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Journal articles on the topic 'Recrystallization kinetics'

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Author: Grafiati

Published: 10 December 2022

Last updated: 28 January 2023

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1

Kaverinsky, V. V., and Z. P. Sukhenko. "Mathematical Modelling of Primary Recrystallization Kinetics and Precipitation of Carbonitride Particles in Steels. II. Recrystallization Kinetics." METALLOFIZIKA I NOVEISHIE TEKHNOLOGII 43, no. 2 (April 23, 2021): 235–44. http://dx.doi.org/10.15407/mfint.43.02.0235.

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2

Erukhimovitch, V., and J. Baram. "Modeling recrystallization kinetics." Materials Science and Engineering: A 214, no. 1-2 (August 1996): 78–83. http://dx.doi.org/10.1016/0921-5093(96)10223-9.

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3

Kraft, F. F., R. N. Wright, and M. K. Jensen. "Kinetics of nonisothermal recrystallization." Journal of Materials Engineering and Performance 5, no. 2 (April 1996): 213–19. http://dx.doi.org/10.1007/bf02650889.

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4

Bracke, Lieven, Kim Verbeken, Leo Kestens, and Jan Penning. "Recrystallization Behaviour of an Austenitic High Mn Steel." Materials Science Forum 558-559 (October 2007): 137–42. http://dx.doi.org/10.4028/www.scientific.net/msf.558-559.137.

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The recrystallization behaviour of a cold rolled austenitic Fe-Mn steel is studied to explain the fine grained final microstructure. Thorough investigation of the kinetics, the microstructure and the texture evolution during recrystallization showed that the fast recrystallization kinetics is responsible for the final microstructure, while an oriented nucleation mechanism determines the texture evolution. The reason for the fast recrystallization kinetics is the low amount of recovery prior to recrystallization, resulting in a high driving force for the latter.

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5

He, T., Y. D. Liu, Yan Wu, Q. W. Jiang, Gang Wang, Yan Dong Wang, and Liang Zuo. "Study on the Micro Mechanism of Recrystallization Texture Formation in Cold-Rolled IF Steel Sheet." Materials Science Forum 495-497 (September 2005): 417–22. http://dx.doi.org/10.4028/www.scientific.net/msf.495-497.417.

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An experimental setup was designed to study the recrystallization kinetics of Interstitial Free (IF) steel in this work. The 80% cold rolled IF steel foils are heated rapidly to 680°C, 730°C and 780°C by a salt bath. The recrystallization kinetic curves were obtained by the quantitative analysis of texture components, microstructures and EBSP (electron back-scattering patterns) measurements. With the help of EBSD, the orientations of the recrystallization nuclei are determined. The growth rule of the recrystallization nuclei was analyzed statistically. The effect of nucleus orientation on the formation of the recrystallization texture was investigated.

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6

Chun, Y. B., S. Lee Semiatin, and Sun Keun Hwang. "Monte-Carlo Modeling of Recrystallization Kinetics of Cold-Rolled Titanium." Materials Science Forum 654-656 (June 2010): 1486–91. http://dx.doi.org/10.4028/www.scientific.net/msf.654-656.1486.

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The recrystallization behavior of cold-rolled, commercial-purity titanium was studied experimentally and with Monte-Carlo (MC) modeling. Utilization of EBSD-OIM as input for MC modeling resulted in realistic predictions of recrystallization kinetics, microstructure and texture, which were in good agreement with experimental results. MC modeling of recrystallization kinetics predicted that the non-uniform stored energy distribution, heterogeneous nucleation of recrystallization and recovery in combination leads to a negative deviation from linear JMAK kinetics. It was found that concurrent recovery that takes place during recrystallization is an important process that controls both the overall recrystallization kinetics and the deviation of linear JMAK kinetics. On the other hand, the non-uniformly distributed stored energy itself has little effect on the negative deviation from JMAK kinetics but intensifies the deviation when heterogeneous nucleation is combined. Modeling results also revealed that heterogeneous nucleation of recrystallized grains and their early impingement in local areas of high deformation are essential for producing a log-normal distribution of grain size and a typical recrystallization texture of rolled titanium.

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7

Xiong, Xue Gang. "Austenite Recrystallization Model of High Ti Microalloyed Steels." Advanced Materials Research 1014 (July 2014): 25–32. http://dx.doi.org/10.4028/www.scientific.net/amr.1014.25.

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Through the thermal simulation test, the curves of austenite recrystallization kinetics is recorded, the influence of the parameters including deformation temperature, strain and strain rate on the austenite recrystallization fraction of Ti microalloyed steels is studied, the recrystallization kinetics equation is calculated, and the austenite recrystallization model of the test steel is obtained. The results improve that Ti inhibits both the dynamic and static austenite recrystallization in high Ti microalloyed steels.

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8

RAOUGUI, Atae, Ion GRECU, Volkan Murat YILMAZ, and Kenan YILDIZ. "SOĞUK HADDELENMİŞ AA3105 VE AA5005 LEVHALARIN DSC ANALİZİ İLE YENİDEN KRİSTALLENME KİNETİĞİ." Euroasia Journal of Mathematics, Engineering, Natural & Medical Sciences 8, no. 17 (September 25, 2021): 80–85. http://dx.doi.org/10.38065/euroasiaorg.621.

