相场模拟研究AZ31B镁合金的动态再结晶

许可; 盛杰; 刘瑜; 黄厚兵; 施小明; 宋海峰

doi:10.11858/gywlxb.20230780

相场模拟研究AZ31B镁合金的动态再结晶

doi: 10.11858/gywlxb.20230780

许可^{1, 2, 3,},
盛杰³,
刘瑜^3,*, ,,
黄厚兵²,
施小明⁴,
宋海峰³

1.
北京理工大学材料学院, 北京　100081
2.
北京理工大学前沿交叉科学研究院, 北京　100081
3.
北京应用物理与计算数学研究所计算物理全国重点实验室, 北京　100094
4.
北京科技大学数理学院, 北京　100083

基金项目: 国家科技部重点研发计划（2021YFB3501503）；国家自然科学基金（U2230401）；计算物理全国重点实验室基金

详细信息

作者简介:
许　可（1996－），男，博士研究生，主要从事镁合金动态加载的相场模拟研究. E-mail：xukebit@qq.com

通讯作者:
刘　瑜（1985－），男，博士，副研究员，博士生导师，主要从事高压物理、凝聚态物理、材料物理相关的理论研究. E-mail：liu_yu@iapcm.ac.cn

中图分类号: O521.2; O347.3
计量
- 文章访问数: 237
- HTML全文浏览量: 129
- PDF下载量: 32
出版历程
- 收稿日期: 2023-11-07
- 修回日期: 2024-01-19
- 网络出版日期: 2024-04-03
- 刊出日期: 2024-06-03

Insight into Dynamic Recrystallization of AZ31B Magnesium Alloys by Phase-Field Simulations

XU Ke^{1, 2, 3
,},
SHENG Jie³,
LIU Yu^{3,*
, ,},
HUANG Houbing²,
SHI Xiaoming⁴,
SONG Haifeng³

1.
School of Materials Science and Engineering, Beijing Institute of Technology, Beijing 100081, China
2.
Advanced Research Institute of Multidisciplinary Sciences, Beijing Institute of Technology, Beijing 100081, China
3.
Laboratory of Computational Physics, Institute of Applied Physics and Computational Mathematics, Beijing 100094, China
4.
School of Mathematics and Physics, University of Science and Technology Beijing, Beijing 100083, China

摘要

摘要: 镁合金被广泛应用于材料科学、航空航天及军事装备等领域。实验发现，镁合金材料在动态加载下的力学响应与介观尺度不连续动态再结晶紧密相关。为此，构建了镁合金动态再结晶的相场模型，以AZ31B镁合金为研究对象，模拟了不同温度（250～400 ℃）、低应变率（0.01～1.00 s⁻¹）加载下的不连续动态再结晶演化过程。再结晶相场模型耦合了塑性应变，实现了应力-应变曲线与再结晶组织演化的迭代求解。模拟发现，再结晶晶粒的体积分数和平均晶粒尺寸随温度的升高而明显增大，随应变率的增大而减小。
- 相场模拟 /
- 镁合金 /
- 动态再结晶 /
- 力学响应
Abstract: Magnesium is widely used for materials science, aerospace, and military equipment. It is found that the mechanical property of magnesium under deformation loading is closely related to discontinuous dynamic recrystallization. In this work, we construct a dynamic recrystallization phenomenological model of magnesium alloy via phase-field methods. We choose AZ31B magnesium alloy as the research object and simulate grains and grain boundaries evolutions during dynamic recrystallization under 0.01–1.00 s⁻¹ and 250–400 ℃. Iterative solving methods of stress-strain curves and recrystallization evolutions are improved by introducing plastic deformation energy to phase-field model. The simulation results show the volume fraction of recrystallization grains and the average grain size of samples increase with the rise of temperature and decrease of strain rates.
- phase-field simulations /
- magnesium alloy /
- dynamic recrystallization /
- mechanical response

