Microstructure Evolution and Recrystallization Behavior During Hot Deformation of Spray Formed AlSiCuMg Alloy

doi:10.11900/0412.1961.2021.00329

Acta Metall Sin

2022, Vol. 58

Issue (7): 932-942 DOI: 10.11900/0412.1961.2021.00329

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Microstructure Evolution and Recrystallization Behavior During Hot Deformation of Spray Formed AlSiCuMg Alloy

WU Caihong¹, FENG Di¹(

), ZANG Qianhao¹, FAN Shichun¹, ZHANG Hao², LEE Yunsoo³

^1.School of Materials Science and Engineering, Jiangsu University of Science and Technology, Zhenjiang 212003, China
^2.Jiangsu Haoran Spray Forming Alloy Co., Ltd., Zhenjiang 212009, China
^3.Metallic Materials Division, Korea Institute of Materials Science, Changwon 51508, Korea

Cite this article:

WU Caihong, FENG Di, ZANG Qianhao, FAN Shichun, ZHANG Hao, LEE Yunsoo. Microstructure Evolution and Recrystallization Behavior During Hot Deformation of Spray Formed AlSiCuMg Alloy. Acta Metall Sin, 2022, 58(7): 932-942.

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Abstract

Wrought Al-Si alloy has partially replaced the traditional wear-resistant alloy for structural weight reduction owing to the excellent comprehensive properties, such as wear resistance, low coefficient of thermal expansion, and high specific strength. The deformation aluminum alloy based on Al-Si binary alloy is widely used in aerospace and automotive industries. The hot compression test, SEM, TEM, and EBSD technologies were used to investigate the microstructure evolution and dynamic recrystallization nucleation mechanism of spray formed Al25Si4Cu1Mg (mass fraction, %) alloy. The results show that the as-sprayed microstructure consists of equiaxed α-Al, coarse Si phase, AlSiCuMg phase, and Al₂Cu phase with different scales. Under 623-723 K and 0.001-5 s^-1, the fine Al₂Cu phases gradually dissolve with the increase in deformation temperature. During high strain rate (5 s^-1) compression, dislocation accumulation causes a high degree of stress concentration in front of the coarse and insoluble primary phases, resulting in the cracking of some brittle primary phases. Local cracks also appear at the interfaces between α-Al and primary phases. The α-Al phase undergoes complete dynamic recrystallization. The recrystallized grain size decreases with the increase and decrease in strain rate and deformation temperature, respectively. The residual dislocation and deformation substructure in the grain decrease with the increase in deformation temperature. The random texture demonstrates that the dynamic recrystallization mechanism of spray formed Al25Si4Cu1Mg alloy is “particle stimulated nucleation (PSN)”.

Key words: AlSiCuMg alloy spray forming hot compression particle stimulate nucleation dynamic recrystallization

Received: 12 August 2021

ZTFLH:

TG146.2

Fund: National Natural Science Foundation of China(51801082);Key Research and Development Program of Zhenjiang City(GY2021003);Key Research and Development Program of Zhenjiang City(GY2021020);Province Graduate Research and Innovation Projects in Jiangsu Province(202110289002Z);Postgraduate Research & Practice Innovation Program of Jiangsu(KYCX21_3453)

About author: FENG Di, associate professor, Tel: (0511)84401188, E-mail: difeng1984@just.edu.cn

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	Caihong WU
	Di FENG
	Qianhao ZANG
	Shichun FAN
	Hao ZHANG
	Yunsoo LEE

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https://www.ams.org.cn/EN/10.11900/0412.1961.2021.00329 OR https://www.ams.org.cn/EN/Y2022/V58/I7/932

Fig.1 Low (a) and high (b) magnified SEM images, the XRD spectrum (c), and the corresponding inverse pole figure (IPF) (d) of as-sprayed Al25Si4Cu1Mg (mass fraction, %) alloy

Table 1 EDS analysis results for second phases of as-sprayed Al25Si4Cu1Mg alloy in Figs.1a and b

Fig.2 True stress-true strain curves of as-sprayed Al25Si4Cu1Mg alloy deformation at 623 K, 673 K, and 723 K under strain rates of 0.001 s^-1 (a), 0.01 s^-1 (b), 0.05 s^-1 (c), 0.1 s^-1 (d), 1 s^-1 (e), and 5 s^-1 (f)

Fig.3 Low (a, c, e, g, i) and high (b, d, f, h, j) magnified SEM images of as-sprayed and as-deformed microstructures under typical conditions of Al25Si4Cu1Mg alloy (T_d—deformation temperature, $ε ˙$ —strain rate, DRX—dynamic recrystallization)
(a, b) as-sprayed state (c, d) T_d = 623 K,

ε ˙

= 5 s^-1 (e, f) T_d = 723 K,

ε ˙

= 5 s^-1 (g, h) T_d = 673 K,

ε ˙

= 0.05 s^-1 (i, j) T_d = 723 K,

ε ˙

= 0.001 s^-1

Fig.4 TEM images of Al25Si4Cu1Mg alloy under different hot compression conditions
(a, b) primary Si particles and deformed grains at T_d = 673 K,

ε ˙

= 0.05 s^-1 (a) and T_d = 623 K,

ε ˙

= 5 s^-1 (b)
(c) interaction between dislocations and nano-Si particles at T_d = 623 K and

ε ˙

= 5 s^-1

Fig.5 EBSD images of as-sprayed and deformed microstructures under different hot compressed conditions of Al25Si4Cu1Mg alloy (The grain boundaries colored by red indicate the misorientation in the range of 2°-15°. The grain boundaries colored by black indicate the misorientation > 15°)
(a) as-sprayed (b) T_d = 623 K,

ε ˙

= 5 s^-1 (c) T_d = 723 K,

ε ˙

= 5 s^-1
(d) T_d = 673 K,

ε ˙

= 0.05 s^-1 (e) T_d = 723 K,

ε ˙

= 0.001 s^-1

Fig.6 {111} pole figures of as-sprayed and hot deformed Al25Si4Cu1Mg alloy microstructure (extrude direction-normal direction section) under different deformation conditions
(a) as-sprayed state (b) T_d = 623 K,

ε ˙

= 5 s^-1 (c) T_d = 723 K,

ε ˙

= 5 s^-1
(d) T_d = 673 K,

ε ˙

= 0.05 s^-1 (e) T_d = 723 K,

ε ˙

= 0.001 s^-1

Fig.7 Schematics of hot deformation microstructure evolution of spray formed Al25Si4Cu1Mg alloy under different deformation conditions (Z—Zener-Hollomon parameter)

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