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In this study, the non-isothermal recrystallization kinetics of cold rolled AA3105 and AA5005 aluminum alloy sheets obtained from ASAŞ Aluminum located in Akyazı-Sakarya was studied by using differential scanning calorimetry (DSC). The non – isothermal kinetics was performed by using Kissenger, Boswell, Ozawa and Starink methods known as model – free methods. The recrystallization temperatures on DSC graphics at different heating rates (β) were deduced and the activation energies were calculated from the slopes from Y – 1/T diagrams. Y is ln(β/T2) for Kissenger, ln(β/T) for Boswell, ln(β) for Ozawa and ln(β/T1.92) for Starink. The results showed that the activation energies of recrystallization are in the range of 194 – 206 kJ/mol for cold rolled AA5005 sheet and in the range of 235 – 257 kJ/mol for cold rolled AA3105 sheet, according to four non-isothermal kinetics model.

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9

Dutta, S., and M. S. Kaiser. "Recrystallization Kinetics in Aluminum Piston." Procedia Engineering 90 (2014): 188–92. http://dx.doi.org/10.1016/j.proeng.2014.11.835.

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10

Wang, Jian, and Hong Xiao. "Determination of the Kinetics for Dynamic and Static Recrystallization by Using the Flow Curves." Materials Science Forum 575-578 (April 2008): 904–9. http://dx.doi.org/10.4028/www.scientific.net/msf.575-578.904.

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Improved methods to estimate the kinetics of dynamic and static recrystallization are proposed in this paper. The kinetics for dynamic and static recrystallization can be evaluated by inverse analysis of the flow curves obtained using the single-hit and double-hit hot compression tests carried out on Gleeble 3500. The dynamic and static recrystallization volume fractions can be seen as functions of plastic strain and time, respectively. The mathematical formulations between the recrystallization volume fractions and the dislocation density related to the flow stress are used in incremental forms in the study. The methods are applied to the hot compression tests of plain carbon steel and the kinetics of dynamic and static recrystallization are gained successfully for some conditions at elevated temperature. The results are clarified by comparing them with those reported in previous investigations. It is confirmed that the present methods can provide accurate kinetics for dynamic and static recrystallization with shorter time for experiment and computation.

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11

Mungole, M. N., Prakash C. Trivedi, Satyam Sharma, and R. C. Sharma. "Recrystallization Kinetics in 17Cr 1Mo Ferritic Steel." Defect and Diffusion Forum 279 (August 2008): 79–83. http://dx.doi.org/10.4028/www.scientific.net/ddf.279.79.

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The recrystallization kinetic of 17Cr 1Mo ferritic steel was studied using 60% cold rolled samples. The recrystallization was carried out at 750 , 800 and 9000C for 3, 5, 15, 30 and 60 minuets. The volume fraction of the recrystallized grains was used as a kinetic parameter. The magnitude of time exponent “n” was much less than the ideal value because of the heterogeneous recrystallization. The estimated activation energy for recrystallization “Q” was more as compared to those for pure metals.

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12

Serajzadeh, S., A. Karimi Taheri, and S. M. Zebarjad. "The effect of carbon on the restoration phenomena during hot deformation of carbon steels." International Journal of Materials Research 94, no. 8 (August 1, 2003): 916–21. http://dx.doi.org/10.1515/ijmr-2003-0163.

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Abstract A study has been made to determine the influence of the carbon content on the kinetics of dynamic and static recrystallization during and after hot deformation of carbon steels. For this purpose, single- and double-hit hot compression experiments at various strain rates and temperatures together with the Avrami-type kinetics equation and Bergstrom approach have been utilized to investigate recrystallization behavior. The results show that the apparent activation energy of hot deformation decreases with increasing carbon content and this phenomenon results in a faster dynamic recrystallization at high temperatures and/or low strain rates. Also, increasing carbon content leads to a higher rate of static recrystallization at low strain rates while at high strain rates it causes a slower kinetics of static recrystallization.

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13

Qi, Hong Na, Zhi Min Zhang, Jian Min Yu, Xue Yan Yin, and Zhi Yuan Du. "Dynamic Recrystallization of Mg-8Gd-3Y-1Nd-0.5Zr Alloy during Hot Deformation." Materials Science Forum 898 (June 2017): 311–22. http://dx.doi.org/10.4028/www.scientific.net/msf.898.311.

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Uniaxial hot compression was conducted on Gleeble-3500 thermo simulation machine. Based on stress-strain curves, the constitutive relationship and the dynamic recrystallization kinetics model of Mg-8Gd-3Y-1Nd-0.5Zr were established. Simultaneously, dynamic recrystallization mechanism of this alloy under different deformation condition was investigated by SEM, EBSD and OM. The critical strain equation and the dynamic recrystallization kinetics model were obtained. The results showed that the dynamic recrystallization volume fraction increased with the increasing of the strain.The twin dynamic recrystallization (TDRX) was the mainly DRX mechanism at 350°C;the dynamiac recrysallization mechanism was dominated by continuous dynamic recrystallization (CDRX) at 400°C and 450°C. At higher temperature (500°C), the dynamic recrystallization was dominated by discontinuous dynamic recrystallization (DDRX) with a small amount of CDRX.

