Relevant bibliographies by topics / AUSTENITIC STEELS

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  1. Journal articles
  2. Dissertations / Theses
  3. Books
  4. Book chapters
  5. Conference papers
  6. Reports

Academic literature on the topic 'AUSTENITIC STEELS'

Author: Grafiati
Published: 4 June 2021
Last updated: 1 February 2022

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Journal articles on the topic "AUSTENITIC STEELS"

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Antoine, P., B. Soenen, and Nuri Akdut. "Static Strain Aging in Cold Rolled Metastable Austenitic Stainless Steels." Materials Science Forum 539-543 (March 2007): 4891–96. http://dx.doi.org/10.4028/www.scientific.net/msf.539-543.4891.

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Transformation of austenite to martensite during cold rolling operations is widely used to strengthen metastable austenitic stainless steel grades. Static strain aging (SSA) phenomena at low temperature, typically between 200°C and 400°C, can be used for additional increase in yield strength due to the presence of α’-martensite in the cold rolled metastable austenitic stainless steels. Indeed, SSA in austenitic stainless steel affects mainly in α’-martensite. The SSA response of three industrial stainless steel grades was investigated in order to understand the aspects of the aging phenomena at low temperature in metastable austenitic stainless steels. In this study, the optimization of, both, deformation and time-temperature parameters of the static aging treatment permitted an increase in yield strength up to 300 MPa while maintaining an acceptable total elongation in a commercial 301LN steel grade. Deformed metastable austenitic steels containing the “body-centered” α’-martensite are strengthened by the diffusion of interstitial solute atoms during aging at low temperature. Therefore, the carbon redistribution during aging at low temperature is explained in terms of the microstructural changes in austenite and martensite.
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Itman Filho, André, Wandercleiton da Silva Cardoso, Leonardo Cabral Gontijo, Rosana Vilarim da Silva, and Luiz Carlos Casteletti. "Austenitic-ferritic stainless steel containing niobium." Rem: Revista Escola de Minas 66, no. 4 (December 2013): 467–71. http://dx.doi.org/10.1590/s0370-44672013000400010.

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The austenitic-ferritic stainless steels present a better combination of mechanical properties and stress corrosion resistance than the ferritic or austenitic ones. The microstructures of these steels depend on the chemical compositions and heat treatments. In these steels, solidification starts at about 1450ºC with the formation of ferrite, austenite at about 1300ºC and sigma phase in the range of 600 to 950ºC.The latter undertakes the corrosion resistance and the toughness of these steels. According to literature, niobium has a great influence in the transformation phase of austenitic-ferritic stainless steels. This study evaluated the effect of niobium in the microstructure, microhardness and charge transfer resistance of one austenitic-ferritic stainless steel. The samples were annealed at 1050ºC and aged at 850ºC to promote formation of the sigma phase. The corrosion testes were carried out in artificial saliva solution. The addition of 0.5% Nb in the steel led to the formation of the Laves phase.This phase, associated with the sigma phase, increases the hardness of the steel, although with a reduction in the values of the charge transfer resistance.
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Gołębiowski, Bartosz, and Wiesław Świątnicki. "Microstructural Changes Induced during Hydrogen Charging Process in Stainless Steels with and without Nitrided Layers." Solid State Phenomena 186 (March 2012): 305–10. http://dx.doi.org/10.4028/www.scientific.net/ssp.186.305.

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The purpose of this study is to analyze the effect of glow discharge nitriding on hydrogen degradation of two types of steels: two-phase austenitic-ferritic and single-phase austenitic. The nitriding process resulted in formation of surface layers composed of expanded austenite (S phase), and in the case of two-phase steel of expanded austenite and expanded ferrite. Microstructural changes occurring under the influence of hydrogen on steels without and with nitrided layers were investigated with the use of scanning (SEM) and transmission (TEM) electron microscopy techniques. It was shown that the density of cracks formed during cathodic hydrogen charging is higher on the surface of the non-nitrided steels compared to the nitrided steels after identical hydrogen charging process. Moreover in non nitrided steel hydrogenation leads to considerable increase of dislocation density, which results from the high concentration of hydrogen absorbed to the steel during its cathodic charging. This leads in turn to high stress concentration and local embrittlement giving rise to cracks formation. Conversely nitriding reduces the absorption of hydrogen and prevents structural changes resulting in hydrogen embrittlement. The conducted studies show that glow discharge nitriding can be used to increase resistance to hydrogen embrittlement of austenitic and austenitic ferritic stainless steels.
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Maznichevsky, Alexander N., Radii V. Sprikut, and Yuri N. Goikhenberg. "Investigation of Nitrogen Containing Austenitic Stainless Steel." Materials Science Forum 989 (May 2020): 152–59. http://dx.doi.org/10.4028/www.scientific.net/msf.989.152.