HTML全文

具有钙钛矿结构的稀土-3d过渡金属氧化物RMO₃（R为稀土，M为3d过渡金属）因表现出诸如多铁性^[1–3]、高温超导^[4]、巨磁阻效应^[5]等奇异的物性而一直备受关注。从晶体结构来看，3d过渡金属阳离子M与氧离子形成共角连接的MO₆八面体，稀土阳离子R位于MO₆八面体的空隙中间。这种结构不仅可以容纳多种不同离子半径的稀土和过渡金属阳离子，造成MO₆八面体的扭转和倾斜，而且还允许氧离子空位存在有序或无序排列。从电子结构来看，随着过渡金属阳离子3d价电子和稀土阳离子4f价电子的排布变化，考虑到电子间的强关联库仑相互作用，系统的轨道序和磁基态将发生显著改变。因此，稀土-3d过渡金属钙钛矿中存在结构、电荷、轨道和自旋多个量子自由度之间的相互耦合和竞争，为研究结构与物性的构效关系提供了绝佳平台。

在钙钛矿结构中，用几何结构容忍因子 $t\equiv d_{\mathrm{R}-\mathrm{O}}\big/\left(\sqrt{2}d_{\mathrm{M}-\mathrm{O}}\right)$ 描述结构的晶格畸变，其中 $d_{\mathrm{R}-\mathrm{O}}$ 和 $d_{\mathrm{M}-\mathrm{O}}$ 分别表示稀土阳离子和过渡金属阳离子与配位氧离子之间的键长。实验发现，稀土-3d过渡金属氧化物RMO₃的钙钛矿结构通常在 $1 - \delta \leqslant t \leqslant 1$ 时保持稳定^[6]。在高压作用下，体系将倾向于对称性更高的结构，从而减小晶格体积、增大物质密度。一方面，对于 $t < 1 - \delta$ 的低对称非钙钛矿结构，其八面体在高压下扭转或畸变减弱，将导致晶格对称性提高，进而转变为钙钛矿结构；另一方面，对于 ${t} > 1$ 的类钙钛矿共面变形体，由于在压力作用下R―O键比M―O键更易压缩，使得 $t$ 因子在高压下逐渐减小并趋近于1，最终成为钙钛矿结构。因此，高压可极大拓宽钙钛矿结构稳定存在的范围，在合成新型钙钛矿材料方面具有独特优势。

然而，过去关于稀土-3d过渡金属钙钛矿RMO₃的研究主要集中在过渡金属钒基^[7–9]、铬基^[10–12]、锰基^{[3, 13–14]}、铁基^[15–17]、钴基^[18–20]和镍基^[21–23]体系，对铜基稀土钙钛矿RCuO₃的探索非常缺乏。其中一个主要原因是，含有反常高价态Cu³⁺的钙钛矿RCuO₃需要在超高氧压下合成，使得该体系的样品制备异常困难。虽然LaCuO₃可在5.0 GPa高压下合成^[24]且已被广泛研究，但是随着稀土离子R半径的进一步减小，RCuO₃钙钛矿结构的几何容忍因子t变得更小，因此需要更高压力条件才能合成。Zhou等^[25]在1600 ℃、6.5 GPa的高温高压条件下合成了一系列La_1–xNd_xCuO₃（0≤x≤0.6）固溶体，并系统研究了该体系的结构和物性演化规律，其中LaCuO₃表现出金属性和增强的泡利顺磁性。Chen等^[26]在15.0 GPa高压下合成出正交结构的钙钛矿NdCuO₃样品，样品呈现绝缘体行为，但尚未系统研究其物性。以上结果表明，随着Nd³⁺的掺杂浓度提高，La_1–xNd_xCuO₃（0.7≤x≤1）需要更高的合成压力，同时由于其σ^*带逐渐变窄，将成为Cu³⁺单价钙钛矿体系中研究电子从巡游向局域渡越的关键材料。

为此，本研究将利用自主设计的高压组件，在Walker型二级推进压机上探索在最佳压力和温度条件下合成新型铜基稀土钙钛矿La_1–xNd_xCuO₃（0≤x≤1）样品，并通过精修X射线衍射谱图获得详细的结构相图，为进一步研究压力对其晶格结构和电子结构的调控规律提供实验依据。

1. 实验技术

1.1 前驱体制备

将La₂O₃、Nd₂O₃ （Macklin公司，纯度99.9%）在900 ℃条件下预烧12 h，去除水分和附着气体；将预烧过的La₂O₃、Nd₂O₃和CuO粉末（Aladdin公司，纯度99.9%）按照La_1–xNd_xCuO₃（0≤x≤1）的化学计量比混合均匀，研磨30 min以上；将混合粉末放入坩埚中，在马弗炉上于1000 ℃烧结20 h，获得La_1–xNd_xCuO₃（0≤x≤0.4）样品的前驱体；将研磨均匀的原料放入球磨机，以55 Hz频率高速球磨12 h，获得La_1–xNd_xCuO₃（0.5≤x≤1）样品的前驱体。高能球磨可以制造纳米级微观结构，使原料具有更小的粒径和更窄的粒度分布，促进其在非常规条件下发生反应^[27–28]，从而降低制备高浓度掺杂Nd³⁺样品的反应压力和温度条件。