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14

Tang, Shuai, Xiaofang Li, Jianping Li, Zhenyu Liu, and Guodong Wang. "Role of Microalloying Elements on Recrystallization Kinetics of Cold-Rolled High Strength Low Alloy Steels." Metals 12, no. 10 (October 17, 2022): 1741. http://dx.doi.org/10.3390/met12101741.

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The recrystallization kinetics of two cold-rolled high strength low alloy steels with the addition of Ti and Ti-V, respectively, during annealing were investigated by means of modeling and experimental validation. The recrystallization kinetics of the Ti-V steel were hindered compared to the Ti steel. Based on solid solution theory, mass conservation law and classical nucleation, growth and coarsening theory, the precipitation behavior of Ti and Ti-V steels was predicted. The radius of TiC is larger, and its number density is lower than (Tix, V1−x)C. On this basis, by considering the comprehensive effect of recrystallization on stored energy, the effect of the microalloyed precipitates and microalloying solute on the driving force and grain boundary mobility, the model of the recrystallization kinetics was proposed, which could well reproduce the effect of microalloying elements on recrystallization. Moreover, it was indicated that solute drag is more effective in retarding recrystallization than the pinning effect of precipitates.

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15

Decreus, B., Hatem S. Zurob, John Dunlop, and Yves Bréchet. "Effect of Low-Temperature Recovery Treatments on Subsequent Recrystallization in Al-2.5%Mg." Materials Science Forum 550 (July 2007): 381–86. http://dx.doi.org/10.4028/www.scientific.net/msf.550.381.

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The effect of low temperature recovery treatments on the recrystallization kinetics during subsequent high temperature annealing was investigated in three Al-2.5%Mg alloys with various Fe additions. Recovery treatments were carried out at 190oC for times ranging from 0.25 to 65 hrs. Recrystallization treatments were carried out at 280oC. The kinetics of recrystallization was followed using the techniques of hardness measurement, optical metallography and calorimetry.

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16

Xiong, Ji Chun, Li Jie Hu, and Jia Rrong Li. "Kinetics and Microstructures of Cellular Recrystallization of Single Crystal Superalloy DD6." Materials Science Forum 1072 (October 25, 2022): 155–60. http://dx.doi.org/10.4028/p-15w80y.

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The samples of single crystal superalloy DD6 were grit blasted and heat treated at 1100°C for 0.5h, 1h, 2h, 4h, 8h, 16h at vacuum atmosphere, respectively, then the recrystallization microstructure and kinetics of DD6 alloy was investigated. The results showed that the cellular recrystallization grains nucleated in grit blasted single crystal samples heat treated at 1100°Cfor 0.5h, 1h, 2h, 4h, 8h, 16h. With the increase of the duration of heat heating process, the configuration of cellular recrystallization cleared up, and the depth of cellular recrystallization increased. While the coarse γ phase formed in the cellular recrystallization, and the shape of γ phases in the cellular recrystallization was almost equiaxed near the surface of the grit blasted samples and lamellar at the interface between cellular recrystallization and the original zone, respectively. The lamellar γ phase in the cellular grains was radial, and perpendicular to the cellular grain boundary. The recrystallization kinetics of single crystal superalloy DD6 was disclosed, with the increase of the duration of heat heating process, the depth of cellular recrystallization increase quickly and then almost keeps stable at last. The velocity of growth of cellular recrystallization increase very quickly at first, and then decrease at some stage, at last, the velocity tends to zero.

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17

Shkatov, Valeriy, and Igor Mazur. "Modeling the Dynamic Recrystallization and Flow Curves Using the Kinetics of Static Recrystallization." Materials 12, no. 18 (September 18, 2019): 3024. http://dx.doi.org/10.3390/ma12183024.

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The results of modeling the dynamic recrystallization of steels during hot deformation on the basis of information on their static recrystallization kinetics are presented. The results of predicting the amount of deformation accumulated in the metal under the conditions of dynamic recrystallization development were used for calculating the metal flow curves. The model was validated by comparing the calculated flow curves with the experimental flow curves determined on the 1045 steel by means of hot torsion tests carried out from 1000 °C to 1100 °C and at strain rates from 0.1 to 10 s‒1. The difference between the experimental and predicted flow stress values did not exceed 6%. The influence of the chemical element content in low-alloyed steels on the magnitude of the critical strain for the initiation of dynamic recrystallization is assessed. The method of predicting the kinetics of dynamic recrystallization by recalculating the kinetics of static recrystallization to the conditions of continuous growth of the strain degree during metal deformation implemented in the model can be used in designing and optimizing technologies associated with metal hot forming processes.

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18

Lin, Feng Xiang, Torben Leffers, Wolfgang Pantleon, and Dorte Juul Jensen. "Effects of Widening during Rolling on the Subsequent Recrystallization Kinetics of Copper." Materials Science Forum 753 (March 2013): 285–88. http://dx.doi.org/10.4028/www.scientific.net/msf.753.285.