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An important factor in solving the problem of stainless steel corrosion resistance is carbon concentration reduction. However, a decrease in carbon content of austenitic steels leads to a drop in level of their strength properties. Theoretically, nitrogen alloying can lead to a strength increase in all types of austenitic corrosion-resistant steels. Practically, nitrogen alloying is effectively only with low-carbon compositions. This work shows the effect of nitrogen on the mechanical properties of middle-alloying nitrogen, containing stainless steel, and a study of AISI 304L and pilot steel with different nitrogen content (from 0.16 to 0.30 wt. %). Nitrogen increases strength of steel, which is approximately 30-60% higher than for steel without nitrogen, but reduces technological plasticity. Pilot steels show high corrosion resistance and fine austenite grains.
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Ryś, J., and A. Zielińska-Lipiec. "Deformation of Ferrite-Austenite Banded Structure in Cold-Rolled Duplex Steel / Odkształcenie Pasmowej Struktury Ferrytu I Austenitu W Walcowanej Na Zimno Stali Duplex." Archives of Metallurgy and Materials 57, no. 4 (December 1, 2012): 1041–53. http://dx.doi.org/10.2478/v10172-012-0116-2.

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Duplex type ferritic-austenitic stainless steels develop a specific two-phase banded structure upon thermo-mechanical pre-treatment and subsequent cold-rolling. The band-like morphology of ferrite and austenite imposes different conditions on plastic deformation of both constituent phases in comparison to one-phase ferritic and austenitic steels. In the present research the ingot of a model ferritic-austenitic steel of duplex type, produced by laboratory melt, was subjected to preliminary thermo-mechanical treatment including forging and solution annealing. Afterwards cold-rolling was conducted over a wide deformation range. The investigations comprised examination of ferrite and austenite microstructures by means of optical and transmission electron microscopy and texture measurements after selected rolling reductions. The presented results indicate that deformation mechanisms operating within the bands of both constituent phases are essentially the same as compared to one-phase steels, however their appearance and contribution are changed upon deformation of two-phase banded structure. Different deformation behavior within ferrite-austenite bands in duplex steels, visible especially at higher strains, considerably affects microstructure evolution and in consequence texture formation in both phases.
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Adachi, Shinichiro, Motoo Egawa, Takuto Yamaguchi, and Nobuhiro Ueda. "Low-Temperature Plasma Nitriding for Austenitic Stainless Steel Layers with Various Nickel Contents Fabricated via Direct Laser Metal Deposition." Coatings 10, no. 4 (April 7, 2020): 365. http://dx.doi.org/10.3390/coatings10040365.

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In this study, low-temperature plasma nitriding is applied to austenitic stainless steels at temperatures below 450 °C. This enhances the wear resistance of the steels with maintaining corrosion resistance, by producing expanded austenite (known as the S-phase), which dissolves excessive nitrogen. Austenitic stainless steels contain nickel, which has the potential to play an important role in the formation and properties of the S-phase. In this experiment, austenitic stainless steel layers with different nickel contents were processed using direct laser metal deposition, and subsequently treated using low-temperature plasma nitriding. As a result, the stainless steel layers with high nickel contents formed the S-phase, similar to the AISI 316L stainless steel. The thickness and Vickers hardness of the S-phase layers varied with respect to the nickel contents. Due to lesser chromium atoms binding to nitrogen, the chromium content relatively decreased. Moreover, there was no evident change in the wear and corrosion resistances due to the nickel contents.
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Li, Zhuang, Di Wu, Wei Lv, Zhen Zheng, and Shao Pu Kang. "Investigations on Low Environmental Impact Machining Processes of Free Cutting Austenitic Stainless Steels." Applied Mechanics and Materials 377 (August 2013): 112–16. http://dx.doi.org/10.4028/www.scientific.net/amm.377.112.

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In the present paper, sulfur, RE (rare earth) and bismuth were added to an austenite stainless steel. Low environmental impact machining processes of free cutting austenitic stainless steels was investigated by machinability testing. The results show that a significant amount of grey and dispersed inclusions were found in steel B. The inclusions are typical sulfide inclusions, and bismuth element is attached to double end of manganese sulfide inclusions. Some inclusions exhibit globular shape due to the presence of rare earths elements in steel B. Chip morphology was improved in steel B under the same turning conditions. The machinability of steel B is much better than that of steel A. This is attributed to the presence of free-cutting additives of sulfur, RE and bismuth in the austenitic stainless steels. Satisfactory mechanical properties were also obtained under the conditions of our experiments. The reasons why satisfactory mechanical properties were obtained may lie in that the sulfides and bismuth are soft phase, and the presence of rare earths elements contributes to the improvement of the toughness of the austenitic stainless steels.
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Ravi Kumar, B., J. K. Sahu, and S. K. Das. "Influence of Annealing Process on Recrystallisation Behaviour of a Heavily Cold Rolled AISI 304L Stainless Steel on Ultrafine Grain Formation." Materials Science Forum 715-716 (April 2012): 334–39. http://dx.doi.org/10.4028/www.scientific.net/msf.715-716.334.