1.2 高压高温制备

如图1所示，本研究通过在高温下分解KClO₄产生氧气并封装在密闭金筒中提供高氧压环境^[29]，利用Walker型二级推进压机在高温高压条件下合成高质量的La_1–xNd_xCuO₃（0≤x≤1）样品。

图 1 (a) 高压合成组件侧面图；(b) 高压合成组件剖面图；(c)高压合成组件的校压曲线；(d) 高压合成组件在14 GPa下的标温曲线

Figure 1. (a) Side view of the high-pressure assembly; (b) sectional drawing of the high-pressure assembly; (c) pressure calibration of high-pressure assembly; (d) temperature calibration of high-pressure assembly under 14 GPa

下载: 全尺寸图片幻灯片

首先，自主设计加工了Walker型高压组件，通过建立组件尺寸、强度与压力的关系模型，优化其尺寸精度、材料强度和受力结构。通过在压机中对特定的压力标定材料加压，测量其电阻随外部油压的变化曲线^[30–34]，获得样品压强与外部油压的对应关系。每套组件由传压介质八面体（主要成分为氧化镁）、铬酸镧、氮化硼、铂筒、金箔、钼片和热电偶组成，其中热电偶放置在样品中心处，用来标定样品中心的反应温度。通过压力和温度校准，该高压组件可实现的最高压强和温度分别达到25 GPa和1300 ℃。

在此基础上，将样品的前驱体粉末冷压成圆柱体置于金箔筒中，并在样品两端装填近似等量的KClO₄粉末，KClO₄粉末与前驱体粉末的体积比约为1∶2，保证加热过程中释放过量的氧气与样品充分反应减少氧空位。合成La_1–xNd_xCuO₃（0≤x≤1）样品所需的优化压力和温度条件见表1。实验结果表明，随着Nd³⁺离子掺杂浓度的提高，La_1–xNd_xCuO₃（0.7≤x≤1）需要更高的合成压力。

表 1 La_1–xNd_xCuO₃ （0≤x≤1）样品合成的压力和温度优化条件

Table 1. Pressure and temperature conditions of synthesizing La_1–xNd_xCuO₃ (0≤x≤1)

Sample	Pressure/GPa	Temperature/℃	Time/min
LaCuO₃	6	1000	30
La_0.9Nd_0.1CuO₃	6	1000	30
La_0.8Nd_0.2CuO₃	6	1000	30
La_0.7Nd_0.3CuO₃	10	1000	30
La_0.6Nd_0.4CuO₃	10	1000	30
La_0.5Nd_0.5CuO₃	10	1000	30
La_0.4Nd_0.6CuO₃	10	1000	30
La_0.3Nd_0.7CuO₃	14	1000	30
La_0.2Nd_0.8CuO₃	14	1000	30
La_0.1Nd_0.9CuO₃	14	1000	30
NdCuO₃	14	1000	30

下载: 导出CSV

| 显示表格

1.3 样品表征与精修

将合成的样品研磨30 min，用去离子水清洗3遍以上去除KCl杂质，利用Bruker D8 Advance X射线粉末衍射仪（PXRD，X射线波长λ=1.54056 Å）在衍射角度为20°～100°、步长为0.02°条件下测量PXRD数据，通过Fullprof 软件对La_1–xNd_xCuO₃（0≤x≤1）的PXRD谱图进行Rietveld精修，获取晶体结构信息^[35]。

2. 实验结果和讨论

图2显示了LaCuO₃、La_0.5Nd_0.5CuO₃、La_0.2Nd_0.8CuO₃和NdCuO₃的PXRD数据精修结果，其他更多组分的La_1–xNd_xCuO₃（0≤x≤1）结构精修结果见表2，其中：R_P、R_WP、Chi2为精修品质因子。

图 2 (a) LaCuO₃、(b) La_0.5Nd_0.5CuO₃、(c) La_0.2Nd_0.8CuO₃和(d) NdCuO₃ 的PXRD Rietveld 精修谱图

