Research Progress and Future Prospect on New Low-Alloyed Bake-Hardenable Magnesium Alloys

doi:10.11900/0412.1961.2024.00370

Acta Metall Sin

2025, Vol. 61

Issue (3): 372-382 DOI: 10.11900/0412.1961.2024.00370

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Research Progress and Future Prospect on New Low-Alloyed Bake-Hardenable Magnesium Alloys

WANG Huiyuan¹^,²^,³(

), MENG Zhaoyuan¹^,³, JIA Hailong¹^,³, XU Xinyu⁴(

), HUA Zhenming²

1 Key Laboratory of Automobile Materials of Ministry of Education, School of Materials Science and Engineering, Jilin University, Changchun 130025, China
2 School of Materials Science and Engineering, Hebei University of Technology, Tianjin 300130, China
3 International Center of Future Science, Jilin University, Changchun 130012, China
4 Department of Mechanical Engineering, The University of Hong Kong, Hong Kong 999077, China

Cite this article:

WANG Huiyuan, MENG Zhaoyuan, JIA Hailong, XU Xinyu, HUA Zhenming. Research Progress and Future Prospect on New Low-Alloyed Bake-Hardenable Magnesium Alloys. Acta Metall Sin, 2025, 61(3): 372-382.

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Abstract

Magnesium alloys are widely used in aerospace, automotive, and rail transit industries as the lightest structural metallic materials. Minor alloying additions have proven to be effective in enhancing processability and ductility. Recent studies demonstrate that low-alloyed Mg-Zn-Ca(-Al) alloys exhibit exceptional room-temperature formability due to their weak texture after rolling and annealing. This advancement indicates that magnesium alloy sheets could potentially replace steel and aluminum alloy in body panel applications. However, achieving improved strength while maintaining formability remains a substantial challenge, limiting the broader adoption of low-alloyed magnesium alloys. Bake hardening (BH) treatment, a technique commonly employed for steel and Al body panels to enhance post-forming strength, has recently been shown to strengthen Mg-Zn-Ca(-Al) alloy sheets. BH treatment partially addresses the trade-off between formability and strength in low-alloyed magnesium alloys by utilizing the limited solid solution atoms. As the development of BH magnesium alloy sheets progresses, further improvements in properties or the design of new alloy compositions require a thorough understanding of the relationship between microstructure and mechanical properties and the underlying mechanisms. This review examines recent advancements in low-alloyed bake-hardenable magnesium alloys, focusing on three mechanisms: dislocation segregation, twin boundary segregation, and Guinier-Preston (GP) zone-induced bake hardening. Additionally, it provides a brief outlook on the future development trends aimed at expanding the application range of these materials. The insights presented here are expected to guide the design and optimization of BH magnesium alloys with enhanced performance and broader industrial applicability.

Key words: magnesium alloy low alloying bake-hardening solute segregation GP zone

Received: 04 November 2024

ZTFLH:

TG146.2

Fund: National Natural Science Foundation of China(52334010);National Natural Science Foundation of China(52271103)

Corresponding Authors: WANG Huiyuan, professor, Tel: (022)60201981, E-mail: wanghuiyuan@hebut.edu.cn;
XU Xinyu, Tel: (022)60201981, E-mail: xinyuxu@connect.hku.hk

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https://www.ams.org.cn/EN/10.11900/0412.1961.2024.00370 OR https://www.ams.org.cn/EN/Y2025/V61/I3/372

Fig.1 Correlative TEM-APT characterization of 2% pre-strained and bake-hardened (BH) AZMX1110 alloys^[15] (APT—atom probe tomography, insets in Figs.1a and d are the selected area electron diffraction (SAED) patterns)
(a) two-beam bright field-TEM (BF-TEM) image of 2% pre-strained sample obtained under the g =

01 1 ¯ 0

( g —diffraction vector)
(b) APT map obtained from the same tip shown in Fig.1a
(c) overlay of Fig.1b and the corresponding region in Fig.1a
(d) two-beam BF-TEM image of bake-hardened sample obtained under the g =

01 1 ¯ 1

(e) APT map obtained from the same tip shown in Fig.1d (a-d represents four dislocations)
(f) overlay of Fig.1e and the corresponding region in Fig.1d

Fig.2 Tensile engineering stress-strain curves of annealed, directly aged, pre-strained, and bake-hardened ZXTM1000 alloys (a) and tensile yield strength as function of elongation for various rolled and extruded Mg alloys (b)^[31]

Table 1 Mechanical properties of low-alloyed bake-hardening Mg alloys and bake-hardening steels/aluminum alloys^[31-36]

Fig.3 High-angle annular dark field-scanning transmission electron microscope (HAADF-STEM) images (a-e) and EDS results (f-h) of pre-strained ZXTM1000 alloy during in situ heating^[31] (White arrows in Figs.3a and e represent areas of EDS line scanning results in Fig.3h; red arrows in Fig.3e show the solute segregation at dislocations after in situ heating for 30 min)
(a) pre-strained (b) reaching at 175 ^oC (c) heating at 175 ^oC for 10 min (d) 175 ^oC for 20 min (e) 175 ^oC for 30 min
(f, g) EDS mappings of pre-strained (f) and after heating (g) samples
(h) EDS line scanning results of white arrows in Figs.3a and e

Fig.4 Periodic segregation of solutes in twinning boundaries (TBs)^[39]
(a, c) HAADF-STEM images showing {

10 1 ¯ 1

} TBs in Mg-0.2Zn alloys (atomic fraction, %) (a) and {

10 1 ¯ 2

} TBs in Mg-0.8Zn alloy (atomic fraction, %) (c)
(b, d) close-ups of Figs.4a and c, respectively
(e, f) schematic illustrations of Figs.3b and d, respectively (Blue (in the paper plane) or purples (out of the paper plane) balls represent atoms in the A layer, yellow (in the paper plane) or orange (out of the paper plane) balls represent atoms in the B layer)

Fig.5 TEM analyses of the bake-hardened Mg-2.0Zn-0.5Ca alloy^[32]
(a, e) BF-TEM images of twin boundary, taken from the [

4 2 ¯ 2 ¯ 3 ¯

] direction (a) and dislocations (e) (Insets are the corresponding SAED patterns at the white crosshair; M and T represent matrix and twinning, respectively)
(b, f) HAADF-STEM images of the white rectangle region in Fig.5a (b) and dislocations (f)
(c, d) EDS mappings of the white rectangle region in Fig.5b
(g) line EDS scanning result of the white line in Fig.5f

Fig.6 TEM and APT analyses and mechanical properties of the Mg-1.61Zn-0.57Mn-0.54Ca-0.46Al (ZMXA2110) alloy^[33]
(a) electron backscattered diffraction (EBSD) image of ZMXA2110 alloy under solution treatment at 450 ^oC for 10 min (Inset is the distribution of grain size. RD—rolling direction, TD—transverse direction)
(b) strain-stress curves of solution treated and bake-hardened ZMXA2110 alloy (Inset is the Erichsen cupping test result of the solution treated ZMXA2110 alloy. IE—index Erichsen)
(c) tensile yield strength and IE value of ZMXA2110 alloy and other Mg sheet alloys
(d-f) TEM (d) and high resolution TEM (HRTEM) (f) images and SAED (e) pattern of bake-hardened ZMXA2110 sample which were obtain along the [10

1 ¯

0]_Mg zone axis
(g-i) atom maps (g), APT map of Mg and iso-concentration surface of 1.0%Ca (atomic fraction) (in cyan) (h), and concentration proxigram histogram corresponding to the iso-concentration surface in Fig.6h (i)

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