawnicza Politechniki Wrocławskiej, 2013.

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Brooks, Charlie R. Principles of the austenitization of steels. London: Elsevier Applied Science, 1992.

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Saleh, M. Husin Bin. Retained austenite in dual phase steel and its effect on mechanical properties. Manchester: UMIST, 1998.

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Patel, Pratful. Modelling the recrystallisation-stop temperature of vanadium austenite by single pass rolling. Manchester: UMIST, 1997.

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Fookes, B. G. Factors influencing the sub-critical decomposition of austenite in iron-silicon-carbon alloys. Uxbridge: BrunelUniversity, 1985.

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Ryś, Janusz. Krystalograficzne aspekty oddziaływania ferrytu i austenitu w bikryształach i stalach dwufazowych: Crystallographic aspects of ferrite and austenite interaction in two-phase steels and bicrystals. Kraków: Wydawnictwa AGH, 2013.

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Book chapters on the topic "Austenite"

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Durand-Charre, Madeleine. "The decomposition of austenite." In Microstructure of Steels and Cast Irons, 179–93. Berlin, Heidelberg: Springer Berlin Heidelberg, 2004. http://dx.doi.org/10.1007/978-3-662-08729-9_9.

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Samoilov, Andrej, Yuri Titovets, Nikolay Zolotorevsky, Gottfried Hribernig, and Andreas Pichler. "Modeling the Effect of Austenite Grain Size Distribution on Austenite Decomposition Kinetics." In THERMEC 2006, 4584–89. Stafa: Trans Tech Publications Ltd., 2007. http://dx.doi.org/10.4028/0-87849-428-6.4584.

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Sawaguchi, Takahiro. "Designing High-Mn Steels." In The Plaston Concept, 237–57. Singapore: Springer Nature Singapore, 2022. http://dx.doi.org/10.1007/978-981-16-7715-1_11.

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AbstractHigh-Mn austenitic steels undergo characteristic plasticity mechanisms of the γ-austenite with an FCC structure, such as extended dislocation glide, mechanical twinning, and mechanical martensitic transformation into ε-martensite with an HCP structure and/or α’-martensite with a BCC/BCT structure. Distortions of polyhedron models are used to describe these plasticity mechanisms. These are the smallest volumetric units occupying the lattices and reflect the crystallographic characteristics of the lattices. The complicated crossing shears are correlated to the fine crystal phases formed at the intersection of the ε-martensite variants. The unidirectionality of the {1 1 1} < 1 1 2 > γ twinning shear provides reversibility to the dislocation motion under cyclic loading. Based on this knowledge, the design concept of high-Mn steels is described considering microstructural, thermodynamic, and crystallographic characteristics.
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Hao, Wang, Liu Guoquan, and Xu Kuangdi. "Austenite, Structure and Characteristic of." In The ECPH Encyclopedia of Mining and Metallurgy, 1. Singapore: Springer Nature Singapore, 2022. http://dx.doi.org/10.1007/978-981-19-0740-1_100-1.

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Hao, Wang, and Liu Guoquan. "Austenite, Structure and Characteristic of." In The ECPH Encyclopedia of Mining and Metallurgy, 96–97. Singapore: Springer Nature Singapore, 2024. http://dx.doi.org/10.1007/978-981-99-2086-0_100.

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Zhenbao, Sun. "Transformation Diagram of Undercooled Austenite." In The ECPH Encyclopedia of Mining and Metallurgy, 2193–98. Singapore: Springer Nature Singapore, 2024. http://dx.doi.org/10.1007/978-981-99-2086-0_1058.

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Zhenbao, Sun, and Xu Kuangdi. "Transformation Diagram of Undercooled Austenite." In The ECPH Encyclopedia of Mining and Metallurgy, 1–6. Singapore: Springer Nature Singapore, 2023. http://dx.doi.org/10.1007/978-981-19-0740-1_1058-1.

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An, Dong, Shiyan Pan, Qing Yu, Chen Lin, Ting Dai, Bruce Krakauer, and Mingfang Zhu. "Modeling of Ferrite-Austenite Phase Transformation." In TMS2015 Supplemental Proceedings, 791–98. Hoboken, NJ, USA: John Wiley & Sons, Inc., 2015. http://dx.doi.org/10.1002/9781119093466.ch96.

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An, Dong, Shiyan Pan, Qing Yu, Chen Lin, Ting Dai, Bruce Krakauer, and Mingfang Zhu. "Modeling of Ferrite-Austenite Phase Transformation." In TMS 2015 144th Annual Meeting & Exhibition, 791–98. Cham: Springer International Publishing, 2015. http://dx.doi.org/10.1007/978-3-319-48127-2_96.

