电弧熔丝增材制造<strong>Mg/Mg</strong>双金属的组织与力学性能

doi:10.11900/0412.1961.2023.00493

金属学报

2025, Vol. 61

Issue (2): 211-225 DOI: 10.11900/0412.1961.2023.00493

研究论文

本期目录 | 过刊浏览

电弧熔丝增材制造Mg/Mg双金属的组织与力学性能

韩启飞, 狄兴隆, 郭跃岭(

), 叶水俊, 郑元翾, 刘长猛

北京理工大学机械与车辆学院北京 100081

Microstructure and Mechanical Properties of Mg/Mg Bimetals Fabricated by Wire Arc Additive Manufacturing

HAN Qifei, DI Xinglong, GUO Yueling(

), YE Shuijun, ZHENG Yuanxuan, LIU Changmeng

School of Mechanical Engineering, Beijing Institute of Technology, Beijing 100081, China

引用本文:

韩启飞, 狄兴隆, 郭跃岭, 叶水俊, 郑元翾, 刘长猛. 电弧熔丝增材制造Mg/Mg双金属的组织与力学性能[J]. 金属学报, 2025, 61(2): 211-225.
Qifei HAN, Xinglong DI, Yueling GUO, Shuijun YE, Yuanxuan ZHENG, Changmeng LIU. Microstructure and Mechanical Properties of Mg/Mg Bimetals Fabricated by Wire Arc Additive Manufacturing[J]. Acta Metall Sin, 2025, 61(2): 211-225.

全文: PDF(4822 KB) HTML

摘要:

传统工艺制备Mg/Mg双金属件流程复杂、成形效率低，电弧熔丝增材制造(WAAM)在提高大尺寸双金属件成形效率方面具有技术优势。为提高大尺寸Mg/Mg双金属件的成形效率和界面性能，本工作采用WAAM技术制备了Mg-Al-Si/Mg-Gd-Y-Zn双金属薄壁，研究了双金属件的宏观形貌、微观组织、显微硬度和力学性能。结果表明，该双金属件通过WAAM实现了良好的界面结合，双金属的界面为厚度约1.4 mm的过渡区。EPMA结果表明，过渡区内形成了成分梯度，从Mg-Al-Si合金侧到Mg-Gd-Y-Zn合金侧，Al和Si元素的含量逐渐降低，而Gd、Y和Zn元素的含量逐步增加。根据非平衡凝固相图和微观组织分析，双金属件由3个区域组成，分别是存在汉字状Mg₂Si相的Mg-Al-Si区，具有粒状Mg₂Si相、Mg₃(Gd, Y)相及Mg₅(Gd, Y)相的过渡区和以Mg₁₂Zn(Gd, Y)相为主的Mg-Gd-Y-Zn合金区。自Mg-Al-Si侧向Mg-Gd-Y-Zn侧，过渡区内的显微硬度从57 HV_0.5连续增加到90 HV_0.5。室温拉伸结果表明，双金属的强度接近Mg-Al-Si合金，极限抗拉强度和屈服强度分别为236.8和102.2 MPa，延伸率和加工硬化指数接近Mg-Gd-Y-Zn合金，分别为11.0%和0.323。WAAM Mg-Al-Si/Mg-Gd-Y-Zn双金属件的断裂位置位于过渡区，Mg-Al-Si合金的断裂机制以韧性断裂为主，而双金属和Mg-Gd-Y-Zn合金的断裂机理均为准解理断裂。