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Recrystallization kinetics in copper cold-rolled to 90% reduction with and without significant widening was investigated by electron backscatter diffraction. It was found that the recrystallization process was slightly retarded and the development of cube recrystallization texture was largely inhibited in the widening sample. Cube grains were observed to have a growth advantage by a factor of 2 in the non-widening sample, while this growth advantage was not observed in the widening sample. The recrystallization kinetics and the development of cube texture in the two samples are discussed.

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19

Winning, Myrjam, Dierk Raabe, and Abhijit P. Brahme. "A Texture Component Model for Predicting Recrystallization Textures." Materials Science Forum 558-559 (October 2007): 1035–42. http://dx.doi.org/10.4028/www.scientific.net/msf.558-559.1035.

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The study presents an analytical model for predicting crystallographic textures and the final grain size during primary static recrystallization of metals using texture components. The kinetics is formulated as a tensorial variant of the Johnson-Mehl-Avrami-Kolmogorov (JMAK) equation. The tensor form is required since the kinetic and crystallographic evolution of the microstructure is described in terms of a limited set of growing (recrystallizing) and swept (deformed) texture components. The number of components required defines the order of the tensor since the kinetic coupling occurs between all recrystallizing and all deformed components. The new method is particularly developed for the fast and physically-based process simulation of recrystallization textures with respect to processing. The present paper introduces the method and applies it to the primary recrystallization of low carbon steels.

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20

Horník, Jakub, Petr Zuna, Jaroslav Malek, and František Jandoš. "Kinetics of Austenite Recrystallization of Selected Steels Used for Heavy Forgings." Materials Science Forum 782 (April 2014): 93–98. http://dx.doi.org/10.4028/www.scientific.net/msf.782.93.

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The kinetics of austenite recrystallization was evaluated in range of typical forging temperatures (850 - 1250) °C. The steels SA-508 and 3.5Ni-1.5Cr were compared. The laboratory one step deformation was applied. The effect of selected chemical elements in evaluated steels on grain growth and recrystallization kinetics of austenite and precipitation was monitored using metallographic methods. The retarding of static recrystallization was proved and no abnormal grain coarsening at defined condition was observed.

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21

Taylor, Adam S., and Peter D. Hodgson. "Recrystallization of 304SS during and after High Strain Rate Deformation." Materials Science Forum 753 (March 2013): 403–6. http://dx.doi.org/10.4028/www.scientific.net/msf.753.403.

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During the hot working of austenitic stainless steels the shape of the flow curve is strongly influenced by the strain rate. Low strain rate deformation results in flow curves typical of dynamic recrystallization (DRX) but as the strain rate increases the shape changes to a ‘flat-top’ curve. This has traditionally been thought to indicate no DRX is taking place and that dynamic recovery (DRV) is the only operating softening mechanism. Examining the work-hardening behaviour and corresponding deformation microstructures showed this is not the case for austenitic stainless steel, as clear evidence of dynamic recrystallization process can be seen. The post-deformation recrystallization kinetics can be modelled using a standard Avrami equation with an Avrami exponent, n, of 1.15. With an increasing value of the Zener-Hollomon parameter it was found that the kinetics of recrystallization become less strain rate sensitive until at the highest values (highest strain rates/lowest temperatures) the recrystallization kinetics become strain rate insensitive.

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22

Hines, J. A., and K. S. Vecchio. "Recrystallization kinetics within adiabatic shear bands." Acta Materialia 45, no. 2 (February 1997): 635–49. http://dx.doi.org/10.1016/s1359-6454(96)00193-0.

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23

Lauridsen, E. M., D. Juul Jensen, H. F. Poulsen, and U. Lienert. "Kinetics of individual grains during recrystallization." Scripta Materialia 43, no. 6 (August 2000): 561–66. http://dx.doi.org/10.1016/s1359-6462(00)00430-9.

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24

Tajally, M., and Z. Huda. "Recrystallization kinetics for aluminum alloy 7075." Metal Science and Heat Treatment 53, no. 5-6 (September 2011): 213–17. http://dx.doi.org/10.1007/s11041-011-9371-5.

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25

Jonas, John J., Xavier Quelennec, Lan Jiang, and Étienne Martin. "The Avrami kinetics of dynamic recrystallization." Acta Materialia 57, no. 9 (May 2009): 2748–56. http://dx.doi.org/10.1016/j.actamat.2009.02.033.

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26

Barnett, M. R., G. L. Kelly, and P. D. Hodgson. "Inferring dynamic recrystallization in ferrite using the kinetics of static recrystallization." Metallurgical and Materials Transactions A 33, no. 7 (July 2002): 1893–900. http://dx.doi.org/10.1007/s11661-002-0022-8.

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27

Ji, Mo, Martin Strangwood, and Claire Davis. "Effect of Strain-Induced Precipitation on the Recrystallization Kinetics in a Model Alloy." Metallurgical and Materials Transactions A 52, no. 5 (March 19, 2021): 1963–75. http://dx.doi.org/10.1007/s11661-021-06206-8.

