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Relevant bibliographies by topics / Dynamic strain aging

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Academic literature on the topic 'Dynamic strain aging'

Author: Grafiati

Published: 4 June 2021

Last updated: 1 February 2022

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Journal articles on the topic "Dynamic strain aging"

1

Ohmori, Masanobu, Yasunori Harada, Misao Itoh, and Fusahito Yoshida. "Dynamic Strain Aging in Chromium." Journal of the Japan Institute of Metals 54, no. 3 (1990): 270–75. http://dx.doi.org/10.2320/jinstmet1952.54.3_270.

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Mardoukhi, Ahmad, Jari Rämö, Taina Vuoristo, Amandine Roth, Mikko Hokka, and Veli-Tapani Kuokkala. "Effects of microstructure on the dynamic strain aging of ferriticpearlitic steels at high strain rates." EPJ Web of Conferences 183 (2018): 03009. http://dx.doi.org/10.1051/epjconf/201818303009.

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This paper presents an experimental study of the effects of dynamic strain aging on the mechanical behavior of selected high carbon and chromium-manganese steels in dynamic loading condition. In ferritic-pearlitic steels, the dynamic strain aging is typically caused by carbon, nitrogen, and possibly some other small solute atoms. Therefore, the thermomechanical treatments affect strongly how strong the dynamic strain aging effect is and at what temperature and strain rate regions the maximum effect is observed. In this work, we present results of the high temperature dynamic compression tests carried out for two different ferritic-pearlitic steels, 16MnCr5 and C60, that were heat treated to produce different microstructure variants of these standard alloys. The microstructures were analyzed using electron microscopy, and the materials were tested with the Split Hopkinson Pressure Bar device at three different strain rates at temperatures ranging from room temperature up to 680 °C to study the effect of the heat treatments and the resulting microstructures on the dynamic behavior of the steels and the dynamic strain aging effect. The results indicate that for both steels, a coarse grain structure has the strongest dynamic strain aging sensitivity at small plastic strains. However, at higher strains, all microstructures show similar strain aging sensitivities.

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Podrezov, Y. N., and L. G. Shtyka. "Dynamic strain aging of powdered iron." Powder Metallurgy and Metal Ceramics 36, no. 9-10 (September 1997): 491–95. http://dx.doi.org/10.1007/bf02680499.

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4

Mesarovic, Sinisa Dj. "Dynamic strain aging and plastic instabilities." Journal of the Mechanics and Physics of Solids 43, no. 5 (May 1995): 671–700. http://dx.doi.org/10.1016/0022-5096(95)00010-g.

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Wang, Xiaorong, and Christopher G. Robertson. "Memory of Prior Dynamic Strain History in Filled Rubbers." Rubber Chemistry and Technology 83, no. 2 (June 1, 2010): 149–59. http://dx.doi.org/10.5254/1.3548271.

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Abstract We recently discovered that particle-reinforced rubbers after being sheared (or aged) in oscillation at a frequency ƒa at a small strain γa (e.g., ∼1% strain) for time ta can often display a spectrum hole or drop in their dissipation spectra. The location of the hole depends on the aging strain amplitude γa. The depth of this hole is influenced by both the oscillatory aging frequency ƒa and the aging duration ta, and follows a simple power relationship of the product of ƒa and ta. Sequential shear at two strains reveals that when γa1>γa2 the resulting dynamic spectra appear to be a combination of that aged at γa1 and γa2, whereas for γa1>γa2, the resulting dynamic spectra only reflect the characteristic hole burning of the second strain after holding at γa2. This new memory effect occurs at very small strains in filled elastomers and involves material stiffening during the strain aging; both of those features are quite different from the Mullins effect. Also, this new memory is found to last for more than 10 days without any noticeable sign of disappearing.

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Fressengeas, C., A. J. Beaudoin, M. Lebyodkin, L. P. Kubin, and Y. Estrin. "Dynamic strain aging: A coupled dislocation—Solute dynamic model." Materials Science and Engineering: A 400-401 (July 2005): 226–30. http://dx.doi.org/10.1016/j.msea.2005.02.073.

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Zhang, Si Qian, Liang Mao, and Li Jia Chen. "Dynamic Strain Aging during Tensile Deformation of Extruded AZ81 Magnesium Alloy." Advanced Materials Research 652-654 (January 2013): 1937–41. http://dx.doi.org/10.4028/www.scientific.net/amr.652-654.1937.