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Li, Jian, and Pei Liu. "Austenite Stability Under Focused Ion Beam Milling." In The Minerals, Metals & Materials Series, 81–88. Cham: Springer International Publishing, 2020. http://dx.doi.org/10.1007/978-3-030-36628-5_8.

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Conference papers on the topic "Austenite"

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Sumiya, Kenzo, Shinkichi Tokuyama, Tatsuyuki Aoki, Junichi Fukui, Atsushi Nishiyama, and Akio Nishimoto. "Active-Screen Plasma Nitriding of an Austenitic Stainless Steel Small Thin Rolled Plate." In IFHTSE 2024, 139–44. ASM International, 2024. http://dx.doi.org/10.31399/asm.cp.ifhtse2024p0139.

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Abstract The purpose of this study is to clarify the mechanical properties of the expanded austenite (S phase) formed in austenitic stainless steel (ASS). A small thin rolled plate of SUS304 with 0.5 mm thickness was used as test sample. The test sample was nitrided by active screen plasma nitriding (ASPN) at low processing temperature of 400 °C and 450 °C during 4 h processing time. S phase was formed on the surface of the test sample. The surface hardness of ASPN sample was higher than that of untreated sample. Furthermore, tensile tests and fracture surface observations revealed that the tensile strength was also improved compared to untreated samples.
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Mohr, A., O. Schwabe, K. Ernst, H. Hill, and P. Kluge. "Thermal Spraying of a Novel Nickel-Free High Strength and Corrosion Resistant Austenitic Steel." In ITSC2022. DVS Media GmbH, 2022. http://dx.doi.org/10.31399/asm.cp.itsc2022p0631.

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Abstract Stainless austenitic steels like the 316L (1.4404) are widely applied in various applications and were also used for surface protection using thermal spraying. The reason for this is the easy processability and the high corrosion resistance. Stainless austenitic steels typically contain the following alloying elements: The formation of an austenitic microstructure is achieved by nickel (Ni). The addition of chromium (Cr) lead to good corrosion resistance due to formation of an oxide layer. For resistance against pitting corrosion, molybdenum (Mo) can be added. Also, stainless austenites usually exhibit very low carbon and nitrogen contents to prevent chromium carbides and nitrides which reduces the corrosion resistance. However, both alloying elements cannot be classified as being detrimental in stainless austenites in general. In contrast high nitrogen contents can also be used to improve the chemical properties, especially the resistance against pitting corrosion. Finally, carbon and nitrogen lead to an increase in hardness of the thermal sprayed layer. Based on this knowledge, a high-strength austenite for thermal spraying was developed. The new high strength austenite was processed by HVAF spraying with different particle distributions and parameter variations. Resulting coatings were investigated regarding the microstructure, elemental composition, hardness and corrosion properties in comparison to the standard coating material 316L.
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Daniel, Tobias, Annika Boemke, Marek Smaga, and Tilmann Beck. "Investigations of Very High Cycle Fatigue Behavior of Metastable Austenitic Steels Using Servohydraulic and Ultrasonic Testing Systems." In ASME 2018 Pressure Vessels and Piping Conference. American Society of Mechanical Engineers, 2018. http://dx.doi.org/10.1115/pvp2018-84639.

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To investigate the fatigue behavior of metastable austenite steels in the VHCF-regime, high loading frequencies are essential to realize acceptable testing times. Hence, two high-frequency testing systems were used at the authors’ institute: an ultrasonic testing system with a test frequency of 20 000 Hz and also, a servohydraulic system with a test frequency of 980 Hz. In the present study, two different batches of the metastable austenitic stainless steel AISI 347 were investigated. Fatigue tests on metastable austenitic steel AISI 347 batch A were carried out at an ultrasonic test system at a test frequency of 20 000 Hz, at ambient temperature. Because the test rig acts as a mechanical resonant circuit excited by a piezoelectric transducer the specimen must be designed for oscillation in its vibration Eigenmode at the test frequency to assure maximum displacement at the end and maximum stress in the gauge length center, respectively. For analyzing the deformation behavior during the tests, the change in temperature was measured. Additionally, Feritscope™ measurements at the specimen surface were performed ex-situ after defined load cycles. First results showed a pronounced development of phase transformation from paramagnetic face-centered cubic γ-austenite to ferromagnetic body-centered cubic α‘-martensite. Because formation of α‘-martensite influences the transient behavior and high frequency loadings leads to pronounced self-heating of the material, ultrasonic fatigue tests on metastable austenites represent a challenge in controlling of displacement amplitude and limiting the specimen temperature. First investigations on metastable austenitc steel AISI 347 batch B using a servohydraulic test system at a frequency of 980 Hz and a temperature of T = 300 °C resulted in no fatigue failure beyond N = 107 cycles in the VHCF-regime. However, only specimens with a low content of cyclic deformation-induced α‘-martensite achieved the ultimate number of cycles (Nu = 5·108).
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Paidar, V. "Mechanisms of austenite-martensite transition." In ESOMAT 2009 - 8th European Symposium on Martensitic Transformations. Les Ulis, France: EDP Sciences, 2009. http://dx.doi.org/10.1051/esomat/200902026.