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AISI 304L austenitic stainless steel was cold rolled to 90% with and no inter-pass cooling to produced 89% and 43% of deformation induced martensite respectively. The cold rolled specimens were annealed by isothermal and cyclic thermal process. The microstructures of the cold rolled and annealed specimens were studied by the electron microscope. The observed microstructural changes were correlated with the reversion mechanism of martensite to austenite and strain heterogeneity of the microstructure. The results indicated possibility of ultrafine austenite grain formation by cyclic thermal process for austenitic stainless steels those do not readily undergo deformation induced martensite. Keywords: Austenitic stainless steel, Grain refinement, Cyclic thermal process, Ultrafine grain
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Gontijo, L. C., R. Machado, L. C. Casteletti, S. E. Kuri, and Pedro A. P. Nascente. "Study of the S Phases Formed on Plasma-Nitrided Austenitic and Ferritic Stainless Steels." Materials Science Forum 638-642 (January 2010): 775–80. http://dx.doi.org/10.4028/www.scientific.net/msf.638-642.775.

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An expanded austenite layer is formed on the surfaces of austenitic stainless steels that are nitrided under low-temperature plasma. This S phase is an iron alloy metastable phase supersaturated with nitrogen. We have identified a similar expanded ferrite or ferritic S phase for nitrided ferritic (BCC) stainless steels. Samples of austenitic AISI 304L and AISI 316L and ferritic AISI 409L stainless steels were plasma-nitrided at 350, 400, 450 and 500°C, and the structural and corrosion characteristics of the modified layers were analyzed by X-ray diffraction (XRD) and electrochemical tests. For the austenitic AISI 304L stainless steel, the results showed that a hard S phase layer was formed on the surface, without corrosion resistance degradation, by using low plasma temperatures (350 and 400°C). A similar behavior was observed for the austenitic AISI 316L stainless steel: the modified layers formed at 350 and 400°C were constituted mainly by the S phase. Plasma-nitriding treatment of the ferritic AISI 409L stainless steel caused the formation of a layer having high amount of nitrogen. XRD measurements indicated high strain states for the modified layers formed on the three stainless steels, being more pronounced for the ferritic S phase.
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Berezovskaya, Vera V., Eugeny A. Merkushkin, and Ksenia A. Mamchits. "Structure and Phase Transformations in High Nitrogen and High Interstitial Steels of Different Alloying Systems - Short Review." Defect and Diffusion Forum 410 (August 17, 2021): 167–72. http://dx.doi.org/10.4028/www.scientific.net/ddf.410.167.

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The features of the structure evolution under thermal effect of Cr, Cr-Ni, Cr-Ni-Mn, and Cr-Mn-austenitic stainless steels with high nitrogen content and a total high content of carbon and nitrogen are analyzed. When studying the structure, we used light and electron microscopy, X-ray diffraction, dilatometry analysis and electrical resistance measurements. Fine structure and aging processes of austenite, nature and morphology of excess phases, as well as character of phase transformations and their relationship with the properties of steels have been studied. It is shown that Cr-Mn-steels with a high content of (C + N), having a homogeneous structure of austenite without excess phases, surpass Cr-Ni austenitic steels in mechanical and corrosion properties, have higher process ability than Cr-Mn-N-steel and are comparable with them in mechanical properties.
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Dissertations / Theses on the topic "AUSTENITIC STEELS"

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Tsakiris, V. "Deformation twinning in austenitic steels." Thesis, University of Oxford, 1986. http://ethos.bl.uk/OrderDetails.do?uin=uk.bl.ethos.371586.

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Naraghi, Reza. "Martensitic Transformation in Austenitic Stainless Steels." Thesis, KTH, Metallografi, 2009. http://urn.kb.se/resolve?urn=urn:nbn:se:kth:diva-37214.

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Martensitic transformation is very important in austenitic stainless steels where the transformation induced plasticity phenomenon provides a combination of good mechanical properties, such as formability and strength. However, the difficulty of predicting the material behaviour is one of the major drawbacks of these steels. In order to model this behaviour it is of great importance to be able to characterize the morphology, crystallography and the amount of different types of martensite. The morphology and crystallography of thermal and deformation induced lath martensite in stainless steels were re-examined by means of optical microscopy and electron backscatter diffraction (EBSD) technique. The experiments were performed on AISI301, 304 and 204Cu austenitic stainless steels. Plastic deformation was carried out by means of uniaxial tensile tests at the strain rate of  to produce strain induced α’-martensite at a temperature ranging from 0 to 60ºC. An in-situ measurement of the martensite content was performed during the tensile testing using a Ferritescope to provide the necessary experimental values for modelling. Optical microscopy revealed the morphology of the strain induced α’-martensite as sets of thin parallel needles that go through the parent austenite grain and stop at the grain or annealing twin boundaries. Large amount of α’-martensite could be seen at the intersection of shear bands. However, considerable amount of α’-martensite was also observed when only one set of bands is activated. EBSD was successfully used to analyze the morphology and crystallography of martensite. The α’-martensite maintained the Kurdjumov-Sachs (K-S) orientation relationship with the austenite phase. Although all six possible variants did not appear within a single packet, one or two variants were often favoured out of six related to the specific {111} plane. The misorientations between the neighbouring variants were mainly <111> 60º or <110> 49.5º.
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Stewart, John. "Pit initiation on austenitic stainless steels." Thesis, University of Southampton, 1990. http://ethos.bl.uk/OrderDetails.do?uin=uk.bl.ethos.277798.