Figure 2. Rietveld refinement of PXRD patterns of (a) LaCuO₃, (b) La_0.5Nd_0.5CuO₃, (c) La_0.2Nd_0.8CuO₃ and (d) NdCuO₃

下载: 全尺寸图片幻灯片

表 2 La_1–xNd_xCuO₃（0≤x≤1）的晶格参数

Table 2. Structural parameters of La_1–xNd_xCuO₃ (0≤x≤1)

Sample	Space group	Lattice parameters/Å	R_P/%	R_WP/%	Chi2
LaCuO₃	$R\overline 3 c$	a=b=5.4976(6), c=13.2062(9)	3.05	5.59	7.01
La_0.9Nd_0.1CuO₃	$R\overline 3 c$	a=b=5.4976(9), c=13.1917(5)	1.45	1.92	1.10
La_0.8Nd_0.2CuO₃	$R\overline 3 c$	a=b=5.4988(9), c=13.1732(7)	1.25	1.68	0.79
La_0.7Nd_0.3CuO₃	$R\overline 3 c$	a=b=5.4961(1), c=13.1625(7)	1.91	2.73	2.48
La_0.6Nd_0.4CuO₃	$R\overline 3 c$	a=5.4933(9), c=13.1326(6)	2.41	4.14	7.09
La_0.5Nd_0.5CuO₃	Phase 1: $R\overline 3 c$ (36.43%)	a=b=5.4627(1), c=13.2988(9)	4.23	5.85	2.42
La_0.5Nd_0.5CuO₃	Phase 2: Pnma (63.57%)	a=6.1821(1), b=7.3597(8), c=5.4318(7)	4.23	5.85	2.42
La_0.4Nd_0.6CuO₃	Phase 1: $R\overline 3 c$ (43.49%)	a=b=5.4571(7), c=13.2982(1)	1.25	1.68	0.79
La_0.4Nd_0.6CuO₃	Phase 2: Pnma (56.51%)	a=6.5015(2), b=7.6552(6), c=5.3354(4)	1.25	1.68	0.79
La_0.3Nd_0.7CuO₃	Phase 1: $R\overline 3 c$ (44.42%)	a=b=5.4542(6), c=13.3191(9)	3.76	4.81	1.43
La_0.3Nd_0.7CuO₃	Phase 2: Pnma (55.58%)	a=6.3189(6), b=7.2736(7), c=5.3706(8)	3.76	4.81	1.43
La_0.2Nd_0.8CuO₃	Pnma	a=6.3197(8), b=7.2408(1), c=5.3561(1)	7.75	9.92	2.20
La_0.1Nd_0.9CuO₃	Pnma	a=6.3045(3), b=7.2421(7), c=5.3462(9)	1.54	2.24	1.66
NdCuO₃	Pnma	a=6.3039(2), b=7.2176(2), c=5.3334(5)	1.72	2.48	1.42

下载: 导出CSV

| 显示表格

LaCuO₃具有空间群为 $R\overline 3 c$ 的菱方结构，而NdCuO₃具有空间群为Pnma的正交结构，与之前报道^{[24, 26]}一致。随着Nd³⁺掺杂浓度的增加，当x为0.5、0.6、0.7时，样品中存在 $R\overline 3 c$ 菱方结构与Pnma正交结构共存的情况。这一结果与之前Zhou等^[25]报道的La_1–xNd_xCuO₃（0≤x≤0.6）保持菱方结构的结论不同，考虑可能与样品合成的压力和温度条件有关。进一步增大固溶体中Nd³⁺的掺杂浓度，发现样品在x≥0.8时完全转变为Pnma正交结构，并具有较大的晶胞参数和晶格畸变。

基于以上结果，绘制了La_1–xNd_xCuO₃（0≤x≤1）体系随Nd³⁺掺杂浓度变化的结构相图，如图3所示。该体系是Cu³⁺的单价钙钛矿，包含一个半填充的σ^*窄带。LaCuO₃在低温下表现出金属行为^[36]。随着Nd³⁺掺杂增加，σ^*的带宽将逐渐变窄，因此可在该材料中系统研究巡游σ^*电子向局域e电子的渡越行为。与之类似的镍基RNiO₃氧化物体系中，随着稀土离子半径的减小，在PrNiO₃与NdNiO₃之间发生了从金属到反铁磁绝缘体的一级相变，Ni―O键长和Ni―O―Ni键角的变化与巡游σ^*电子向局域e电子的渡越密切相关^[37]。之前的报道并未在La_1–xNd_xCuO₃（0≤x≤0.6）样品中发现金属-绝缘体相变^[25]。由于NdCuO₃表现出绝缘体行为^[26]，后续可在具有更高Nd³⁺掺杂浓度的La_1–xNd_xCuO₃ （0.7≤x≤1）样品中探索电子临界行为和磁性转变。