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Serrated flow has been observed in AZ81 alloy during tensile deformation. The observed static strain ageing effect and negative strain rate sensitivity suggest that the serrated flow is due to interaction between dislocations and solute atoms, know as dynamic strain ageing (DSA). The Portevin-Le Chatelier effect is observed at temperatures between 150oC~200oC and 125oC~200oC. In the microstructure of deformed samples dislocations and twins is observed. It is suggested that the occurrence of the dynamic strain aging is associated with interactions between solute atoms and dislocations.

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Hörnqvist, Magnus, Ceena Joseph, Christer Persson, Jonathan Weidow, and Haiping Lai. "Dynamic strain aging in Haynes 282 superalloy." MATEC Web of Conferences 14 (2014): 16002. http://dx.doi.org/10.1051/matecconf/20141416002.

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Song, Yooseob, Daniel Garcia-Gonzalez, and Alexis Rusinek. "Constitutive Models for Dynamic Strain Aging in Metals: Strain Rate and Temperature Dependences on the Flow Stress." Materials 13, no. 7 (April 10, 2020): 1794. http://dx.doi.org/10.3390/ma13071794.

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A new constitutive model for Q235B structural steel is proposed, incorporating the effect of dynamic strain aging. Dynamic strain aging hugely affects the microstructural behavior of metallic compounds, in turn leading to significant alterations in their macroscopic mechanical response. Therefore, a constitutive model must incorporate the effect of dynamic strain aging to accurately predict thermo-mechanical deformation processes. The proposed model assumes the overall response of the material as a combination of three contributions: athermal, thermally activated, and dynamic strain aging stress components. The dynamic strain aging is approached by two alternative mathematical expressions: (i) model I: rate-independent model; (ii) model II: rate-dependent model. The proposed model is finally used to study the mechanical response of Q235B steel for a wide range of loading conditions, from quasi-static loading ( ε ˙ = 0.001 s − 1 and ε ˙ = 0.02 s − 1 ) to dynamic loading ( ε ˙ = 800 s − 1 and ε ˙ = 7000 s − 1 ), and across a broad range of temperatures ( 93 K − 1173 K ). The results from this work highlight the importance of considering strain-rate dependences (model II) to provide reliable predictions under dynamic loading scenarios. In this regard, rate-independent approaches (model I) are rather limited to quasi-static loading.

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Goretta, K. C., J. L. Routbort, and T. A. Bloom. "Dynamic strain aging and serrated flow in MnO." Journal of Materials Research 1, no. 1 (February 1986): 124–29. http://dx.doi.org/10.1557/jmr.1986.0124.

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The effects of aging on the upper yield stress τup and serrated flow have been studied in MnO single crystals at 900 °C for oxygen partial pressures ρO2 of 10−11 and 10−7 Pa. Aging initially increases τup as a consequence of segregation of aliovalent impurities to dislocations for both ρO2 values. For long aging times and ρO2 = 10-11 Pa, serrated flow accompanied by solute softening is observed. The data fit predictions of a Portevin-Le Chatelier model for serrations, but with impurity atmospheres causing softening instead of hardening. This is believed to result from changes in local defect equilibria caused by segregation of impurities with valences greater than two to dislocations.

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Dissertations / Theses on the topic "Dynamic strain aging"

1

Dehghani, Kamran. "Static and dynamic strain aging in "Interstitial-free" steels." Thesis, National Library of Canada = Bibliothèque nationale du Canada, 1999. http://www.collectionscanada.ca/obj/s4/f2/dsk1/tape8/PQDD_0027/NQ50143.pdf.

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Cunningham, Sandra 1974. "Effect of substitutional elements on dynamic strain aging in steel." Thesis, McGill University, 1999. http://digitool.Library.McGill.CA:80/R/?func=dbin-jump-full&object_id=29855.