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Street, Steven Richard. "Atmospheric corrosion of austenitic stainless steels." Thesis, University of Birmingham, 2017. http://etheses.bham.ac.uk//id/eprint/7390/.

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Atmospheric corrosion was investigated using electrochemical and droplet studies. The effects of changes in bulk solution concentration and local pit chemistry on pit propagation and repassivation of 304L and 316L stainless steels were investigated using \(in\) \(situ\) synchrotron X-radiation and electrochemical techniques. Radiography and zig-zag electrochemical sweeps showed that in dilute chloride solutions, partial passivation was observed to initiate locally and propagate across the corroding surface. This caused repassivation gradually rather than as a uniform event. In concentrated chloride solutions, repassivation did not show a sudden drop in current but rather a gradual decrease as potential swept down. Pitting behaviour was also affected by solution concentration. Dilute solutions showed metastable pitting followed by a sharp breakdown (pitting) potential. Concentrated solutions however showed no metastability and a gradual increase in current when pitting. To determine the cause of current oscillations in 304L artificial pits in NaCl:NaNO\(_3\) solutions near the repassivation potential, the salt layers were scanned \(in\) \(situ\) using XRD. The salt layer was confirmed to be FeCl\(_2\).4H\(_2\)O and no nitrate salt was found. A mechanism was suggested to explain the current oscillations in terms of partial passivation being undercut by the advancing corrosion front.
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Kornegay, Cynthia E. "Impact fracture of austenitic stainless steels." Thesis, Virginia Polytechnic Institute and State University, 1985. http://hdl.handle.net/10919/50038.

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Industry is constantly searching for improved materials for use in highly demanding applications. The materials chosen must withstand a wide range of temperatures and extended exposure in aggressive environments, including hydrogen gas. Because of the risk of catostrophe if brittle failure occurs, careful material selection is imperative. Austenitic stainless steels may be a likely choice for hydrogen service because their behavior in high pressure hydrogen ranges from no apparent damage to relevent, but generally small ductility loss (13). Because of this Variation in behavior, a single category cannot be established to encompass all austenitic steels and studies must be performed on each type of steel to determine its behavior under specific circumstances. Two steels being currently under consideration for use in hydrogen are Armco 21-6-9 and Tenelon, both are fully austenitic stainless steels which may be used over a wide range of temperatures, including service at liquid nitrogen temperature.
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Rao, Ashwin. "Creep and anelastic deformation in austenitic steels." Thesis, Open University, 2010. http://ethos.bl.uk/OrderDetails.do?uin=uk.bl.ethos.524785.

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This study examinest he creepb ehaviour of austenitic steels under service temperatures, to determine the effect of creep on material performance. Nuclear power plant components are in regular use at temperatures greater than 450°C, where creep deformation plays a dominant role in limiting the lifetime of the material. The prime aim of this study was to characterise the effect of load-reductions on the creep behaviour of austenitic steels (AlSI type 316H). In-service materials seldom operate at a constant load and/or temperature. The supply demand, maintenance operations, refuelling, etc. will result in large variation of load and temperature acting on the material. Experiments where load/temperature removals during a creep test were therefore conducted. These unloading procedures result in material recovery of the accumulated creep strain (anelasticity). This phenomenon will influence the material properties such as creep life and ductilities. Creep life was found to increase by 2-3 times whereas creep ductilities decreased by 50% when compared to steady-load creep data under identical conditions. The occurrence of anelasticity suggested the presence of a material backstress. The origin and evolution of this internal stress was investigated using neutron diffraction and TEM microscopy. Lattice strain measurements were conducted in-situ using neutron diffraction during a creep test which consisted of load/unload cycles. Experimental results suggest that creep strain is equivalent to plastic strain at a granular level. The data also shows intergranular micro-stressesa re introduced into the material by primary creep. Anisotropic behaviour of the individual crystal planes results in formation of tensile and compressive intergranular stressesin individual grain families. Residual compressives tressesd rive this anelastic deformation. TEM examinations of samples stopped during the unload show changes in dislocation and precipitate morphologies during the plastic strain recovery phase. Evidence of a changing dislocation substructure during the load-reduction period was found. Examinations have also shown carbide densities change during the unload. Pipe diffusion is a possible mechanism which can be used to explain this occurrence. The changing precipitate and dislocation state will influence the strengthening mechanisms, which in-turn will affect the deformation characteristics. These microstructural observations were introduced into a damage mechanics model. Predictions of material behaviour using this model have shown good agreement with experimental data. Outcomes of this project, have established that changes in creep deformation mechanisms will greatly influence material properties. Deformation history of the material will affect the intergranular stress state which in turn will affect the elastic and plastic response of the material. The effect of plastic strain history must be considered and incorporated accounted in any design and assessment procedure.
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Young, Chune-Ching. "Transformation toughening in phosphocarbide-strengthened austenitic steels." Thesis, Massachusetts Institute of Technology, 1988. http://hdl.handle.net/1721.1/77693.