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Makhneva, Tatyana, Arkadiy Sukhikh, Vyacheslav Dementyev, and Sergey Makarov. "Segregated austenite in maraging steel." In PROCEEDINGS OF THE V INTERNATIONAL SCIENTIFIC CONFERENCE ON ADVANCED TECHNOLOGIES IN AEROSPACE, MECHANICAL AND AUTOMATION ENGINEERING: (MIST: Aerospace-V 2023). AIP Publishing, 2024. http://dx.doi.org/10.1063/5.0199904.

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Yu, Haixuan, Yuan Lu, Xiaoqing Cai, and Richard D. Sisson. "The Effects of Tempering on the Structure of Martensite in 52100 Steel." In HT 2015. ASM International, 2015. http://dx.doi.org/10.31399/asm.cp.ht2015p0060.

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Abstract To experimentally investigate the effect of tempering temperature and time on the structure and composition of Martensite, AISI 52100 was Austenized at 1000°C for 40 minutes and quenched in agitated water at 21°C. The as-quenched steel contained body-centered tetragonal (BCT) Martensite with 22% retained Austenite. These samples were tempered at 100°C, 200°C and 300°C with different holding time and characterized by X-ray Diffraction (XRD) to determine the effect on the structure of the Martensite. It was found that the content of retained Austenite didn’t change after tempering at 100°C. Retained Austenite decomposed after tempering for 40 minutes at 300°C. The change of crystal structure and lattice parameter for tempered Martensite with different holding time and temperature were measured. The effect of sample preparation on retained Austenite measurement and structure of Martensite and tempered Martensite was evaluated. An effective technique for carbides extraction and collection in steel was introduced.
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Eskandari Sabzi, Hossein, Andrew Hamilton, Xinjiang Hao, and Pedro E. J. Rivera-Díaz-del-Castillo. "Transformation-Induced Plasticity In Additively Manufactured Tool Steel." In Euro Powder Metallurgy 2024 Congress & Exhibition. EPMA, 2024. http://dx.doi.org/10.59499/ep246228829.

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There are significant challenges in the additive manufacturing (AM) of high-performance steels susceptible to transformation-induced plasticity (TRIP) effect. This is a mechanically-induced martensitic transformation of retained austenite distributed in a ferritic or martensitic matrix. Austenite stabilisation and retention at room temperature is of paramount significance to promote TRIP. It was discovered that austenite could be effectively retained due to carbide precipitation during AM. The ultimate tensile strength then increases significantly as a result of this metastable austenite's gradual transformation into ε-martensite under straining, while exhibiting a high yield strength. The partitioning of stress and strain, which is constantly changing as the hard martensite forms, is the cause of this rise, as revealed by microscopy techniques and X-ray diffraction.
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Hashimoto, Tadafumi, Shigetaka Okano, Shinro Hirano, Masahito Mochizuki, and Kazutoshi Nishimoto. "Residual Stress by X-Ray Diffraction and Microstructure for Multi-Pass Girth Welded Pipe Joint in Austenitic Stainless Steel Type 316L." In ASME 2011 Pressure Vessels and Piping Conference. ASMEDC, 2011. http://dx.doi.org/10.1115/pvp2011-57434.

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Residual stress due to welding can result in brittle fracture, fatigue failure, and stress corrosion cracking in welded structures. Measuring residual stresses are of great importance, if crack propagation needs to be evaluated. However, it is especially known that the X-ray diffraction method makes remarkable different for austenitic stainless steel, because the microstructures in welds change from the original microstructures during welding thermal cycle. That is, there are the preferred orientation due to the unidirectional solidification and the grain growth in the heat-affected zone. In order to average the sin2Ψ plots to exclude them, Ψ oscillation of ±3 deg was performed and the incident beam size was broadened to 4 by 4 mm. Consequently, typical residual stress distributions due to welding were obtained to various conditions. The residual stress distribution measured by X-ray diffraction agrees very well with that the estimated by thermal-elastic-plastic analysis, if the spatial resolution is correlated. It is attributed that the δ-ferrite grows as the primary phase and the austenite precipitates or crystallizes as the secondary phase. When the secondary austenite nucleates with the Kurdjiumov-Sachs relationship which satisfy δ{110}//γ{111} and δ&lt;111&gt;//γ&lt;110&gt;, plate-like austenite grows randomly into the ferrite and austenite grains are braked up. That is, Specific systems in austenitic stainless steels should be classified, as a material that residual stress can be measured accurately by X-ray diffraction.
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Spiegel, Michael, and Patrik Schraven. "Power Austenite- A Novel σ-Phase Hardened High Temperature Alloy for 700 °C (1292 °F) Fired Boilers." In AM-EPRI 2016, edited by J. Parker, J. Shingledecker, and J. Siefert. ASM International, 2016. http://dx.doi.org/10.31399/asm.cp.am-epri-2016p0304.