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Distinct serrations had been observed on the stress-strain curves of various steels tested previously at high temperatures (950--1100°C) at McGill University. An explanation proposed for this behavior was that dynamic strain aging (DSA), caused by the presence of substitutional elements, was taking place. To investigate the possibility that the jerky flow was caused by an interaction between dislocations and substitutional elements, the conditions of temperature and strain rate under which serrated yielding had previously been observed were explored. In addition, some of the same material was utilized in the testing.
Much of the previous work on DSA in steel has focused on the effect of interstitials, namely, carbon and nitrogen, rather than that of substitutional elements. These studies have been conducted in the blue brittle region (i.e. 100--400°C), where the diffusivity of the interstitial elements is sufficiently rapid for them to keep up with the moving dislocations. However, for substitutional elements to obtain enough mobility to induce DSA, the temperature range must be significantly higher.
The effect of substitutional elements on DSA in steel was examined in torsion and, although numerous tests were formulated and carried out in an attempt to gather evidence for this phenomenon, no firm data for the occurrence of DSA were obtained. Further experiments and analysis will be required to gain a better understanding of the behavior of DSA at elevated temperatures, particularly for the case where dynamic recrystallization is taking place. A testing method might then be devised that could make the effect of DSA more evident.

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Cunningham, Sandra. "Effect of substitutional elements on dynamic strain aging in steel." Thesis, National Library of Canada = Bibliothèque nationale du Canada, 1999. http://www.collectionscanada.ca/obj/s4/f2/dsk1/tape8/PQDD_0017/MQ55019.pdf.

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Lobo, David. "Static and dynamic strain aging of 304 stainless steel at high temperatures." Thesis, McGill University, 2000. http://digitool.Library.McGill.CA:80/R/?func=dbin-jump-full&object_id=31060.

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Distinct yield drops and serrations were observed on the stress-strain curves of a 304 type stainless steel when tested at high temperatures (850--1200ºC). A proposed explanation for the behavior is static strain aging (SSA) and dynamic strain aging (DSA), respectively, caused by the presence of substitutional elements.
Much of the previous work on this topic has been focused on the effects of interstitials, namely carbon and nitrogen, at lower temperatures (100--300ºC, depending on the strain rate). However, for substitutional elements to have the same effect, the temperature range must be significantly higher. To further investigate the likelihood that SSA and DSA are caused by substitutional elements, the domain (i.e. temperature and strain rate range) within which yield drops and serrated yielding are observed was studied.
The results of this investigation showed that the appearance of SSA is dependent upon the pass strain, interpass time and strain rate, whereas the presence of DSA serrations was strongly dependent upon strain rate. The disappearance of yield drops involves interpass times in excess of one second. This is hypothesized to result from the disappearance of the deformation vacancies and of the associated non-equilibrium segregation. The impurity element phosphorus was isolated as the most probable cause of the observed phenomenon. This is a result of its high diffusivity, combined with its high binding energy.

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Meng, Chenlu Verfasser], Günter [Akademischer Betreuer] Gottstein, and Gerhard [Akademischer Betreuer] [Hirt. "Dynamic strain aging of Al-Mg alloys after severe plastic deformation / Chenlu Meng ; Günter Gottstein, Gerhard Kurt Peter Hirt." Aachen : Universitätsbibliothek der RWTH Aachen, 2018. http://d-nb.info/1171905556/34.

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Meng, Chenlu [Verfasser], Günter Akademischer Betreuer] Gottstein, and Gerhard [Akademischer Betreuer] [Hirt. "Dynamic strain aging of Al-Mg alloys after severe plastic deformation / Chenlu Meng ; Günter Gottstein, Gerhard Kurt Peter Hirt." Aachen : Universitätsbibliothek der RWTH Aachen, 2018. http://d-nb.info/1171905556/34.

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7

Hooshmand, Mohammad Shahriar. "Atomic-scale modeling of twinning in titanium and other HCP alloys." The Ohio State University, 2019. http://rave.ohiolink.edu/etdc/view?acc_num=osu1566143337320934.

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8

Calmunger, Mattias. "Effect of temperature on mechanical response of austenitic materials." Thesis, Linköpings universitet, Konstruktionsmaterial, 2011. http://urn.kb.se/resolve?urn=urn:nbn:se:liu:diva-73748.