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Hopkin, Gareth John. "Modelling anisothermal recrystallization in austenitic stainless steels." Thesis, University of Cambridge, 2002. https://www.repository.cam.ac.uk/handle/1810/221867.

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Clausen, Bjoern, and risoe@risoe dk. "Characterisation of polycrystal deformation by numerical modelling and." Thesis, Risoe National Laboratory, 1999. http://www.risoe.dk/rispubl/AFM/ris-r-985.htm.

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Sandström, Rolf, Muhammad Farooq, and Joanna Zurek. "Basic creep models for a 25Cr20NiNbN austenitic stainless steels." KTH, Materialteknologi, 2013. http://urn.kb.se/resolve?urn=urn:nbn:se:kth:diva-122155.

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Basic models for solid solution and precipitation hardening during creep are presented for the austenitic stainless steels 25Cr20NiNbN (TP310HNbN, HR3C, DMV310N). The solid solution hardening is a result of the formation of Cottrell clouds of solutes around the dislocations. In addition to slowing down the creep, the solutes increase the activation energy for creep. The increase in activation energy corresponds to the maximum binding energy between the solutes and the dislocations. The formation of fine niobium nitrides during service enhances the creep strength. It is found that the nitrides have an exponential size distribution. In the modelling the critical event is the time it takes for a dislocation to climb over a particle. The creep models can accurately describe the observed time and temperature of the creep rupture strength.
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Books on the topic "AUSTENITIC STEELS"

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Berns, Hans. High Interstitial Stainless Austenitic Steels. Berlin, Heidelberg: Springer Berlin Heidelberg, 2013.

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Berns, Hans, Valentin Gavriljuk, and Sascha Riedner. High Interstitial Stainless Austenitic Steels. Berlin, Heidelberg: Springer Berlin Heidelberg, 2013. http://dx.doi.org/10.1007/978-3-642-33701-7.

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Biermann, Horst, and Christos G. Aneziris, eds. Austenitic TRIP/TWIP Steels and Steel-Zirconia Composites. Cham: Springer International Publishing, 2020. http://dx.doi.org/10.1007/978-3-030-42603-3.

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Vafaei, Reza. The machinability of austenitic stainless steels. Birmingham: University of Birmingham, 1989.

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Li, Xiaoying. Charcterisation of low temperature plasma nitrided austenitic stainless steels. Birmingham: University of Birmingham, 1999.

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Leinonen, Jouko. Cast-To-Cast Variations In Weld Penetration In Austenitic Stainless Steels. Oulu: University of Oulu, 1987.

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McIntyre, Dale R. Experience survey: Stress corrosion cracking of austenitic stainless steels in water. St.Louis: MTI International, 1987.

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Ver Matrix 4: Resurrecciones | Película Completa [2021] En Español Latino. High manganese austenitic steels: Proceedings of a Conference on Manganese Containing Stainless Steels, held in conjunction with ASM's Materials Week '87, Cincinnati, Ohio, 10-15 October 1987. [Metals Park, Ohio]: ASM International, 1987.

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Engineers, National Association of Corrosion. Protection od austenitic stainless steels and other austenitic alloysfrom polythionic acid stress corosion cracking during shutdown of refinery equipment. Houston: NACE, 1993.

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Vanderborck, Y. Comparison of material property specifications of austenitic steels in fast breeder reactortechnology. Luxembourg: Commission of the European Communities, 1985.

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Book chapters on the topic "AUSTENITIC STEELS"

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Chai, Guocai, Jan-Olof Nilsson, Magnus Boström, Jan Högberg, and Urban Forsberg. "Advanced Heat Resistant Austenitic Stainless Steels." In Advanced Steels, 385–97. Berlin, Heidelberg: Springer Berlin Heidelberg, 2011. http://dx.doi.org/10.1007/978-3-642-17665-4_40.

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Rao, Ashwin, P. John Bouchard, and Michael E. Fitzpatrick. "Anelasticity in Austenitic Steels." In Ceramic Transactions Series, 133–43. Hoboken, NJ, USA: John Wiley & Sons, Inc., 2010. http://dx.doi.org/10.1002/9780470930991.ch13.