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AbstractThe effects of Nb addition on the recrystallization kinetics and the recrystallized grain size distribution after cold deformation were investigated by using Fe-30Ni and Fe-30Ni-0.044 wt pct Nb steel with comparable starting grain size distributions. The samples were deformed to 0.3 strain at room temperature followed by annealing at 950 °C to 850 °C for various times; the microstructural evolution and the grain size distribution of non- and fully recrystallized samples were characterized, along with the strain-induced precipitates (SIPs) and their size and volume fraction evolution. It was found that Nb addition has little effect on recrystallized grain size distribution, whereas Nb precipitation kinetics (SIP size and number density) affects the recrystallization Avrami exponent depending on the annealing temperature. Faster precipitation coarsening rates at high temperature (950 °C to 900 °C) led to slower recrystallization kinetics but no change on Avrami exponent, despite precipitation occurring before recrystallization. Whereas a slower precipitation coarsening rate at 850 °C gave fine-sized strain-induced precipitates that were effective in reducing the recrystallization Avrami exponent after 50 pct of recrystallization. Both solute drag and precipitation pinning effects have been added onto the JMAK model to account the effect of Nb content on recrystallization Avrami exponent for samples with large grain size distributions.

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28

Roumina, R., Chad W. Sinclair, and F. Fazeli. "Precipitation and Recrystallization in an Al-Mg-Sc Alloy." Materials Science Forum 519-521 (July 2006): 1647–52. http://dx.doi.org/10.4028/www.scientific.net/msf.519-521.1647.

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The addition of scandium severely retards the recrystallization of Al-Sc alloys when it is present in the form of fine Al3Sc precipitates. Though many studies have focused on the role of Al3Sc in the deformation and recrystallization of pre-aged or hot deformed Al-Sc alloys, recent studies on the annealing response of solutionized and cold rolled material have shown various possibilities for microstructural stability depending on the relative kinetics of precipitation and recrystallization. In this study, the microstructural evolution of solutionized and cold rolled Al- 2.9wt%Mg-0.16wt%Sc has been followed in order to evaluate the role of imposed strain and annealing temperature on the recrystallization kinetics.

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29

Yu, Tian Bo, and Niels Hansen. "A Model for Recovery Kinetics of Aluminum after Large Strain." Materials Science Forum 715-716 (April 2012): 374–79. http://dx.doi.org/10.4028/www.scientific.net/msf.715-716.374.

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A model is suggested to analyze recovery kinetics of heavily deformed aluminum. The model is based on the hardness of isothermal annealed samples before recrystallization takes place, and it can be extrapolated to longer annealing times to factor out the recrystallization component of the hardness for conditions where recovery and recrystallization overlap. The model is applied to the isothermal recovery at temperatures between 140 and 220°C of commercial purity aluminum deformed to true strain 5.5. EBSD measurements have been carried out to detect the onset of discontinuous recrystallization. Furthermore, comparison between the present model and a similar recently developed recovery model is made, and the result is discussed.

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30

Skrotzki, Werner, K. Kegler, R. Tamm, and C. G. Oertel. "Recrystallization of Iron Aluminides." Materials Science Forum 467-470 (October 2004): 525–30. http://dx.doi.org/10.4028/www.scientific.net/msf.467-470.525.

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Cast iron aluminides of three compositions were strongly deformed by hot extrusion and subsequently annealed. The texture development and kinetics of recrystallization were determined by local and global texture measurements. The deformation texture of Fe-10Al (A2 structure) is a <110>-fibre, Fe-35Al and Fe-50Al (B2 structure) show a <100>-<110> double fibre texture with <110> dominating Fe-35Al. The texture change with composition is due to a change in slip system. The deformed samples are partially dynamically recrystallized. The recrystallization components are aligned along the symmetry line <100>- <110> and towards <114> for Fe-10Al. For the other alloys the recrystallization texture is <111> with a tendency to <112>. The texture components do not change during static recrystallization. In general, the recrystallization texture is quite weak. The microstructure is very inhomogeneous ranging from deformed, strongly recovered to recrystallized areas. Beside primary recrystallization abnormal grain growth takes place. The heterogeneity of recrystallization makes it difficult to quantify the kinetics of recrystallization. The results are discussed with respect to the order of the alloys.

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31

Su, Juan Hua, Ya Wei Han, Feng Zhang Ren, and Zhi Qiang Chen. "Dynamic Recrystallization Behavior of Pure Titanium." Advanced Materials Research 852 (January 2014): 66–70. http://dx.doi.org/10.4028/www.scientific.net/amr.852.66.

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The dynamic recrystallization of commercially pure titanium was investigated by compression tests on Gleeble-1500D thermal simulation test machine at temperature of 700950 °C and strain rate of 0. 015 s1. The total compression deformation is 0.7(true strain). The kinetics of dynamic recrystallization of commercially pure titanium at 950 °C was modeled by Avrami equation. The results show that the dynamic recovery and recrystallization obviously occur during compression. The flow stress increases to a peak value and gradually decreases to a steady state. The flow stress is decreased with the increase of deformation temperature and it is increased with the increase of strain rate. The Avrami kinetics model of dynamic recrystallization of commercially pure titanium at 950 °C is obtained .

