Multimodal Microstructure of Mg-Gd-Y Alloy Through an Integrated Simulation of “Process-Structure-Property”

doi:10.11900/0412.1961.2021.00222

Acta Metall Sin

2022, Vol. 58

Issue (1): 114-128 DOI: 10.11900/0412.1961.2021.00222

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Multimodal Microstructure of Mg-Gd-Y Alloy Through an Integrated Simulation of “Process-Structure-Property”

LI Shaojie¹, JIN Jianfeng¹^,²(

), SONG Yuhao¹, WANG Mingtao¹, TANG Shuai², ZONG Yaping¹, QIN Gaowu¹(

)

^1. School of Materials Science and Engineering, Northeastern University, Shenyang 110819, China
^2. State Key Laboratory of Rolling and Automation, Northeastern University, Shenyang 110819, China

Cite this article:

LI Shaojie, JIN Jianfeng, SONG Yuhao, WANG Mingtao, TANG Shuai, ZONG Yaping, QIN Gaowu. Multimodal Microstructure of Mg-Gd-Y Alloy Through an Integrated Simulation of “Process-Structure-Property”. Acta Metall Sin, 2022, 58(1): 114-128.

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Abstract

Rare earth Mg alloys containing Gd elements can be used in aerospace, automotive, and other industrial fields owing to their high strength and creep resistance at room and high temperatures. However, the poor ductility of Mg alloys limits their application. Recently, it was discovered that the ductility of Mg alloy can be improved without compromising on its strength if sufficient amount of coarse grains is distributed in fine grains. In this study, taking the Mg-8Gd-3Y-0.5Zr (GW83K) alloy as an example, an approach for optimizing multimodal microstructures was investigated, which aimed to improve the mechanical properties of alloys. An alloy with a multimodal grain structure can be used as a particulate compound model, in which the grain boundary is considered the matrix, and different-sized grains are treated as different-types of particles embedded into the grain boundary matrix. A 2D finite element micromechanics model combined with Taylor-based nonlocal plasticity theory, which considers the size effect of the particles, was established to simulate the mechanical response of the multimodal structure Mg alloy in a tensile test. The model was verified through the experimental data of the stress-strain curve. Moreover, the effects of process parameters on the mechanical properties of the GW83K alloy were further evaluated by combining the grain structure under different annealing processes, simulated from a real space-time phase-field model as the geometric input of the finite element model. Finally, the relationships between the annealing parameters, multimodal structure, and mechanical properties of the GW83K alloy were described. The results show that the yield and tensile strengthes of the multimodal GW83K alloy presented a Hall-Petch relationship with the average grain size. The content and distribution of coarse grains greatly affected the plasticity of the GW83K alloy. By annealing the GW83K alloy at 623 K for 90 min, better plasticity could be achieved without sacrificing strength, which is helpful in promoting multimodal microstructural design.

Key words: magnesium alloy multimodal grain mechanical property microstructural design finite element method

Received: 21 May 2021

ZTFLH:

TG113.25

Fund: National Key Research and Development Program of China(2016YFB0701204);Project of Introducing Talents of Discipline to Universities(B20029);Fundamental Research Funds for the Central Universities(N2007011)

About author: QIN Gaowu, professor, Tel: (024)83691565, E-mail: qingw@smm.neu.edu.cn
JIN Jianfeng, associate professor, Tel: 13194248493, E-mail: jinjf@atm.neu.edu.cn

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	Shaojie LI
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	Yaping ZONG
	Gaowu QIN

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https://www.ams.org.cn/EN/10.11900/0412.1961.2021.00222 OR https://www.ams.org.cn/EN/Y2022/V58/I1/114

Fig.1 Free energy-component data of GW83K Mg alloy at 623, 673, and 723 K, and their fitting curves (c _Gd—concentration of Gd)

T	A	A ₁	A ₂	B ₁	B ₂	$L ̂$	c ₁	ϕ ^2nd	f ^2nd	d ^2nd
K	kJ·mol^-1	kJ·mol^-1	kJ·mol^-1	kJ·mol^-1	kJ·mol^-1	mol·s^-1·J^-1			%	μm
623	-49.2	297.3	-775.2	371	51.2	0.45	0.46	Lath	0.67	1-2
673	-52.6	308	-869.6	365.7	51.2	1.22	0.46	Lath	1.35	1-2
723	-55.9	322.4	-901.1	373.7	51.2	2.72	0.46	Sphere	1.35	1-2

Table 1 Parameters in the phase-field model for grain growth

Fig.2 Averaged grain sizes obtained by phase field simulation and experiment^[67] under different annealing processes

Fig.3 Schematics of the finite element (FE) model for GW83K Mg alloy with multimodal grain size distribution

Fig.4 Experimental tensile stress-strain (σ-ε) curves and constitutive input curves for monolithic grain GW83K Mg alloy with different grain sizes
(a) experimental data^[13,74] (

d ˉ

—average grain size from experiment,

d 1 g

d 6 g

—grain size ranges of the grain-interior phases 1-6)
(b) constitutive inputs of grain-interior phases 1-6 (

g 1 i n

g 6 i n

) for finite element model

Fig.5 Predicted results from the finite element model for GW83K Mg alloy during tensile loading
(a) comparison of the predicted σ-ε curves with the experimental data^[13]
(b) von Mises equivalent (EQV.) stress contours under the applied strain of 11%
(c) EQV. strain contours under the applied strain of 11% (GB—grain boundary-matrix phase)

Table 2 The values of annealing temperature and time in phase field models for GW83K Mg alloy

Fig.6 Microstructures and grain size distributions of GW83K Mg alloy under different annealing processes
(a, b) microstructures from phase field models with and without the 2nd phase particles after annealing at 723 K for 90 min, respectively
(c) grain size distributions for Figs.6a and b
(d)

d ˉ

from the phase field model with and without the 2nd phase particles under different annealing processes

Fig.7 Microstructures (a) and geometric models (b) of GW83K Mg alloy without the 2nd phase particle from phase-field simulation at different annealing temperatures and time (marked with model Nos.1-9, grain-interior phases 1-6 marked by different colors and grain boundaries marked by black)

Fig.8 Microstructure characteristics in finite element model of GW83K Mg alloy
(a) volume fraction of grain boundary (f _GB) and

d ˉ

of model Nos.1-9
(b-d) grain size distributions under 623 K, 673 K, and 723 K for different annealing time, respectively

Fig.9 Simulation results of finite element model of GW83K Mg alloys under different annealing processes
(a) σ-ε curves
(b) relationship among average grain size and yield strength (σ _y), tensile strength (σ _s), and total elongation (ε _s)
(c) EQV. strain contours of model Nos.1-9, distinguished by the critical strain (ε _CR)
(d) relationship among the

d ˉ

and proportion of slip band (γ _s

) ?

and volume fraction of coarse grains (f _CG)

Fig.10 Mechanical responses from finite element model for GW83K Mg alloy with and without the 2nd phase particles from model A, B, and C after annealing at 723 K for 90 min (a) and EQV. strain contours of models A and C under fractured strain (b) (Model A is the FE simulation from microstructure with the 2nd phase particles after annealing, model B is from microstructure without the 2nd phase particles after annealing, and model C is from Fig.10a without the 2nd phase particles)

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