A Phase-field Model to Simulate Recrystallization in an AZ31 Mg Alloy in Comparison of Experimental Data

材料科学技术（英）, 2008, 24(6): 829-834.

^1, , ^2, , ^3,

1.School of Materials and Metallurgy, Northeastern University, Shenyang 110004, China

2.School of Materials and Metallurgy, Northeastern University, Shenyang 110004, China

3.School of Materials and Metallurgy, Northeastern University, Shenyang 110004, China

基金项目: 国家自然科学基金(50771028;504.71024) Education Min-istry of China for an outstanding teacher research fund to this study

A Phase-field Model to Simulate Recrystallization in an AZ31 Mg Alloy in Comparison of Experimental Data

Mingtao WANG ^1, , B.Y.Zong ^2, , Gang WANG ^3,

1.School of Materials and Metallurgy, Northeastern University, Shenyang 110004, China

2.School of Materials and Metallurgy, Northeastern University, Shenyang 110004, China

3.School of Materials and Metallurgy, Northeastern University, Shenyang 110004, China

Keywords： Static recrystallization

A model has been established to simulate the realistic spatio-temporal microstructure evolution in recrystal-lization of a magnesium alloy using the phase field approach.A set of rules have been proposed to decide the real physical value of all parameters in the model.The thermodynamic software THERMOCALC is applied to determine the local chemical free energy and strain energy,which is added to the free energy density of grains before recrystallization.The Arrhenius formula is used to describe boundary mobility and the activity energy is suggested with a value of zinc segregation energy at the boundary.However,the mobility constant in the formula was found out by fitting to a group of grain size measurements during recrystallization of the alloy.The boundary range is suggested to decide the gradient parameters in addition of fitting to the experimental boundary energy value.These parameter values can be regarded as a database for other similar simulations and the fitting rules can also be applied to build up databases for any other alloy systems.The simulated results show a good agreement with reported experimental measurement of the alloy at the temperatures from 300 to 400℃ for up to 100 min but not at 250℃.This implies a mechanism variation in activity energy of the boundary mobility in the alloy at low temperature.

参考文献

[1]	H Ramanarayan;T A Abinandanan .[J].Physical A,2003,318:213.
[2]	P Poduri;L Q Chen .[J].Acta Materialia,1998,46:3915.
[3]	W Guo;Y P Zong;G Wand;L Zuo .[J].Journal of Materials Science and Technology,2004,20(03):245.
[4]	D.Y.Li;L.Q.Chen .Computer simulation of stress-oriented nucleation and growth of θ ' precipitates in Al-Cu alloys[J].Acta materialia,1998(8):2573-2585.
[5]	X. Q. Ma;S. Q. Shi;C. H. Woo;L. Q. Chen .Phase-field simulation of hydride precipitation in bi-crystalline zirconium[J].Scripta materialia,2002(4):237-241.
[6]	J Z Zhu;T Wang;A J Ardell;S H Zhou Z K Liu and L Q Chen .[J].Acta Materialia,2004,522:837.
[7]	Y. Wang .Field kinetic model and computer simulation of precipitaation of Ll2 ordered intermetallics from F. C. C. solid solution[J].Acta materialia,1998(9):2983-2988.
[8]	Y. Ustinovshikov;I. Igumnov;V. Koretsky .Decomposition of solid solutions having a tendency toward ordering or separation[J].Computational Materials Science,2001(2):185-196.
[9]	J.Z. Zhu;Z.K. Liu;V. Vaithyanathan .Linking phase-field model to CALPHAD: application to precipitate shape evolution in Ni-base alloys[J].Scripta materialia,2002(5):401-406.
[10]	Y. H. Wen;B. Wang;J. P. Simmons .A phase-field model for heat treatment applications in Ni-based alloys[J].Acta materialia,2006(8):2087-2099.
[11]	V Marx;F R Reher;G Gottstein .[J].Acta Metallurgica,1999,47:1219.
[12]	B Radhakrishnan;G B Saxma;T Zacharia .[J].Acta Metallurgica,1998,46:4415.
[13]	Raochuan LIU;Lingyun WANG;Leigang GU;Guangsheng HUANG .[J].Light Alloy Fabrication Technology,2004,32:22.
[14]	J W Cahn .[J].Acta Metallurgica,1961,9:795.
[15]	S M Allen;J W Cahn .[J].Acta Metallurgica,1979,27:1085.
[16]	D N Fan;L Q Chen .[J].Acta Materialia,1997,45:611.
[17]	C E Krill III;L Q Chen .[J].Acta Metallurgica,2002,50:3057.
[18]	G Moreau;J A Cornet;D Calais .[J].J Nuci Mater,1971,38:197.
[19]	R D Doherty;D A Hughes;F J Humphreys;J J Jonas D Juul Jensen M E Kassner W E King T R McNelley H J McQueen and A D Rollett .[J].Materials Science and Engineering A:Structural Materials Properties Microstructure and Processing,1997,238:219.
[20]	M. Verdier;I. Groma;L. Flandin;J. Lendvai;Y. Bréchet;P. Guyot .Dislocation densities and stored energy after cold rolling of Al-Mg alloys: Investigations by resistivity and differential scanning calorimetry[J].Scripta materialia,1997(4):449-454.
[21]	N A Gjostein;F N Rhines .[J].Acta Metallurgica,1959,7:319.
[22]	K Lücke;K Detert .[J].Acta Metallurgica,1957,5:628.
[23]	C.W. Su;L. Lu;M.O. Lai .A model for the grain refinement mechanism in equal channel angular pressing of Mg alloy from microstructural studies[J].Materials Science & Engineering, A. Structural Materials: Properties, Misrostructure and Processing,2006(1/2):227-236.

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A Phase-field Model to Simulate Recrystallization in an AZ31 Mg Alloy in Comparison of Experimental Data

参考文献