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32

Aryshenskii, Evgeniy V., Jürgen Hirsch, Erkin D. Beglov, Sergey V. Konovalov, and Vladimir R. Kargin. "Specific of the Recrystallization Driving Force Calculation on the early Stages of Thermomechanical Treatment of Aluminum Alloys." Materials Science Forum 1037 (July 6, 2021): 273–80. http://dx.doi.org/10.4028/www.scientific.net/msf.1037.273.

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The article investigates the effect of the strain rate on the driving force of recrystallization during hot working of the as-cast structure. For the study, we applied previously obtained experimental data of recrystallization kinetics during this stage of thermomechanical treatment. In addition, hot laboratory rolling, followed by saltpeter bath soaking, were performed in order to obtain supplemental data on grain structure size and orientations. Grain structure size was examined by optical microscopy, and its orientation was examined by X-ray texture analysis. The studies demonstrated, that overestimated recrystallization driving force not only results in erroneous kinetics estimation, but also gives excessive number of recrystallization centers and undersized grain structure. Besides, unaccounted effect of recrystallization driving force on grain size leads to distorted predictions of texture composition. In order to avoid this, it was recommended to apply an special exponential accumulated strain dependent coefficient.

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33

Lindkvist, A., T. Holm Johansen, L. Kørup Pedersen, Y. Zhang, and D. Juul Jensen. "Recrystallization kinetics of cold rolled Gum Metal." IOP Conference Series: Materials Science and Engineering 1249, no. 1 (July 1, 2022): 012022. http://dx.doi.org/10.1088/1757-899x/1249/1/012022.

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Abstract A wire of a β-Titanium alloy known as Gum Metal was cold rolled to a reduction of 80% and heat treated for times in the range 3-120 minutes at a fixed temperature of 740 °C to yield a set of partially recrystallized microstructures. The recrystallization course was evaluated by light optical microscopy and Electron Backscatter Diffraction, based on which the recrystallization kinetics was analysed using the Johnson-Mehl-Avrami-Kolmogorov (JMAK) model. This analysis showed that the kinetics of this material does not follow the traditional JMAK behaviour but has two distinct stages with very different Avrami exponents.

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34

Fellah, Lahcene, Abdallah Diha, and Zakaria Boumerzoug. "MICROSTRUCTURAL STUDY AND RECRYSTALLIZATION KINETICS OF DEFORMED COMMERCIAL COPPER WIRES." Acta Metallurgica Slovaca 24, no. 1 (March 22, 2018): 32. http://dx.doi.org/10.12776/ams.v24i1.1011.

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This work aims to investigate the microstructure after cold-wiredrawing process of commercial copper and its recrystallization kinetics under isochronal annealing. In this paper, the samples studied are commercial copper wires reduced at six different reductions by a wiredrawing at room temperature. Optical microscopy, Scanning Electron Microscopy (SEM), and DSC were used as characterization techniques. The samples were annealed under Argon atmosphere with four different heating rates by using DSC. The Kissinger, Ozawa, Boswell, and Starink methods were used to determine the recrystallization kinetics. The results showed that the cold-wiredrawing had caused the elongation of grains along the main axis of the wires also showed the existence of slip bands. It has been found, on the one side, that the recrystallization temperature increased and shifted to higher temperatures as the heating rate increased, which means that this reaction is thermally actived; On the other sidethe recrystallization temperature clearly shifted to lower temperatures as the deformation increased, which indicated that recrystallization is profoundly enhanced by high deforming.We noted a decrease in the activation energy values when the reduction increases, the activation energy for the most reduced materials were lower than that in the less reduced wires.

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35

Brandt, Felix, Martina Klinkenberg, Jenna Poonoosamy, Juliane Weber, and Dirk Bosbach. "The Effect of Ionic Strength and Sraq upon the Uptake of Ra during the Recrystallization of Barite." Minerals 8, no. 11 (November 2, 2018): 502. http://dx.doi.org/10.3390/min8110502.

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Recrystallization and solid-solution formation with barite is considered as relevant retention mechanism for 226Ra in long-term scenarios of nuclear waste management. Here, we studied the effect of ionic strength and the presence of Sr in solution upon the Ra-uptake kinetics and final Ra concentrations in solution by recrystallizing barite in solution with varying Sr and NaCl concentration and temperature for up to 1000 days. Final Ra-concentrations were interpreted based on thermodynamic modelling. Our results indicate a slight decrease of the retention potential of barite for Ra but little effect on the uptake kinetics due to the increase of ionic strength from. 0.1 mol/kg to 1.0 mol/kg of NaCl. The final concentrations at solid/liquid ratio of 0.5 g/kg are well described based on available thermodynamic models whereas at 5 g/kg additional Ra uptake probably due to kinetic effects was observed. On the contrary, the presence of Sr in solution can have a significant inhibiting kinetic effect on the uptake kinetics and lower the final Ra-uptake. In some cases, with low solid/liquid ratio or at ambient conditions, Sr completely inhibits barite recrystallization. In all other cases, Ra, Ba and Sr were taken up as thermodynamically predicted at the end of the experiments.

