scholarly journals Simulation of the Texture Evolution During Annealing of Cold Rolled Bcc and Fcc Metals Using a Cellular Automation Approach

1997 ◽  
Vol 28 (3-4) ◽  
pp. 211-218 ◽  
Author(s):  
V. Marx ◽  
D. Raabe ◽  
O. Engler ◽  
G. Gottstein
Keyword(s):  
Static Recrystallization ◽  
Texture Evolution ◽  
Three Dimensional ◽  
Deformation Texture ◽  
Three Dimensional Model ◽  
Static Recovery ◽  
Fcc Metals ◽  
Cellular Automation ◽  
Texture Change ◽  
Cold Rolled

In this study both primary static recrystallization and static recovery of cold rolled bcc and fcc metals and alloys are numerically simulated using a three-dimensional model that is based on a modified cellular automaton approach. The model considers the influence of the initial deformation texture and microstructure on both static recovery and primary static recrystallization with a high spatial resolution. The cellular automat technique provides both local and statistical information about the kinetics, the morphology and the texture change during annealing. The influence of nucleation and growth can be studied in detail. The simulations are compared to experimental results obtained on fcc and bcc polycrystals.

Recrystallization of Iron Aluminides

2004 ◽  
Vol 467-470 ◽  
pp. 525-530 ◽  
Author(s):  
Werner Skrotzki ◽  
K. Kegler ◽  
R. Tamm ◽  
C.G. Oertel
Keyword(s):  
Recrystallization Texture ◽  
Static Recrystallization ◽  
Hot Extrusion ◽  
Deformation Texture ◽  
Primary Recrystallization ◽  
Iron Aluminides ◽  
The Other ◽  
Texture Change ◽  
Kinetics Of ◽  
B2 Structure

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.

Texture evolution during static recrystallization of cold-rolled magnesium alloys

2016 ◽  
Vol 105 ◽  
pp. 479-494 ◽  
Author(s):  
Z.R. Zeng ◽  
Y.M. Zhu ◽  
S.W. Xu ◽  
M.Z. Bian ◽  
C.H.J. Davies ◽  
...  
Keyword(s):  
Magnesium Alloys ◽  
Static Recrystallization ◽  
Texture Evolution ◽  
Cold Rolled

Spatially Inhomogeneous Recrystallization in Ferritic Stainless Steels

2012 ◽  
Vol 715-716 ◽  
pp. 866-871 ◽  
Author(s):  
Guillaume Lefebvre ◽  
Sina Shahandeh ◽  
Chad W. Sinclair ◽  
Matthias Militzer ◽  
Jean Denis Mithieux ◽  
...  
Keyword(s):  
Static Recrystallization ◽  
Grain Shape ◽  
Deformation Texture ◽  
Local Deformation ◽  
Physical Explanation ◽  
Ferritic Stainless Steels ◽  
Spatially Inhomogeneous ◽  
Cold Rolled ◽  
Kinetics Of ◽  
Made In

The kinetics of static recrystallization in cold rolled ferritic stainless steel sheet tends to slow drastically over the last 10-20% of recrystallization. This has its origins in both the microstructure (deformed grain shape, precipitates) and in the local deformation texture. In this work we have sought to provide a physical explanation for the slow last stages of recrystallization through a texture dependent JMAK model which is informed by the microstructure of the partially recrystallized microstructure. The geometrical assumptions made in developing this JMAK model have been compared to phase field simulations using experimental observations as the source of their starting configuration.

Texture Development in Pure Mg and Mg Alloy AZ31

2005 ◽  
Vol 495-497 ◽  
pp. 623-632 ◽  
Author(s):  
Günter Gottstein ◽  
T. Al Samman
Keyword(s):  
Static Recrystallization ◽  
Texture Evolution ◽  
Texture Development ◽  
Mg Alloy ◽  
High Temperature Deformation ◽  
Temperature Deformation ◽  
Alloy Az31 ◽  
The Poor ◽  
Texture Change ◽  
Similar Texture

Texture evolution in pure Mg and Mg alloy AZ31 during deformation and annealing was investigated. The poor low temperature ductility can be attributed to both, insufficient shear systems and unfavorable deformation geometry. Static recrystallization was shown to proceed discontinuously despite little texture change. High temperature deformation was accompanied by dynamic recrystallization with similar texture development as during static recrystallization.