关键词 ：电弧熔丝增材制造, 双金属件, 组织, 强化机理

Abstract：

Mg/Mg bimetallic components, especially Mg-Al-Si/Mg-Gd-Y-Zn bimetals, hold promise for applications in the aerospace and automotive industries as structural materials because of their potential advantages of low cost, lightweight, high strength, and high plasticity. At present, Mg/Mg bimetallic components are primarily fabricated via extrusion and compound casting. However, these conventional processes are complex and have low forming efficiency. Recently, rapid advancements in additive manufacturing have enabled the real-time manufacturing of bimetallic structural components. In particular, wire arc additive manufacturing (WAAM) offers technical advantages for improving the forming efficiency of large-sized bimetallic components. Herein, to enhance the forming efficiency and interfacial performance of large-sized Mg/Mg bimetallic components, a thin-walled Mg-Al-Si/Mg-Gd-Y-Zn bimetallic component was fabricated using WAAM technology. Specifically, a Mg-Al-Si alloy thin wall was first deposited and then cooled to room temperature over a period of time. Subsequently, the top layer of the Mg-Al-Si alloy thin wall was remelted, followed by the deposition of the Mg-Gd-Y-Zn alloy. Further, the macroscopic morphology, microstructure, microhardness, and mechanical properties of the bimetallic component were examined. Based on the macroscopic morphology, bimetallic components exhibited good interface bonding through WAAM. OM images demonstrated a transition zone near the bimetallic interface with a thickness of approximately 1.4 mm. The line scanning results and EPMA mappings revealed the formation of a composition gradient in the transition zone due to element diffusion. From the Mg-Al-Si alloy side to the Mg-Gd-Y-Zn alloy side, the Al and Si contents gradually decreased, while the Gd, Y, and Zn contents gradually increased. Based on the nonequilibrium solidification phase diagram and microstructure analysis, the bimetallic component comprised three regions: the Mg-Al-Si region with the Chinese-script Mg₂Si phase; transition region comprising granular Mg₂Si, the Mg₃(Gd, Y) phase, and the Mg₅(Gd, Y) phase; and Mg-Gd-Y-Zn alloy region with the Mg₁₂Zn(Gd, Y) phase as the primary component. After microhardness testing, the hardness of the bimetallic component continuously increased from 57 HV_0.5 (Mg-Al-Si alloy side) to 90 HV_0.5 (Mg-Gd-Y-Zn alloy side) due to the composition gradient and small second phases in the transition zone. The results of tensile testing at room temperature (20 ^oC) showed that the strength of the bimetallic component was close to that of the Mg-Al-Si alloy, with an ultimate tensile strength of 236.8 MPa and a yield strength of 102.2 MPa. Meanwhile, the elongation and hardening index of the bimetallic component were close to those of the Mg-Gd-Y-Zn alloy, reaching 11.0% and 0.323, respectively. The fracture position of the WAAM Mg-Al-Si/Mg-Gd-Y-Zn bimetal was located in the transition zone. The fracture mechanism of the Mg-Al-Si alloy was primarily ductile, while those of the bimetal and Mg-Gd-Y-Zn alloy were quasi-cleavage.

Key words： wire arc additive manufacturing bimetallic component microstructure strengthening mechanism

收稿日期: 2023-12-21

ZTFLH:

TG444

基金资助:国防基础科研计划项目(JCKY2023602B012)

通讯作者: 郭跃岭，y.guo@bit.edu.cn，主要从事金属增材制造与非平衡凝固研究

Corresponding author: GUO Yueling, professor, Tel: (010)68915097, E-mail: y.guo@bit.edu.cn

作者简介: 韩启飞，男，1997年生，博士生

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表1 Mg-Al-Si 和Mg-Gd-Y-Zn合金丝材的化学成分 (mass fraction / %)

图1 Mg-Al-Si/Mg-Gd-Y-Zn双金属薄壁件电弧熔丝增材制造(WAAM)过程示意图

图2 WAAM Mg-Al-Si/Mg-Gd-Y-Zn双金属薄壁件的模型、材料表征和力学性能测试的取样位置及力学性能测试试样尺寸示意图

Alloy

$I p$

$t p$

$I p$ / $I b$

$V s$

mm·min^-1

$V w$

cm·min^-1

$V a$

L·min^-1

$U a$

Mg-Al-Si

122

1.5

150

1.3

Remelting Mg-Al-Si

150

1.5

150

090

1.3

Mg-Gd-Y-Zn

122

1.5

150

090

1.3

表2 Mg-Al-Si/Mg-Gd-Y-Zn双金属WAAM工艺参数

图3 WAAM Mg-Al-Si/Mg-Gd-Y-Zn双金属的宏观形貌、界面附近的OM像及显微硬度

图4 WAAM Mg-Al-Si/Mg-Gd-Y-Zn双金属过渡区的背散射电子(BSE)像及EPMA结果

图5 Mg-Al-Si和Mg-Gd-Y-Zn合金的非平衡凝固相图

图6 WAAM Mg-Al-Si/Mg-Gd-Y-Zn双金属界面区的BSE和SE像

表3 图6中各点的化学成分 (atomic fraction / %)

图7 3组拉伸试样的室温(20 ℃)真应力-真应变曲线、力学性能统计图及应力-应变双对数拟合曲线

图8 3组拉伸试样断裂后的形貌、断口形貌及断口纵截面显微组织

图9 WAAM Mg-Al-Si/Mg-Gd-Y-Zn双金属过渡区内沉淀相的形成机理示意图

图10 WAAM Mg-Al-Si/Mg-Gd-Y-Zn双金属过渡区的形成机理示意图

图11 Mg-Al-Si和Mg-Gd-Y-Zn合金α-Mg基体中溶质分数与固相分数的关系曲线

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