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36

Su, Jing, Mehdi Sanjari, Abu Syed Kabir, In Ho Jung, and Steve Yue. "Static Recrystallization Characteristic of Low Temperature Rolled AZ31 Magnesium Alloy during Annealing." Materials Science Forum 828-829 (August 2015): 239–43. http://dx.doi.org/10.4028/www.scientific.net/msf.828-829.239.

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Microstructure evolution and static recrystallization kinetics of a magnesium AZ31 alloy during annealing have been investigated. The Mg alloy sheets were rolled at 100°C at a low rolling speed of 15m/min and a high rolling speed of 1000m/min to reductions of 8%, 23% and 30%. Annealing was then conducted on the as-rolled specimens at 200°C for different times. The microstructure was characterized by optical microscopy and recrystallization kinetics were evaluated by means of Johnson-Mehl-Avrami-Kolmogorov (JMAK) model. The softening behavior was found to be divided into two annealing stages. The first stage was related to the recrystallization on high stored energy regions, such as shear bands and twins, while the second stage was associated to the recrystallization of low stored energy areas.

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Jorge-Badiola, D., J. L. Lanzagorta, and Isabel Gutiérrez. "A Step Forward in the Understanding of the Strain Reversal Effect on the Recrystallization Kinetics after Hot Working." Materials Science Forum 715-716 (April 2012): 643–48. http://dx.doi.org/10.4028/www.scientific.net/msf.715-716.643.

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A reversion of the strain produces a modification of the static recrystallization kinetics. Initially, the reversion increases the recrystallization time, that reaches a maximum at a certain strain, and decreases again for increasing reverse strains. This transient on recrystallization kinetics develops over a strain interval similar to that of the microstructural and stress-strain transients. At strains beyond the transient, the reversion can be regarded as a shift on the strain axis. However, at the authors knowledge there is no formulation able to describe the material behaviour during the transient. The present work introduces an equivalent strain concept based on the substructural dissolution/build-up processes taking place as a result of the strain reversal. This formulation allows including the effect of the strain path on recrystallization models.

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38

Vandermeer, R. A., and Dorte Juul Jensen. "Effects of Nuclei Clustering on Recrystallization Kinetics." Materials Science Forum 467-470 (October 2004): 193–96. http://dx.doi.org/10.4028/www.scientific.net/msf.467-470.193.

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In this work, it is shown that the contiquity ratio, Crr, defined as the fraction of the total grain boundary area of recrystallized grains shared by other recrystallized grains, is a useful experimental parameter for describing the clustering of recrystallization nuclei in partially recrystallized microstructures. Two experimental examples are presented where anisotropic impingement behavior, i.e. non random recrystallized grain distributions, is thought to be important. In the experimental examples, the deviation of Crr from Crr = Vv which is a characteristic of a random distribution, is clearly shown. The results justify the need for these cases to be modelled, as had been done, by impingement patterns other than the simple random nucleation behavior so often postulated without proof in recrystallization kinetics studies.

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39

Voronova, L. M., M. V. Degtyarev, and T. I. Chashchukhina. "Recrystallization Kinetics of Niobium with Submicrocrystalline Structure." Physics of Metals and Metallography 120, no. 10 (October 2019): 949–55. http://dx.doi.org/10.1134/s0031918x19100144.

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40

Džubinský, Mikola, František Kováč, and Martin Černı́k. "Secondary recrystallization kinetics in GO electrotechnical steels." Journal of Magnetism and Magnetic Materials 215-216 (June 2000): 83–85. http://dx.doi.org/10.1016/s0304-8853(00)00072-x.

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41

Price, C. W. "Simulations of grain impingement and recrystallization kinetics." Acta Metallurgica 35, no. 6 (June 1987): 1377–90. http://dx.doi.org/10.1016/0001-6160(87)90020-4.

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42

Woldt, E., and D. Juul Jensen. "Recrystallization kinetics in copper: Comparison between techniques." Metallurgical and Materials Transactions A 26, no. 7 (July 1995): 1717–24. http://dx.doi.org/10.1007/bf02670758.

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43

Khoddam, S., P. D. Hodgson, and H. Beladi. "Computational inverse analysis of static recrystallization kinetics." International Journal of Mechanical Sciences 103 (November 2015): 97–103. http://dx.doi.org/10.1016/j.ijmecsci.2015.09.008.

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44

Volovitch, Polina, Thierry Baudin, Richard Penelle, F. Caleyo, and Laurent Barrallier. "Role of Recovery in the Recrystallization Simulation Application to a Cold Rolled IF-Ti Steel and a Cold Drawn Copper Wire." Materials Science Forum 550 (July 2007): 453–58. http://dx.doi.org/10.4028/www.scientific.net/msf.550.453.