Deformation Texture of Ti-26mol%Nb-3mol%Al β-Titanium Alloy

2012 ◽  
Vol 706-709 ◽  
pp. 1899-1902 ◽  
Author(s):  
Tomonari Inamura ◽  
Ryutaro Shimizu ◽  
Hideki Hosoda ◽  
Shuichi Miyazaki
Keyword(s):  
Recrystallization Texture ◽  
Room Temperature ◽  
Texture Evolution ◽  
Parent Phase ◽  
Reduction Rate ◽  
Deformation Texture ◽  
Cold Rolled ◽  
Superelastic Deformation ◽  
Rate Optimization ◽  
Start Temperature

The effect of reduction rate on the deformation texture of cold-rolled Ti-26mol%Nb-3mol%Al shape memory alloy was investigated. The alloy is the parent phase (β: bcc) at room temperature (RT) and the martensite start temperature is much lower than RT; no residual martensite was detected after cold-rolling. The reduction rate,r, was varied in the range of 60 ~ 99%. Texture evolution was as following; γ-fiber à {001}<110> à {001}<110> + {112}<110> (α-fiber). The strength of {001}<110> was maximized at aboutr= 97%. The recrystallization texture is expected to be controlled by the reduction rate; optimization ofris supposed to be promising to obtain the {001}<110> recrystallization texture that is preferred for superelastic deformation.

scholarly journals Distinct Recrystallization Pathways in a Cold-Rolled Al-2%Mg Alloy Evidenced by In-Situ Neutron Diffraction

2018 ◽  
Vol 2 (3) ◽  
pp. 17 ◽  
Author(s):  
Grigoreta Stoica ◽  
Luc Dessieux ◽  
Alexandru Stoica ◽  
Sven Vogel ◽  
Govindarajan Muralidharan ◽  
...  
Keyword(s):  
Neutron Diffraction ◽  
Texture Evolution ◽  
Deformation Texture ◽  
Mg Alloy ◽  
Scanning Calorimetry ◽  
Los Alamos ◽  
Oak Ridge ◽  
Quasi Monte Carlo ◽  
Cold Rolled

The time-of-flight neutron diffraction data collected in-situ on Oak Ridge National Laboratory’s (ORNL, Oak Ridge, TN, USA) VULCAN and Los Alamos National Laboratory’s (LANL, Los Alamos, NM, USA) High-Pressure-Preferred-Orientation (HIPPO) diffractometers have been analyzed complementarily to show the texture evolution during annealing of a cold-rolled Al-2%Mg alloy. The texture analysis aimed to identify the components present in the initial rolling (or deformation) texture and in the thermally-activated recrystallization texture, respectively. Using a quasi-Monte-Carlo (QMC) approach, a new method has been developed to simulate the weighted texture components, and to obtain inverse pole figures for both rolling and normal directions. As such, distinct recrystallization pathways during annealing in isochronal conditions, can be revealed in terms of the evolution of the texture components and their respective volume fractions. Moreover, the recrystallization kinetics associated with the cube and random texture components are analyzed quantitatively using a similar approach developed for differential scanning calorimetry (DSC).

Annealing of Deformed Materials Developed by Continuous/Discontinuous Dynamic Recrystallization

2007 ◽  
Vol 550 ◽  
pp. 327-332 ◽  
Author(s):  
Taku Sakai ◽  
Hiromi Miura
Keyword(s):  
Dynamic Recrystallization ◽  
Room Temperature ◽  
Static Recrystallization ◽  
Pure Copper ◽  
Large Strains ◽  
Static Recovery ◽  
Fine Grained ◽  
Texture Change ◽  
Characteristic Nature ◽  
Fine Grained Structure

Annealing behaviour was studied in deformed copper developed by continuous or discontinuous dynamic recrystallization (cDRX or dDRX). Pure copper was deformed to large strains by multi-directional forging at room temperature, resulting in an ultra-fine grained structure due to operation of cDRX. Subsequent annealing of such a fine-grained copper can be controlled mainly by grain growth accompanied with recovery and no texture change, that is continuous static recrystallization (cSRX). On the other hand, 4 kinds of static restoration processes operate during annealing of dDRXed copper, i.e. metadaynamic recovery and recystallization (mDRV and mDRX), and classical static recovery and recrystallization. The stable existence of mDRVed grains containing moderate dislocations leads to incomplete recrystallization even after a long period of annealing time. It is discussed how such various types of annealing processes, occurring in cDRXed or dDRXed matrices, can be connected with the characteristic nature of the deformed microstructures.

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