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Global increase in energy consumption and global warming require more energy production but less CO2emission. Increase in efficiency of energy production is an effective way for this purpose. This can be reached by increasing boiler temperature and pressure in a biomass power plant. By increasing material temperature 50°C, the efficiency in biomass power plants can be increased significantly and the CO2emission can be greatly reduced. However, the materials used for future biomass power plants with higher temperature require improved properties. Austenitic stainless steels are used in most biomass power plants. In austenitic stainless steels a phenomenon called dynamic strain aging (DSA), can occur in the operating temperature range for biomass power plants. DSA is an effect of interaction between moving dislocations and solute atoms and occurs during deformation at certain temperatures. An investigation of DSA influences on ductility in austenitic stainless steels and nickel base alloys have been done. Tensile tests at room temperature up to 700°C and scanning electron microscope investigations have been used. Tensile tests revealed that ductility increases with increased temperature for some materials when for others the ductility decreases. This is, probably due to formation of twins. Increased stacking fault energy (SFE) gives increased amount of twins and high nickel content gives a higher SFE. Deformation mechanisms observed in the microstructure are glide bands (or deformations band), twins, dislocation cells and shear bands. Damage due to DSA can probably be related to intersection between glide bands or twins, see figure 6 a). Broken particles and voids are damage mechanisms observed in the microstructure.

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9

Wang, Huaidong. "Comportement mécanique et rupture des aciers au C-Mn en présence de vieillissement dynamique." Phd thesis, Ecole Centrale Paris, 2011. http://tel.archives-ouvertes.fr/tel-00704515.

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Le vieillissement dynamique se manifeste en particulier par le phénomène de Portevin-Le Chatelier (PLC). Il se produit dans les aciers aux environs de 200°C pour des sollicitations quasi-statiques. Dans les aciers au C-Mn, il conduit à une chute de ductilité et de ténacité qui doit être prise en compte dans le dimensionnement des structures de sûreté. L'objectif de la thèse consiste à modéliser le comportement mécanique des aciers au C-Mn en tenant compte du vieillissement dynamique et à prédire leur rupture ductile en présence de ce phénomène. Le comportement mécanique du matériau étudié, un acier au C-Mn, a été caractérisé par des essais de traction simple. Le modèle KEMC implémenté dans le code de calculs par éléments finis Zébulon, a été identifié sur ces essais : l'effet de Portevin Le-Chatelier (PLC) a été correctement simulé sur les éprouvettes lisses, entaillées et CT. Nous avons montré l'importance des conditions aux limites dans la manifestation du PLC. Pour la rupture ductile, l'application du critère de Rice et Tracey (identifié à 20°C) sur les éprouvettes entaillées AE4 montre que la prise en compte du vieillissement dynamique dans le comportement ne suffit pas pour avoir une bonne prédiction de la rupture. Des études micromécaniques de croissance de cavité indiquent que les localisations de PLC peuvent favoriser la croissance et la coalescence de cavité. L'écrouissage apparent, qui dépend du durcissement par la déformation mais aussi du durcissement provenant du vieillissement dynamique, modifie la vitesse de croissance de cavité, mais pas le taux critique de croissance de cavité. On identifie une loi d'endommagement dont les paramètres dépendent de la température à partir des calculs micromécaniques. Le nouveau modèle donne une meilleure prédiction que le modèle de Rice et Tracey sur les éprouvettes entaillées AE4 et a permis de prédire un creux de ténacité sur les éprouvettes CT. Pour améliorer les prédictions, la loi d'endommagement doit dépendre de la vitesse de déformation.

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Belotteau, Jeanne. "Comportement et rupture d’un acier au C-Mn en présence de vieillissement sous déformation." Thesis, Châtenay-Malabry, Ecole centrale de Paris, 2009. http://www.theses.fr/2009ECAP0002/document.