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A simple model including the recovery and nucleation kinetics is proposed to simulate recrystallization using a Monte Carlo technique. Nucleation is simulated on the basis of equations describing stored energy evolution and subgrain growth kinetics. The parameters describing the stored energy evolution during recovery are shown to influence not only the relative number, orientation and local distribution of nuclei, but also the recrystallization kinetics and the final texture. The estimated kinetics of nucleation, the mean stored energy evolution as well as the preferential texture of first nuclei are in agreement with experimental observations for annealing 40% cold-rolled IF-Ti steel and cold drawn copper wires.

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45

Luo, Haiwen, Jilt Sietsma, and Sybrand van der Zwaag. "Characteristics of the Static Recrystallization Kinetics of an Intercritically Deformed C-Mn Steel." Materials Science Forum 467-470 (October 2004): 293–98. http://dx.doi.org/10.4028/www.scientific.net/msf.467-470.293.

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The austenite recrystallization kinetics in the intercritical region of a C-Mn steel is investigated by means of stress relaxation tests. It is found that the Avrami exponent, n, decreases significantly with decreasing temperature, i.e. with increasing ferrite fraction. This behaviour deviates from that of austenite recrystallization in the purely austenitic state, in which case the Avrami exponent is constant and independent of temperature and deformation. To interpret this, the influence of spatial variation of the plastic strain in the intercritical austenite grains on recrystallization kinetics is modelled quantitatively. The modelling results seem to indicate that the strain heterogeneity is responsible for the decreasing Avrami exponent with decreasing intercritical temperature.

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Martínez-de-Guereñu, Ane, M. Oyarzabal, F. Arizti, and Isabel Gutiérrez. "Application of Coercive Field Measurements to the Evaluation of Recovery and Recrystallization in Cold Rolled Interstitial Free (IF) Steel." Materials Science Forum 500-501 (November 2005): 647–54. http://dx.doi.org/10.4028/www.scientific.net/msf.500-501.647.

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The recovery and recrystallization kinetics of a cold rolled interstitial free (IF) steel were studied during isothermal annealing. Magnetic methods based on coercive field measurements, hardness tests and metallography were applied so as to follow the kinetics experimentally. The coercive field measurement technique reveals a higher degree of resolution for monitoring recovery than conventional hardness determination and also allows the recrystallization progress to be monitored. The results obtained are compared to those previously determined for a non-stabilized extra low carbon (ELC) steel. The observed differences are discussed in terms of the presence of microalloying elements, Ti and Nb, which slow down recovery and delay recrystallization.

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Meyer, Nicolas, Yves Bréchet, Muriel Véron, Marc Mantel, Pierre Emmanuel Dubois, and Oliver Geoffroy. "Influence of Nb Stabilization on the Recovery and Recrystallization Kinetics of a Ferritic Stainless Steel: Consequences on Magnetic Losses." Materials Science Forum 558-559 (October 2007): 253–58. http://dx.doi.org/10.4028/www.scientific.net/msf.558-559.253.

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Softening kinetics of two 17% chromium (Cr) stainless steel grades that differ in niobium (Nb) content are compared. In the experiments, we observed that a low Nb stabilization makes recrystallization nucleation much faster and prevents incomplete recrystallization. A qualitative interpretation, based on interaction with precipitates, is proposed and explains the main features of the softening kinetics as well as the microstructures obtained. For the Nb stabilized grade, magnetic losses were measured in the deformed state and after recrystallization. Above a specific magnetizing frequency, the deformed state led to smaller losses than the recrystallized state. These results are believed to be attributed to a grain size effect.

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Yoon, Dae Hwan, Ya Zhang, and Dong Won Jung. "A Study on Dynamic Recrystallization Kinetics Model of 45Cr4NiMoV." Applied Mechanics and Materials 789-790 (September 2015): 160–64. http://dx.doi.org/10.4028/www.scientific.net/amm.789-790.160.

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The dynamic recrystallization critical strain of this alloy was investigated by Poliak and other scholars using the hardening rate (θ) method; they thought the critical condition corresponded to the inflection point of the lnθ-ε curve and the minimum value on the ∂ (lnθ)/∂ε-ε curve. A dynamic recrystallization critical strain model of 45Cr4NiMoV was established.

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Kim, Dong Kyu, K. H. Jung, H. W. Lee, and Yong Taek Im. "Cellular Automata Simulation of Textural Evolution during Primary Static Recrystallization of IF Steel." Materials Science Forum 702-703 (December 2011): 615–18. http://dx.doi.org/10.4028/www.scientific.net/msf.702-703.615.

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A two dimensional probabilistic cellular automata model is used to simulate primary static recrystallization of interstitial free (IF) steel. The present study is to investigate the effect of curvature-driven pressure that is induced by protrusions/retrusions of recrystallization fronts on the microstructural and textural evolution during recrystallization. It was found that local interface migration of protrusions/retrusions of recrystallization fronts could significantly affect the kinetics, grain morphology and annealing texture according to the present investigation.

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Geisler, Thorsten, Robert T. Pidgeon, Wilhelm van Bronswijk, and Ron Pleysier. "Kinetics of thermal recovery and recrystallization of partially metamict zircon: a Raman spectroscopic study." European Journal of Mineralogy 13, no. 6 (November 26, 2001): 1163–76. http://dx.doi.org/10.1127/0935-1221/2001/0013-1163.

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