图 3 La_1–xNd_xCuO₃（0≤x≤1）的结构相图

Figure 3. Structural phase diagram of La_1–xNd_xCuO₃ (0≤x≤1)

下载: 全尺寸图片幻灯片

3. 结　论

通过自主设计加工的Walker型高压组件，实现了1300 ℃、25 GPa的高温高压合成条件。在此基础上，成功合成了La_1–xNd_xCuO₃（0≤x≤1）系列样品，并对其进行了详细的结构研究。实验结果表明：当x在0～0.4范围内时，样品具有 $R\overline 3 c$ 菱方结构的单相；当x为0.5、0.6、0.7时，样品具有 $R\overline 3 c$ 菱方结构与Pnma正交结构共存的混合相；而当x在0.8～1.0范围内时，样品具有Pnma正交结构的单相。该体系为深入研究Cu³⁺单价钙钛矿的结构和物性演化规律提供了材料基础。

图 1 初始多晶与再结晶晶粒序参量构造示意图^[25]

Figure 1. Schematic diagram of the order parameter configuration of initial polycrystalline and recrystallized grains^[25]

下载: 全尺寸图片幻灯片

图 2 动态再结晶本构模型构造示意图

Figure 2. Schematic diagram of the constitutive model of dynamic recrystallization

下载: 全尺寸图片幻灯片

图 3 AZ31B镁合金多晶在300 ℃、不同应变率动态加载下的微观组织（序参量η）演化

Figure 3. Microstructure (η) evolution of AZ31B magnesium alloy polycrystal under dynamic loading at a temperature of 300 °C and different strain rates

下载: 全尺寸图片幻灯片

图 4 AZ31B镁合金多晶在应变率为1.00 s⁻¹、不同温度动态加载下的微观组织（序参量η）演化

Figure 4. Microstructure (η) evolution of AZ31B magnesium alloy polycrystal under dynamic loading at a strain rate of 1.00 s⁻¹ and different temperatures

下载: 全尺寸图片幻灯片

图 5 动态再结晶体积分数与(a)温度和(b)应变率的关系以及再结晶平均晶粒尺寸随应变的演化与(c)温度和(d)应变率的关系

Figure 5. Recrystallization volume fraction of dynamic recrystallization versus (a) temperature and (b) strain rate, and the evolution of average grain size with strain versus (c) temperature and (d) strain rate

下载: 全尺寸图片幻灯片

图 6 动态再结晶关于形核率 $\dot{n}$ 与晶界迁移速率M_gb的平均晶粒尺寸相图（形核速率和晶界迁移速率均采用真实数值）

Figure 6. Phase diagram of the average grain size of dynamic recrystallization with respect to the nucleation rate ( $\dot{n}$ ) versus the grain boundary migration rate M_gb, where real values are used for both the nucleation rate and the grain boundary migration rate

下载: 全尺寸图片幻灯片

图 7 AZ31B镁合金在动态加载下的应力-应变曲线（实线为实验测量数据^[27]，样条为相场模拟结果）

Figure 7. Stress-strain curves of AZ31B magnesium alloy under dynamic loading (The solid lines represent the experimental data^[27], and the splines represent the phase field simulation results)

下载: 全尺寸图片幻灯片

表 1 AZ31B镁合金的相场模型参数^{[23, 26]}

Table 1. Model parameters for phase-field simulation of AZ31B magnesium alloy^{[23, 26]}

α	μ/GPa	b/m	Q_drx/(kJ·mol⁻¹)	Q_self/(kJ·mol⁻¹)
0.5	17.0	3.2×10⁻¹⁰	158.7	156.2

γ_gb/(J·m⁻²)	D_gb/(m²·s⁻¹)	q	k_B/(J·K⁻¹)	R/(J·mol⁻¹·K⁻¹)
0.55	3.2×10⁻⁸	0.634	1.38×10⁻¹²	8.314