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Les aciers de construction au carbone manganèse (C-Mn) sont largement utilisés pour diverses applications mécaniques, et en particulier pour les tuyauteries de circuit secondaire des centrales nucléaires de type Réacteurs à Eau sous Pression (REP). La robustesse des composants des circuits sous pression des REP vis-à-vis de la fissuration doit être démontrée, tant au niveau de la conception que de l’exploitation. Les aciers au C-Mn sont sensibles au vieillissement sous déformation qui entraîne une chute importante de ductilité et de ténacité entre 150 et 350°C,températures de service des tuyauteries du circuit secondaire. Ce phénomène est dû à une interaction entre les atomes de solutés et les dislocations, et peut se traduire entre autres par une sensibilité négative de la contrainte à la vitesse de déformation, et des localisations de la déformation plastique (Lüders, Portevin – Le Chatelier). L’origine physique du vieillissement sous déformation a été beaucoup étudiée, surtout dans les métaux purs, en relation avec le phénomène Portevin-Le Chatelier (PLC), mais son influence sur les propriétés mécaniques et notamment la rupture reste très controversée. L’objectif de la thèse est de modéliser le comportement et la rupture d’un acier au C-Mn dans un large domaine de température compris entre 20 et 350°C, en tenant compte des phénomènes de vieillissement sous déformation, et en particulier des localisations de déformation. Le comportement et la rupture de l’acier au C-Mn étudié ont été caractérisés expérimentalement dans le domaine 20-350°C à l’aide d’essais de traction sur éprouvettes lisses, sur éprouvettes axisymétriques entaillées, et d’essais de déchirure sur éprouvettes CT. Le modèle d’Estrin Kubin McCormick, prenant en compte le vieillissement sous déformation, a été identifié dans cette même gamme de température et la plupart des effets du vieillissement sous déformation ont pu être simulés numériquement : sensibilité négative de la contrainte d’écoulement à la vitesse de déformation, bandes de Lüders, effet PLC, modification des propriétés mécaniques de traction… Le modèle ainsi identifié a été appliqué à l’étude de la rupture d’éprouvettes lisses, entaillées et CT. La baisse de l’allongement réparti est bien décrite en traction sur éprouvettes lisses. Pour prévoir la rupture des éprouvettes entaillées, l’approche locale de la rupture a été appliquée (modèle de Rice et Tracey). Cette étude a donc permis de disposer d’un modèle prenant en compte le vieillissement sous déformation de 20°C à 350°C et décrivant les localisations de déformation plastique de type Lüdersou PLC, pour différentes géométries d’éprouvettes. Ce modèle a été utilisé pour simuler la rupture des aciers au C-Mn, suscitant ainsi une vision nouvelle pour comprendre la baisse de ductilité associée au vieillissement dynamique
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Books on the topic "Dynamic strain aging"

1

Castelli, Michael G. Thermomechanical deformation behavior of a dynamic strain aging alloy, Hastelloy X. [Washington, DC]: National Aeronautics and Space Administration, 1992.

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Observations of dynamic strain aging in polycrystalline NiAl. [Washington, D.C: National Aeronautics and Space Administration, 1997.

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D, Noebe R., and Kaufman M. J, eds. Observations of dynamic strain aging in polycrystalline NiAl. [Washington, D.C: National Aeronautics and Space Administration, 1997.

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Manifestations of dynamic strain aging in soft-oriented NiAl single crystals. [Washington, D.C: National Aeronautics and Space Administration, 1997.

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J, Kaufman M., and Noebe R. D, eds. Manifestations of dynamic strain aging in soft-oriented NiAl single crystals. [Washington, D.C: National Aeronautics and Space Administration, 1997.

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6

C, Marschall, U.S. Nuclear Regulatory Commission. Office of Nuclear Regulatory Research. Division of Engineering., and Battelle Memorial Institute, eds. Effect of dynamic strain aging on the strength and toughness of nuclear ferritic piping at LWR temperatures. Washington, DC: Division of Engineering, Office of Nuclear Regulatory Research, U.S. Nuclear Regulatory Commission, 1994.

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Book chapters on the topic "Dynamic strain aging"

1

Guo, Wei Guo. "Dynamic Strain Aging during the Plastic Flow of Metals." In Engineering Plasticity and Its Applications, 823–28. Stafa: Trans Tech Publications Ltd., 2007. http://dx.doi.org/10.4028/0-87849-433-2.823.

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Antoun, Bonnie R., Coleman Alleman, and Kelsey De La Trinidad. "Experimental Investigation of Dynamic Strain Aging in 304L Stainless Steel." In Challenges in Mechanics of Time-Dependent Materials, Volume 2, 65–72. Cham: Springer International Publishing, 2018. http://dx.doi.org/10.1007/978-3-319-95053-2_10.

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Antoun, Bonnie R., Coleman Alleman, and Joshua Sugar. "Dynamic Strain Aging in Additively Manufactured Steel at Elevated Temperatures." In Thermomechanics & Infrared Imaging, Inverse Problem Methodologies and Mechanics of Additive & Advanced Manufactured Materials, Volume 7, 27–32. Cham: Springer International Publishing, 2021. http://dx.doi.org/10.1007/978-3-030-59864-8_5.