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Berns, Hans, Valentin Gavriljuk, and Sascha Riedner. "Introduction." In High Interstitial Stainless Austenitic Steels, 1–5. Berlin, Heidelberg: Springer Berlin Heidelberg, 2012. http://dx.doi.org/10.1007/978-3-642-33701-7_1.

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Berns, Hans, Valentin Gavriljuk, and Sascha Riedner. "Constitution." In High Interstitial Stainless Austenitic Steels, 7–19. Berlin, Heidelberg: Springer Berlin Heidelberg, 2012. http://dx.doi.org/10.1007/978-3-642-33701-7_2.

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Berns, Hans, Valentin Gavriljuk, and Sascha Riedner. "Structure." In High Interstitial Stainless Austenitic Steels, 21–83. Berlin, Heidelberg: Springer Berlin Heidelberg, 2012. http://dx.doi.org/10.1007/978-3-642-33701-7_3.

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Berns, Hans, Valentin Gavriljuk, and Sascha Riedner. "Properties." In High Interstitial Stainless Austenitic Steels, 85–109. Berlin, Heidelberg: Springer Berlin Heidelberg, 2012. http://dx.doi.org/10.1007/978-3-642-33701-7_4.

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Berns, Hans, Valentin Gavriljuk, and Sascha Riedner. "Manufacture." In High Interstitial Stainless Austenitic Steels, 111–26. Berlin, Heidelberg: Springer Berlin Heidelberg, 2012. http://dx.doi.org/10.1007/978-3-642-33701-7_5.

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Berns, Hans, Valentin Gavriljuk, and Sascha Riedner. "Assessment." In High Interstitial Stainless Austenitic Steels, 127–39. Berlin, Heidelberg: Springer Berlin Heidelberg, 2012. http://dx.doi.org/10.1007/978-3-642-33701-7_6.

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Fonstein, Nina. "Austenitic Steels with TWIP Effect." In Advanced High Strength Sheet Steels, 369–92. Cham: Springer International Publishing, 2015. http://dx.doi.org/10.1007/978-3-319-19165-2_11.

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Streicher, M. A., and J. F. Grubb. "Austenitic and Ferritic Stainless Steels." In Uhlig's Corrosion Handbook, 657–93. Hoboken, NJ, USA: John Wiley & Sons, Inc., 2011. http://dx.doi.org/10.1002/9780470872864.ch51.

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Conference papers on the topic "AUSTENITIC STEELS"

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Jayakumar, Tammana, Anish Kumar, Baldev Raj, Donald O. Thompson, and Dale E. Chimenti. "ULTRASONIC CHARACTERIZATION OF AUSTENITIC STAINLESS STEELS." In REVIEW OF PROGRESS IN QUANTITATIVE NONDESTRUCTIVE EVALUATION: 34th Annual Review of Progress in Quantitative Nondestructive Evaluation. AIP, 2008. http://dx.doi.org/10.1063/1.2902564.

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Schlüter, H., A. Zwick, M. Aden, G. Uhlig, K. Wissenbach, and E. Beyer. "Descaling of austenitic steels by laser radiation." In ICALEO® ‘94: Proceedings of the Laser Materials Processing Conference. Laser Institute of America, 1994. http://dx.doi.org/10.2351/1.5058876.

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Santacreu, P. O., J. C. Glez, N. Roulet, T. Fröhlich, and Y. Grosbety. "Austenitic Stainless Steels For Automotive Structural Parts." In SAE 2006 World Congress & Exhibition. 400 Commonwealth Drive, Warrendale, PA, United States: SAE International, 2006. http://dx.doi.org/10.4271/2006-01-1215.

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Chen, Y., W.-Y. Chen, A. S. Rao, Z. Li, Y. Yang, B. Alexandreanu, and K. Natesan. "Fracture Resistance of Cast Austenitic Stainless Steels." In 2016 24th International Conference on Nuclear Engineering. American Society of Mechanical Engineers, 2016. http://dx.doi.org/10.1115/icone24-60736.

