Solution Behavior of Spray-Formed Hypereutectic AlSiCuMg Alloy

doi:10.11900/0412.1961.2021.00079

Acta Metall Sin

2022, Vol. 58

Issue (9): 1129-1140 DOI: 10.11900/0412.1961.2021.00079

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Solution Behavior of Spray-Formed Hypereutectic AlSiCuMg Alloy

FENG Di¹(

), ZHU Tian¹, ZANG Qianhao¹, LEE Yunsoo²^,³, FAN Xi⁴, ZHANG Hao⁴

^1.School of Materials Science and Engineering, Jiangsu University of Science and Technology, Zhenjiang 212003, China
^2.Metallic Materials Division, Korea Institute of Materials Science, Changwon 51508, Korea
^3.Department of Materials Science and Engineering, Inha University, Incheon 22212, Korea
^4.Jiangsu Haoran Spray Forming Alloy Co., Ltd., Zhenjiang 212009, China

Cite this article:

FENG Di, ZHU Tian, ZANG Qianhao, LEE Yunsoo, FAN Xi, ZHANG Hao. Solution Behavior of Spray-Formed Hypereutectic AlSiCuMg Alloy. Acta Metall Sin, 2022, 58(9): 1129-1140.

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Abstract

Al-Si multicomponent alloys are commonly used in automotive and aerospace fields owing to their excellent castability, good wear resistance, and low coefficient of thermal expansion. After adding Cu and Mg followed by appropriate heating, Al₂Cu, AlCuSiMg, or Mg₂Si phases precipitate in an α-Al matrix. Hypereutectic AlSiCuMg alloys have been used in wear-resistant products, such as engine cylinders, pistons, and air-conditioning rotors, owing to the hardening effect of Si particles and the solid solution strengthening and precipitation strengthening effects of Cu and Mg. The evolution behaviors of secondary phases and the grains of the spray-formed Al25Si4Cu1Mg (mass fraction, %) alloy were examined via OM, XRD, SEM + EBSD, TEM, hardness tests, and phase diagram calculations. The results showed that the hot extrusion microstructure of spray-formed hypereutectic AlSi alloys comprises equiaxed α-Al, proeutectic Si, eutectic Si, eutectic AlCuSiMg, a eutectic Al₂Cu phase, and a low volume fraction Fe-bearing phase at the micron level but without a lamellar morphology. α-Al contained both micro-nano and nano-sized Al₂Cu phases precipitates. Over the temperature range of 475-495^oC, the precipitated Al₂Cu phase and some of the eutectic Al₂Cu phase redissolved, and the residual Al₂Cu phase concentrated to a Fe-bearing phase and coarsened. The volume fraction and size of the AlCuSiMg phase increased. However, when solution-treated at less than 515^oC, the volume fraction of the AlCuSiMg phase began to decrease, and no overburning structure was observed. When the solution temperature exceeded 515^oC, the incipient melting of the nonequilibrium eutectic phase increased with increasing solution temperature. The main characteristics of the overburning structure were the network eutectic and grain boundary broadening. The hardness of the spray-formed Al25Si4Cu1Mg alloy was dependent on five factors: the solid solubility of solute atoms, the volume fraction of the residual second phase, the grain size of α-Al, the scale of the Si phase, and the incipient melting of the nonequilibrium eutectic phase.

Key words: spray forming hypereutectic alloy AlSiCuMg alloy solution incipient melting

Received: 25 February 2021

ZTFLH:

TG166.3

Fund: National Natural Science Foundation of China(51801082);Undergraduate Innovation and Entrepreneurship Training Program of Jiangsu Province(202010289019Z)

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

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https://www.ams.org.cn/EN/10.11900/0412.1961.2021.00079 OR https://www.ams.org.cn/EN/Y2022/V58/I9/1129

Fig.1 DSC curves of spray-formed Al25Si4Cu1Mg alloy after hot extrusion (a) and partial enlarged drawing of Fig.1a (b)

Fig.2 XRD spectra of Al25Si4Cu1Mg alloy

Fig.3 SEM images of spray-formed Al25Si4Cu1Mg alloy
(a-c) as-sprayed (Fig.3c is the detail of the box in Fig.3b) (d-f) as-extruded

Fig.4 OM images of microstructures of spray-formed Al25Si4Cu1Mg alloy treated by different solution temperatures (solution time is 2 h)
(a) 475^oC (b) 495^oC (c) 515^oC (d) 535^oC (e) 555^oC

Fig.5 SEM images of microstructures of spray-formed Al25Si4Cu1Mg alloy treated by different solution temperatures (solution time is 2 h)
(a) 495^oC (b) 515^oC (c, e) 535^oC (d, f) 555^oC

Fig.6 The hardness comparison between different solution treatments
(a) hardness of different solution temperatures (solution time is 2 h)
(b) hardness of different solution time (solution temperature is 515℃)

Fig.7 Local misoritations (a, c, e) and secondary electron images (b, d, f) of microstructures under different solution temperatures (The grain boundary colored by black indicate the misorientation larger than 15°. The grain boundary colored by red indicate the misorientation is in the range of 2°~15°. Solution time is 2 h)
(a, b) 475^oC (c, d) 515^oC (e, f) 535^oC

Fig.8 The vertical section of Al25Si4Cu1Mg phase diagram based on FactSage software (Normal to the cross sectional surface)

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