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Wang, Tong, Stephen Yue, and John J. Jonas. "Effect of Dynamic Strain Aging on the Strain Rate Sensitivity of a Mg-2Zn-2Nd Alloy." In Magnesium Technology 2015, 115–19. Hoboken, NJ, USA: John Wiley & Sons, Inc., 2015. http://dx.doi.org/10.1002/9781119093428.ch23.

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Wang, Tong, Stephen Yue, and John J. Jonas. "Effect of Dynamic Strain Aging on the Strain Rate Sensitivity of a Mg-2Zn-2Nd Alloy." In Magnesium Technology 2015, 115–19. Cham: Springer International Publishing, 2015. http://dx.doi.org/10.1007/978-3-319-48185-2_23.

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Cui, C. Y., C. G. Tian, Y. Z. Zhou, T. Jin, and X. F. Sun. "Dynamic Strain Aging in Ni Base Alloys with Different Stacking Fault Energy." In Superalloys 2012, 715–22. Hoboken, NJ, USA: John Wiley & Sons, Inc., 2012. http://dx.doi.org/10.1002/9781118516430.ch79.

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Peng, Kai Ping, Wen Zhe Chen, and Kuang Wu Qian. "Effect of Dynamic Strain Aging on Fatigue Softening Process of H68 Brass." In Key Engineering Materials, 2508–12. Stafa: Trans Tech Publications Ltd., 2005. http://dx.doi.org/10.4028/0-87849-978-4.2508.

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Hongwei, Zhou, He Yizhu, Lv Jizu, and Rao Sixian. "Study on Dynamic Strain Aging and Low-Cycle Fatigue of Stainless Steel in Ultra-Supercritical Unit." In Energy Materials 2014, 299–306. Cham: Springer International Publishing, 2014. http://dx.doi.org/10.1007/978-3-319-48765-6_33.

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Hongwei, Zhou, He Yizhu, Lv Jizu, and Rao Sixian. "Study on Dynamic Strain Aging and Low-Cycle Fatigue of Stainless Steel in Ultra-Supercritical Unit." In Energy Materials 2014, 299–306. Hoboken, NJ, USA: John Wiley & Sons, Inc., 2015. http://dx.doi.org/10.1002/9781119027973.ch33.

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Hörnqvist, Magnus, and Birger Karlsson. "Temperature and Strain Rate Effects on the Dynamic Strain Ageing of Aluminium Alloy AA7030." In Materials Science Forum, 883–88. Stafa: Trans Tech Publications Ltd., 2006. http://dx.doi.org/10.4028/0-87849-408-1.883.

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Conference papers on the topic "Dynamic strain aging"

1

Hong, S. H., H. Y. Kim, J. S. Jang, and I. H. Kuk. "Dynamic Strain Aging Behavior of Inconel 600 Alloy." In Superalloys. TMS, 1996. http://dx.doi.org/10.7449/1996/superalloys_1996_401_407.

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Mahajanam, S., and M. Joosten. "Dynamic Strain Aging in Oil and Gas Production." In MS&T17. MS&T17, 2017. http://dx.doi.org/10.7449/2017/mst_2017_1086_1102.

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Mahajanam, S., and M. Joosten. "Dynamic Strain Aging in Oil and Gas Production." In MS&T17. MS&T17, 2017. http://dx.doi.org/10.7449/2017mst/2017/mst_2017_1086_1102.

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Kojima, N., K. Mimura, and T. Umeda. "Dynamic tensile properties of mild steel sheets after strain aging." In DYMAT 2009 - 9th International Conferences on the Mechanical and Physical Behaviour of Materials under Dynamic Loading. Les Ulis, France: EDP Sciences, 2009. http://dx.doi.org/10.1051/dymat/2009103.

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Kobayashi, Hiroe, Yoshio Urabe, and Yasuhide Asada. "Strain Rate of Pipe Elbow at Seismic Event and Its Effect on Dynamic Strain Aging." In ASME 2005 Pressure Vessels and Piping Conference. ASMEDC, 2005. http://dx.doi.org/10.1115/pvp2005-71443.