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Cast austenitic stainless steels (CASS) possess excellent corrosion resistance and mechanical properties and are used alongside with wrought stainless steels (SS) in light water reactors for primary pressure boundaries and reactor core internal components. In contrast to the fully austenitic microstructure of wrought SS, CASS alloys consist of a dual-phase microstructure of delta ferrite and austenite. The delta ferrite is critical for the service performance since it improves the strength, weldability, corrosion resistance, and soundness of CASS alloys. On the other hand, the delta ferrite is also vulnerable to embrittlement when exposed to reactor service temperatures and fast neutron irradiations. In this study, the combined effect of thermal aging and neutron irradiation on the degradation of CASS alloys was investigated. Neutron-irradiated CASS specimens with and without prior thermal aging were tested in simulated light water reactor environments for crack growth rate and fracture toughness. Miniature compact-tension specimens of CF-3 and CF-8 alloys were tested to evaluate the extent of embrittlement resulting from thermal aging and neutron irradiation. The materials used are static casts containing more than 23% delta ferrite. Some specimens were thermally aged at 400 °C for 10,000 hours prior to the neutron irradiation to simulate thermal aging embrittlement. Both the unaged and aged specimens were irradiated at ∼320°C to a low displacement damage dose of 0.08 dpa. Crack growth rate and fracture toughness J-integral resistance curve tests were carried out on the irradiated and unirradiated control samples in simulated light water reactor environments with low corrosion potentials. While no elevated crack propagation rates were detected in the test environments, significant reductions in fracture toughness were observed after either thermal aging or neutron irradiation. The loss of fracture toughness due to neutron irradiation seemed more evident in the samples without prior thermal aging. Transmission electron microscope (TEM) examination was carried out on the thermally aged and neutron irradiated specimens. The result showed that both neutron irradiation and thermal aging can induce significant changes in the delta ferrite. A high density of G-phase precipitates was observed with TEM in the thermally aged specimens, consistent with previous results. Similar precipitate microstructures were also observed in the neutron-irradiated specimens with or without prior thermal aging. A more extensive precipitate microstructure can be seen in the samples subjected to both thermal aging and neutron irradiation. The similar precipitate microstructures resulting from thermal aging and neutron irradiation are consistent with the fracture toughness results, suggesting a common microstructural origin of the observed embrittlement after thermal aging and neutron irradiation.
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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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Liang, Bin, Jianming Gong, Shantung Tu, and Yong Jiang. "Study on Corrosion Behavior of AISI316L and SAF2205 Stainless Steels in Acetic Acid Solution Containing Br-Ion." In ASME 2006 Pressure Vessels and Piping/ICPVT-11 Conference. ASMEDC, 2006. http://dx.doi.org/10.1115/pvp2006-icpvt-11-94054.

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Petrochemical equipments made of austenitic stainless steel are often used in the environment of acetic acid solution. Premature corrosion failure led by acetic acid solution containing Cl− or Br− occurs in service. In the present paper, corrosion behavior of AISI316L austenitic stainless steel and SAF2205 duplex stainless steel in acetic acid solution containing Br-ion was studied by measuring the corrosion weight loss and Potentiodynamic anodic polarization curve. Effects of temperature and Br− concentration on the corrosion behaviors of AISI316L and SAF2205 material were investigated. The research results show that the corrosion rate markedly increases and pitting potential rapidly decreases with increasing temperature and Br− ion concentration. The pitting resistance of SAF2205 stainless steels is superior to AISI316L. For sensitized AISI316L and SAF2205 stainless steels, the similar rules were founded with increasing Br− concentration; sensitizing treatment will lead to decrease in corrosion resistance. Pitting induced by Br ion preferentially occurred at austenitic boundaries for sensitized AISI316L stainless steels, whereas pitting preferentially occurred at austenitic boundaries, ferrite-austenite boundaries and ferrite boundaries for sensitized SAF2205 duplex stainless steels.
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Wilhelm, Paul, Paul Steinmann, and Jürgen Rudolph. "Discussion of Fatigue Data for Austenitic Stainless Steels." In ASME 2014 Pressure Vessels and Piping Conference. American Society of Mechanical Engineers, 2014. http://dx.doi.org/10.1115/pvp2014-28066.

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The first results of a detailed fatigue model for austenitic stainless steels in general and for the grades 1.4541 and 1.4550 are presented to describe the effect of the light water reactor (LWR) coolant environments on the fatigue life. The statistical evaluations are based on strain (and load) controlled test series from different institutions. The compiled fatigue data include not only results from America (Keller (1971), Conway (1975), Hale (1977), and Argonne National Laboratory (ANL)(1999–2005)), but also from Europe (Solin (2006), Le Duff (2008–2010), De Baglion (2011, 2012), Huin (2013),…) and Japan (Kanasaki (1997)). The fatigue life is defined as the number of cycles necessary for tensile stress to drop 25 percent from its peak value. Fatigue lives defined by other failure criteria are normalized to the load reduction of 25 percent, before the statistical analysis is performed. The fatigue data are expressed in terms of the Langer equation and the parameter “material variability and data scatter” is quantified. Additionally, fatigue data in air of roughened specimens are compiled and discussed. A reduction factor of 2.5 on number of cycles is derived to cover the maximum allowed surface roughness. Based on the derived best-fit curves, design-curves in air and, in a second step, environmentally assisted fatigue (EAF) curves for LWR environments, which consider temperature, strain rate, dissolved oxygen content, and hold-time effects, will be incorporated in the detailed fatigue model in the future.
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Welch, Amberlee. "Gas Nitriding Comparison of Austenitic and Martensitic Stainless Steels." In HT2019. ASM International, 2019. http://dx.doi.org/10.31399/asm.cp.ht2019p0349.