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Abstract The article gives a brief overview of the newly developed austenitic material “Power Austenite”. The microstructure of the Power Austenite is characterized by grain boundary strengthening with boron stabilized M23(C,B)6 and secondary Nb(C,N) in combination with sigma phase and Nb(C,N) as the major grain strengthening precipitates. The material shows a significant creep strength at 700 °C (1292 °F) and 650 °C (1202 °F) as well as fireside corrosion resistance which makes it a possible candidate for 700 °C (1292 °F) power plants.
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PSODA, M., and R. SOT. "RETAINED AUSTENITE DETERMINATION IN ROLLING BEARINGS." In Proceedings of the XVIII Conference. WORLD SCIENTIFIC, 2001. http://dx.doi.org/10.1142/9789812811325_0048.

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Reports on the topic "Austenite"

1

Williams, D., and W. Maxey. NR198506 Evaluation of an X70 Low-Carbon Bainitic-Steel Pipe. Chantilly, Virginia: Pipeline Research Council International, Inc. (PRCI), October 1985. http://dx.doi.org/10.55274/r0011411.

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A 24-inch-diameter x 0.75-inch-wall X70 low-carbon bainitic-steel pipe was evaluated to obtain an independent measurement of pipe properties and to examine metallurgical characteristics that may affect behavior in gas-transmission service. The steel from which the pipe was produced was processed using advanced steelmaking methods to insure cleanliness but apparently was not treated for sulfide shape control since no sour gas exposure in service was anticipated. Primary microalloying additions in this high manganese steel, other than columbium, were titanium and boron. Titanium was added to form a TiN dispersion during continuous casting to aid in the control of austenite grain size during slab rolling. Boron was added to suppress the transformation of austenite to ferrite or pearlite during and following controlled rolling, so as to promote formation of bainite. Heavy controlled rolling at temperatures below the austenite recrystallization temperature, and finish rolling at temperatures perhaps as low as 1290 F were used to develop a very fine grain size in the bainite.
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Militzer, M., R. Pandi, and E. B. Hawbolt. Austenite to ferrite transformation kinetics during continuous cooling. Office of Scientific and Technical Information (OSTI), December 1994. http://dx.doi.org/10.2172/34419.

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Focht, E. M. Static Recrystallization Behavior of Austenite in HSLA 100 During Thermomechanical Controlled Processing (TMCP). Fort Belvoir, VA: Defense Technical Information Center, November 1994. http://dx.doi.org/10.21236/ada288737.

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Vitek, J. M., S. A. Vitek, and S. A. David. Modeling the ferrite-to-austenite transformation in the heat-affected zone of stainless steel multi-pass welds. Office of Scientific and Technical Information (OSTI), December 1995. http://dx.doi.org/10.2172/201775.

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Hicho, G. E., W. J. Boettinger, L. Swartzendruber, and T. R. Shives. Examination of the excessive retained austenite on the surface of a section of 17-7 precipitation hardening stainless steel. Gaithersburg, MD: National Institute of Standards and Technology, 1991. http://dx.doi.org/10.6028/nist.ir.4502.

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Beavers and Jaske. L51498 Girth Welding Linepipe made from Stainless Steel Either Solid or Internally Clad Phase I. Chantilly, Virginia: Pipeline Research Council International, Inc. (PRCI), February 1986. http://dx.doi.org/10.55274/r0010649.

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Anderl, R. A., and P. K. Nagata. Helium permeability through austenitic stainless steel. Office of Scientific and Technical Information (OSTI), September 1989. http://dx.doi.org/10.2172/7171431.

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Laura Carroll, Julian Benz, and Richard Wright. Creep-Fatigue of Advanced Austenitic Alloys. Office of Scientific and Technical Information (OSTI), August 2010. http://dx.doi.org/10.2172/993156.

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Dalder, E. N. C., and M. C. Juhas. Austenitic stainless steels for cryogenic service. Office of Scientific and Technical Information (OSTI), September 1985. http://dx.doi.org/10.2172/5083581.

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McEvily, A. J. Fatigue of ferritic and austenitic steels. Office of Scientific and Technical Information (OSTI), January 1991. http://dx.doi.org/10.2172/5576198.

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