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NRC expressed their refusal of revised seismic stress criteria for piping systems of the ASME Section III, 2001 Edition at their proposed rule making by 10CFR50.55a. One of technical bases of their refusal is “Dynamic strain aging of carbon steel at high strain rate caused by earthquake and at high temperature condition of nuclear power operation”. This paper presents that the effect of dynamic strain aging at the allowable stress limit is practically negligible small even if the seismic allowable stress for nuclear piping increases up to 150% at ASME Section III 2001 and 2003 Edition from 3.0Sm (ASME Section III 1995 Edition). This seismic stress limit revision was achieved by using the B′2 that is equal to 2/3 B2 instead of B2 stress index in Equation of ASME Section III NB-3656 at seismic stress evaluation. At first, maximum elastic-plastic strain of pipe elbow was calculated at various stress level up to revised allowable stress limits by using the elastic-plastic FEM which was verified by the comparison with experimental results. Obtained strain was converted to strain rate by introducing the dominant frequency of piping system at seismic events. Secondary, data of relationship of strain rate and yield to tensile stress ratio for various type of carbon steel was collected. The yield to tensile stress ratio at very low strain rate was compared with that at strain rate of seismic event. The value of yield to tensile stress ratio at strain rate of seismic event was also evaluated. Finally, effect of maximum strain rate at seismic event under revised stress limit condition was discussed by evaluating the change of the yield to tensile stress ratio at low and seismic event condition and the value of the yield to tensile stress ratio at seismic event. From this discussion, dynamic strain aging would not occur in carbon steel piping at seismic event and high temperature condition under revised stress limit condition.

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6

Bartels, R., D. Löhe, and E. Macherauch. "Interaction of Dynamic Strain Aging and Tranformation 0f Retained Austenite to Martensite." In ESOMAT 1989 - Ist European Symposium on Martensitic Transformations in Science and Technology. Les Ulis, France: EDP Sciences, 1989. http://dx.doi.org/10.1051/esomat/198908005.

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7

Cui, C., C. Tian, Y. Zhou, T. Jin, and X. Sun. "Dynamic Strain Aging in Ni Base Alloys with Different Stacking Fault Energy." In Superalloys. John Wiley & Sons, Inc., 2012. http://dx.doi.org/10.7449/2012/superalloys_2012_715_722.

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8

Manuel, Michele, and Wesley Cuadrado - Castillo. "Connecting Dynamic Strain Aging to Deformation Processing in Magnesium-Calcium-Based Alloys." In The Minerals, Metals, and Materials Society, San Diego, California, February 25, 2020. US DOE, 2020. http://dx.doi.org/10.2172/1767117.

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9

Kobayashi, Hiro, and Yoshio Urabe. "Study on Strain Rate Effect on Dynamic Strain Aging and Safety Margin of Pipe Elbow at Seismic Event." In ASME 2009 Pressure Vessels and Piping Conference. ASMEDC, 2009. http://dx.doi.org/10.1115/pvp2009-78134.

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This paper presents the technical reasoning and justification for using the B2′ = (2/3)*B2 in Paragraphs NB-3656(b) and NC/ND-3655(b) of Section III. ASME revised the rules for piping subjected to seismic and other building filtered loads in the 1994 addenda to the 1992 Code to provide an alternative to the existing rules. The purpose of the revision was to recognize the results of significant testing and experience that supported a decrease in the multiplier (B index) of the moment term, among other changes. The use of a B2′ index set equal to 2/3 of the current B2 index effectively raised the Level D allowable 50%. As part of its review in 10CFR50.55a, the NRC noted that use of the new rules was not permitted, due to disagreements in the approach. Since the 1994 addenda were published, the NRC and ASME have worked together to revise the changes. At this time, it is ASME’s understanding that the rules proposed for inclusion in the 2007 Code will be accepted by the NRC, with the exception of the use of a B2′ index equal to 2/3 of B2 for bends and tees. For those items, the NRC believes a multiplier of 3/4 is more appropriate for ferritic steels at temperatures above 300°F, due to dynamic strain aging. Concern has been expressed that since the tests that form part of the basis for setting B2′ = (2/3)*B2 were conducted at ambient temperature, the effect of dynamic strain aging of carbon steels could reduce the seismic margins at temperatures in excess of 300°F (150°C). In response to this concern, the authors prepared this paper as a team working under the Piping Seismic Task Group, ASME Code Committee. This paper demonstrates that: 1) In order to investigate this possibility, authors collected test data at room temperature, and then benchmarked its analytical work against both its tests and data from the EPRI test program since dynamic testing of components at elevated temperature and high stress levels can be quite difficult. From its analytical and test work on components, plus elevated temperature and strain rate work on small specimens, it was concluded that strain rate effects at typical seismic strain rates and amplitudes are not a concern. 2) For typical carbon steel under seismic strain rate loading, at elevated temperature [(above 300°F (150°C)] and at stress levels permitted by the alternative Code equation [NB-3556(b)(2) and NB-3556(b)(3)], the margin to failure is at least 1.5, as recommended by Dr. R.P. Kennedy(1). Thus, the use of B2′ = (2/3)*B2 results in a component with acceptable margin. This is a part of the paper prepared as a team working under the Piping Seismic Task Group under ASME Sec. III, Subgroup Design.