下载: 导出CSV

表 2 AZ31B镁合金的相场模拟初始化参数^[23]

Table 2. Initialization parameters for phase-field simulation of AZ31B magnesium alloy^[23]

W_gb/μm	Δε	ε_end	N_g	T/℃	$\dot{\varepsilon }/{\mathrm{s}}$ ⁻¹
1.0	0.001	1.0	9	250−400	0.01−1.00

下载: 导出CSV

表 3 相场模拟使用的力学本构参数^[26–27]

Table 3. Constitutive parameters used for phase-field simulations^[26–27]

T/℃	$\dot{\varepsilon }/{\mathrm{s}}$ ⁻¹	σ_sat/MPa	σ_ss/MPa	Ω	ε_crit
250	1.00	187	130	26.35	0.320
300	0.01	87	59	42.31	0.093
300	0.10	117	75	31.97	0.112
300	1.00	155	77	28.07	0.180
350	1.00	116	65	30.44	0.110
400	1.00	86	61	39.65	0.200

下载: 导出CSV

参考文献(38)

[1]	谭叶, 肖元陆, 薛桃, 等. 镁铝合金的冲击熔化行为实验研究 [J]. 高压物理学报, 2019, 33(2): 020106. doi: 10.11858/gywlxb.20190729 TAN Y, XIAO Y L, XUE T, et al. Melting of MB2 alloy under shock compression [J]. Chinese Journal of High Pressure Physics, 2019, 33(2): 020106. doi: 10.11858/gywlxb.20190729
[2]	李定远, 朱志武, 卢也森. 冲击加载下42CrMo钢的动态力学性能及其本构关系 [J]. 高压物理学报, 2017, 31(6): 761–768. doi: 10.11858/gywlxb.2017.06.011 LI D Y, ZHU Z W, LU Y S. Mechanical properties and constitutive relation for 42CrMo steel under impact load [J]. Chinese Journal of High Pressure Physics, 2017, 31(6): 761–768. doi: 10.11858/gywlxb.2017.06.011
[3]	潘建华, 陈学东, 姜恒, 等. 准静态和动态加载对裂纹扩展阻力曲线的影响及其关系的研究 [J]. 高压物理学报, 2015, 29(2): 109–116. doi: 10.11858/gywlxb.2015.02.004 PAN J H, CHEN X D, JIANG H, et al. Loading rate effect on crack resistance curves and their correlations [J]. Chinese Journal of High Pressure Physics, 2015, 29(2): 109–116. doi: 10.11858/gywlxb.2015.02.004
[4]	MALIK A, WANG Y W, CHENG H W, et al. Post deformation analysis of the ballistic impacted magnesium alloys, a short-review [J]. Journal of Magnesium and Alloys, 2021, 9(5): 1505–1520. doi: 10.1016/j.jma.2020.07.011
[5]	MEDVEDEV A E, MACONACHIE T, LEARY M, et al. Perspectives on additive manufacturing for dynamic impact applications [J]. Materials & Design, 2022, 221: 110963. doi: 10.1016/j.matdes.2022.110963
[6]	NAZEER F, LONG J Y, YANG Z, et al. Superplastic deformation behavior of Mg alloys: a-review [J]. Journal of Magnesium and Alloys, 2022, 10(1): 97–109. doi: 10.1016/j.jma.2021.07.012
[7]	XU W L, YU J M, JIA L C, et al. Deformation behavior of Mg-13Gd-4Y-2Zn-0.5Zr alloy on the basis of LPSO kinking, dynamic recrystallization and twinning during compression-torsion [J]. Materials Characterization, 2021, 178: 111215. doi: 10.1016/j.matchar.2021.111215
[8]	MALIK A, NAZEER F, NAQVI S Z H, et al. Microstructure feathers and ASB susceptibility under dynamic compression and its correlation with the ballistic impact of Mg alloys [J]. Journal of Materials Research and Technology, 2022, 16: 801–813. doi: 10.1016/j.jmrt.2021.12.051
[9]	MALIK A, WANG Y W. A short review on high strain rate superplasticity in magnesium-based composites materials [J]. International Journal of Lightweight Materials and Manufacture, 2023, 6(2): 214–224. doi: 10.1016/j.ijlmm.2022.10.004
[10]	HE M F, CHEN L X, YIN M, et al. Review on magnesium and magnesium-based alloys as biomaterials for bone immobilization [J]. Journal of Materials Research and Technology, 2023, 23: 4396–4419. doi: 10.1016/j.jmrt.2023.02.037
[11]	DONG J H, LIN T, SHAO H P, et al. Advances in degradation behavior of biomedical magnesium alloys: a review [J]. Journal of Alloys and Compounds, 2022, 908: 164600. doi: 10.1016/j.jallcom.2022.164600