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Abstract The heat treatment method of gas nitriding is proving to be a viable option as a low temperature case hardening process for a variety of stainless steels used in numerous applications. A comparison between an austenitic stainless steel, grade 304, and a martensitic stainless steel, grade 410 in the hardened and non-hardened conditions is used to show the differences in properties obtained as a result of gas nitride process adjustments. The achieved properties, compound layer thickness, hardness, and porosity level along with the measured depth of hardening, can be used to determine which material will be the best option depending on the application.
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Gavriljuk, Valentin, Bela Shanina, Vladyslav Shyvanyuk, and Sergey Teus. "A Concept for Development of Hydrogen-Resistant Austenitic Steels." In ASME 2013 Pressure Vessels and Piping Conference. American Society of Mechanical Engineers, 2013. http://dx.doi.org/10.1115/pvp2013-97011.

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Austenitic steels represent a promising class of engineering materials for hydrogen use in vehicles, e.g. for tanks and pipelines. This topic is analyzed in terms of the effect of alloying elements on the interatomic bonds in the solid solutions and, consequently, on the interaction between hydrogen atoms and dislocations and hydrogen embrittlement, HE. The effect of Cr, Ni, Mn, Mo, Si, Al, Cu, C, N was studied. It is shown that the physical reason for HE amounts to the hydrogen-caused increase in the concentration of free electrons in the austenitic solid solution. For this reason, the alloying with elements decreasing the concentration of free electrons is expected to improve resistance of austenitic steels to HE. Alloying with Cr, Mn, Mo and Si is shown to be useful, whereas Cu, Al, Ni, N assist hydrogen degradation. The role of Ni amounts only to stabilization of the fcc austenitic lattice and its absence or the decrease of its content in steel is desirable. Based on the obtained results, recommendations are made for design of austenitic steels with increased hydrogen resistance.
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Mihalache, Maria, Mihail Mihalache, Iulia Dumitrescu, and Zhangjian Zhou. "Assessment Oxidation Kinetics and Products in SCWR Media of Austenitic ODS Steels With Different Austenite Stabilisers." In 2014 22nd International Conference on Nuclear Engineering. American Society of Mechanical Engineers, 2014. http://dx.doi.org/10.1115/icone22-30665.

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In order to fulfil requirements for corrosion resistance for new reactor GIV, the austenitic 304L stainless steel and 18Cr-20Mn austenitic steel were improved by oxide dispersion strengthening (ODS), using two nano-oxide types: titanium and yttrium oxides. Two new ODS steels and a reference material, A/SA-270 grade 304L SS as plate, were characterised by different techniques and its behaviour in SCWR environment was considered. Coolant compatibility studies have been performed in demineralised water at supercritical conditions: temperature of about 550°C and 25 MPa pressure. The oxide developed on the 304ODS samples is layered, thicker and more uniform than on 304L SS. Some oxides grown on 18Cr-20MnODS steel are un-adherently and they are lost in the simulated water coolant. The weight gains of ODS samples are positive and higher than 304L SS up to approximately 1320 hours while on 18Cr-20MnODS steel is negative. The oxide films were investigated by SEM and EDS techniques.
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Reports on the topic "AUSTENITIC STEELS"

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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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Todd, J. A., and Jyh-Ching Ren. Microstructural studies of advanced austenitic steels. Office of Scientific and Technical Information (OSTI), November 1989. http://dx.doi.org/10.2172/6770532.

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Imrich, K. J., D. R. Leader, N. C. Iyer, and M. R. Jr Louthan. Recycle of radiologically contaminated austenitic stainless steels. Office of Scientific and Technical Information (OSTI), February 1995. http://dx.doi.org/10.2172/10117155.

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Hu, Bin, and Ian Baker. Intermetallic Strengthened Alumina-Forming Austenitic Steels for Energy Applications. Office of Scientific and Technical Information (OSTI), March 2016. http://dx.doi.org/10.2172/1301859.

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Stoller, R. E. Microstructural evolution in fast-neutron-irradiated austenitic stainless steels. Office of Scientific and Technical Information (OSTI), December 1987. http://dx.doi.org/10.2172/5436209.

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Maziasz, P. J., J. P. Shingledecker, N. D. Evans, and M. J. Pollard. Advanced Cast Austenitic Stainless Steels for High Temperature Components. Office of Scientific and Technical Information (OSTI), October 2008. http://dx.doi.org/10.2172/944971.

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Strum, M. J. Control of cryogenic intergranular fracture in high-manganese austenitic steels. Office of Scientific and Technical Information (OSTI), December 1986. http://dx.doi.org/10.2172/6738367.

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Clark, E. A. Materials compatibility of hydride storage materials with austenitic stainless steels. Office of Scientific and Technical Information (OSTI), September 1992. http://dx.doi.org/10.2172/10159240.

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Clark, E. A. Materials compatibility of hydride storage materials with austenitic stainless steels. Office of Scientific and Technical Information (OSTI), September 1992. http://dx.doi.org/10.2172/6485901.

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