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10

Murty, K. Linga, and Chang-Sung Seok. "Effects of Dynamic Strain-Aging and Cyclic Loading on Fracture Behavior of Ferritic Steels." In 10th International Conference on Nuclear Engineering. ASMEDC, 2002. http://dx.doi.org/10.1115/icone10-22151.

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Ferritic steels commonly used for pressure vessels and reactor supports in light water reactors (LWRs) exhibit dynamic strain aging (DSA) resulting in decreased ductility and toughness. In addition, recent work indicated decreased toughness during reverse-cyclic loading that has implications on reliability of these structures under seismic loading conditions. We summarize some of our recent work on these aspects along with synergistic effects, of interstitial impurity atoms (IIAs) and radiation induced point defects, that result in interesting beneficial effects of radiation exposure at appropriate temperature and strain-rate conditions. Radiation-defect interactions were investigated on pure iron, Si-killed mild steel, A533B, A516, A588 and other reactor support and vessel steels. In all cases, DSA is seen to result in decreased ductility accompanied by increased work-hardening parameter. In addition to mechanical property tests, fracture toughness is investigated on both A533B and A516 steels. While dips in fracture toughness are observed in A533B steel in the DSA region, A516 steel exhibited at best a plateau. The reasons could lie in the applied strain-rates; while J1c tests were performed on A533B steel using 3-point bend tests on Charpy type specimens, CT specimens were used for A516 steel. However, tensile and 3-point bend tests on similar grade A516 steel of different vintage did exhibit distinct drop in the energy to fracture. Load-displacement curves during J1c tests on CT specimens did show load drops in the DSA regime. The effect of load ratio (R) on J versus load-line displacement curves for A516 steel is investigated from +1 to −1 at a fixed normalized incremental plastic displacement of 0.1 (R = 1 corresponds to monotonic loading). We note that J-values are significantly reduced with decreasing load ratio. The work-hardening characteristics on the fracture surfaces were studied following monotonic and cyclic loading fracture tests along with the stress-field analyses. From the hardness and the ball-indentation tests, it was shown that decreased load ratio (R) leads to more strain hardening at the crack tip resulting in decreased fracture toughness. From the stress field analysis near the crack tip of a compact tension fracture toughness test specimen, a cycle of tensile and compressive loads is seen to result in tensile residual stresses (which did not exist at the crack tip before). These results are important to evaluations of flawed-structures under seismic loading conditions, i.e. Leak-Before-Break (LBB) and in-service flaw evaluation criteria where seismic loading is addressed. In addition, studies on fast vs total (thermal+fast) neutron spectra revealed unexpected results due to the influence of radiation exposure on source hardening component of the yield stress; grain-size of pure iron plays a significant role in these effects.

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Reports on the topic "Dynamic strain aging"

1

Marschall, C. W., R. Mohan, P. Krishnaswamy, and G. M. Wilkowski. Effect of dynamic strain aging on the strength and toughness of nuclear ferritic piping at LWR temperatures. Office of Scientific and Technical Information (OSTI), October 1994. http://dx.doi.org/10.2172/10193189.

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2

Subramanian, K. H. Test Plan to Update SRS High Level Waste Tank Material Properties Database by Determining Synergistic Effects of Dynamic Strain Aging and Stress Corrosion Cracking. Office of Scientific and Technical Information (OSTI), March 2002. http://dx.doi.org/10.2172/799694.

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