[12]	苏磊, 杨国强. 动态压力加载/卸载装置dDAC及原位表征技术研究进展 [J]. 高压物理学报, 2021, 35(6): 060102. doi: 10.11858/gywlxb.20210505 SU L, YANG G Q. Research progress of dynamic pressure loading/unloading device and in-situ characterization technology [J]. Chinese Journal of High Pressure Physics, 2021, 35(6): 060102. doi: 10.11858/gywlxb.20210505
[13]	GOETZ R L, SEETHARAMAN V. Modeling dynamic recrystallization using cellular automata [J]. Scripta Materialia, 1998, 38(3): 405–413. doi: 10.1016/S1359-6462(97)00500-9
[14]	JONAS J J, QUELENNEC X, JIANG L, et al. The Avrami kinetics of dynamic recrystallization [J]. Acta Materialia, 2009, 57(9): 2748–2756. doi: 10.1016/j.actamat.2009.02.033
[15]	KUBIN L P, CANOVA G, CONDAT M, et al. Dislocation microstructures and plastic flow: a 3D simulation [J]. Solid State Phenomena, 1992, 23/24: 455–472. doi: 10.4028/www.scientific.net/SSP.23-24.455
[16]	MA A, ROTERS F. A constitutive model for fcc single crystals based on dislocation densities and its application to uniaxial compression of aluminium single crystals [J]. Acta Materialia, 2004, 52(12): 3603–3612. doi: 10.1016/j.actamat.2004.04.012
[17]	MA A, ROTERS F, RAABE D. A dislocation density based constitutive model for crystal plasticity FEM including geometrically necessary dislocations [J]. Acta Materialia, 2006, 54(8): 2169–2179. doi: 10.1016/j.actamat.2006.01.005
[18]	PÉREZ-PRADO M T, DEL VALLE J A, CONTRERAS J M, et al. Microstructural evolution during large strain hot rolling of an AM60 Mg alloy [J]. Scripta Materialia, 2004, 50(5): 661–665. doi: 10.1016/j.scriptamat.2003.11.014
[19]	SAKAI T, BELYAKOV A, KAIBYSHEV R, et al. Dynamic and post-dynamic recrystallization under hot, cold and severe plastic deformation conditions [J]. Progress in Materials Science, 2014, 60: 130–207. doi: 10.1016/j.pmatsci.2013.09.002
[20]	CHEN L Q, YANG W. Computer simulation of the domain dynamics of a quenched system with a large number of nonconserved order parameters: the grain-growth kinetics [J]. Physical Review B, 1994, 50(21): 15752–15756. doi: 10.1103/PhysRevB.50.15752
[21]	MOELANS N, GODFREY A, ZHANG Y B, et al. Phase-field simulation study of the migration of recrystallization boundaries [J]. Physical Review B, 2013, 88(5): 054103. doi: 10.1103/PhysRevB.88.054103
[22]	ZHAO P Y, SONG EN LOW T, WANG Y Z, et al. An integrated full-field model of concurrent plastic deformation and microstructure evolution: application to 3D simulation of dynamic recrystallization in polycrystalline copper [J]. International Journal of Plasticity, 2016, 80: 38–55. doi: 10.1016/j.ijplas.2015.12.010
[23]	CAI Y, SUN C Y, LI Y L, et al. Phase field modeling of discontinuous dynamic recrystallization in hot deformation of magnesium alloys [J]. International Journal of Plasticity, 2020, 133: 102773. doi: 10.1016/j.ijplas.2020.102773
[24]	姚松林, 裴晓阳, 于继东, 等. 基于位错动力学方法的动态塑性变形研究 [J]. 高压物理学报, 2019, 33(3): 030107. doi: 10.11858/gywlxb.20190727 YAO S L, PEI X Y, YU J D, et al. Overview of the study of dynamical plastic deformation based on dislocation dynamics method [J]. Chinese Journal of High Pressure Physics, 2019, 33(3): 030107. doi: 10.11858/gywlxb.20190727
[25]	许可. 相场模拟多物理场调控镁合金不连续动态再结晶 [D]. 北京: 北京理工大学, 2023. XU K. Multi-physics-field manipulating discontinuous dynamic recrystallization in magnesium alloys via phase-field simulations [D]. Beijing: Beijing Institute of Technology, 2023.
[26]	CHEN M S, YUAN W Q, LI H B, et al. Modeling and simulation of dynamic recrystallization behaviors of magnesium alloy AZ31B using cellular automaton method [J]. Computational Materials Science, 2017, 136: 163–172. doi: 10.1016/j.commatsci.2017.05.009
[27]	LIU J, CUI Z, RUAN L. A new kinetics model of dynamic recrystallization for magnesium alloy AZ31B [J]. Materials Science and Engineering: A, 2011, 529: 300–310. doi: 10.1016/j.msea.2011.09.032
[28]	LI Y, HOU P J, WU Z G, et al. Dynamic recrystallization of a wrought magnesium alloy: grain size and texture maps and their application for mechanical behavior predictions [J]. Materials & Design, 2021, 202: 109562. doi: 10.1016/j.matdes.2021.109562
[29]	CHEN S F, LI D Y, ZHANG S H, et al. Modelling continuous dynamic recrystallization of aluminum alloys based on the polycrystal plasticity approach [J]. International Journal of Plasticity, 2020, 131: 102710. doi: 10.1016/j.ijplas.2020.102710
[30]	HUANG W Y, CHEN J H, ZHANG R Z, et al. Effect of deformation modes on continuous dynamic recrystallization of extruded AZ31 Mg alloy [J]. Journal of Alloys and Compounds, 2022, 897: 163086. doi: 10.1016/j.jallcom.2021.163086
[31]	LEONARD M, MOUSSA C, ROATTA A, et al. Continuous dynamic recrystallization in a Zn-Cu-Ti sheet subjected to bilinear tensile strain [J]. Materials Science and Engineering: A, 2020, 789: 139689. doi: 10.1016/j.msea.2020.139689
[32]	LIU L, WU Y X, AHMAD A S. A novel simulation of continuous dynamic recrystallization process for 2219 aluminium alloy using cellular automata technique [J]. Materials Science and Engineering: A, 2021, 815: 141256. doi: 10.1016/j.msea.2021.141256
[33]	ZHANG J J, YI Y P, HE H L, et al. Kinetic model for describing continuous and discontinuous dynamic recrystallization behaviors of 2195 aluminum alloy during hot deformation [J]. Materials Characterization, 2021, 181: 111492. doi: 10.1016/j.matchar.2021.111492
[34]	GUO P C, LIU X, ZHU B W, et al. The microstructure evolution and deformation mechanism in a casting AM80 magnesium alloy under ultra-high strain rate loading [J]. Journal of Magnesium and Alloys, 2022, 10(11): 3205–3216. doi: 10.1016/j.jma.2021.07.032
[35]	LI N L, HUANG G J, ZHONG X Y, et al. Deformation mechanisms and dynamic recrystallization of AZ31 Mg alloy with different initial textures during hot tension [J]. Materials & Design, 2013, 50: 382–391. doi: 10.1016/j.matdes.2013.03.028
[36]	POPOVA E, BRAHME A P, STARASELSKI Y, et al. Effect of extension ${ {\text{\{10}}\overline {\text{1}} {\text{2\} }}}$ twins on texture evolution at elevated temperature deformation accompanied by dynamic recrystallization [J]. Materials & Design, 2016, 96: 446–457. doi: 10.1016/j.matdes.2016.02.042
[37]	XIE C, HE J M, ZHU B W, et al. Transition of dynamic recrystallization mechanisms of as-cast AZ31 Mg alloys during hot compression [J]. International Journal of Plasticity, 2018, 111: 211–233. doi: 10.1016/j.ijplas.2018.07.017
[38]	XU S W, KAMADO S, MATSUMOTO N, et al. Recrystallization mechanism of as-cast AZ91 magnesium alloy during hot compressive deformation [J]. Materials Science and Engineering: A, 2009, 527(1/2): 52–60. doi: 10.1016/j.msea.2009.08.062