Effect of trace rare earth La on microstructure and properties of Al-7%Si-0.6%Fe alloy

Qi Zhong-Yi; Wang Bo; Jiang Hong-Xiang; Zhang Li-Li; He Jie

doi:10.7498/aps.73.20231939

Abstract

Al-Si alloys have been widely used in electronic information, communication, and other fields because of their high specific strength, excellent castability and good thermal conductivity. In recent years, with the rapid development of 5G communication technology, electronic communication equipment is gradually developing towards high integration and lightweight. The power of related equipment is higher and higher, which puts forward higher requirements for thermal conductivity and mechanical properties of materials.Si can improve the fluidity and strength of the Al-Si alloy, but a large amount of Si will aggravate the lattice distortion and increases amount of eutectic Si. This will reduce the plasticity of the alloy, increase the electron scattering and reduce the thermal conductivity. In order to improve the mechanical properties and thermal conductivity of Al-Si alloys, chemical inoculation is generally used. Sr is usually used as modifier and Al-B serves as grain refiner. However, the simultaneous addition of Sr and B into Al-Si alloy results in “poisoning” phenomenon, it becomes impossible to refine α-Al grains and modify eutectic Si simultaneously.In recent years, rare earth La has attracted more and more attention in improving the properties of aluminum alloys. However, previous studies mainly focused on the effects of La addition, consequently, the research on the effects of combined addition of La, Sr, B on the microstructure and properties of Al-7%Si-0.6%Fe alloy is lacking. In this work, solidification experiments are performed to investigate the effects of combined addition of La, Sr, B on the microstructure and properties of Al-7%Si-0.6%Fe alloy. The results show that the addition of trace rare earth La can effectively eliminate the poisoning effect of Sr and B, and enhance the modification effect of eutectic Si. Besides, the addition of La can promote the formation of α-Al heterogeneous nucleation substrate LaB₆ and La can be used as a surfactant to reduce the undercooling of α-Al nucleation, thus it refines α-Al grains. The thermal conductivity of the alloy is significantly improved when the addition of La ranges from 0.02% to 0.06%; with the further increase of La addition, LaAlSi intermetallic compounds are formed in the alloy, leading the thermal conductivity of the alloy to decrease.

Keywords:

Authors and contacts

1.
School of Materials Science and Engineering, Northeastern University, Shenyang 110819, China
2.
Shi-changxu Innovation Centre for Advanced Materials, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China

Corresponding author: Jiang Hong-Xiang, hxjiang@imr.ac.cn ; He Jie, jiehe@imr.ac.cn

Funds: Project supported by the Science and Technology Major Project of Guangxi Province, China (Grant No.AA23023032), the National Natural Science Foundation of China (Grant Nos. 52174380, 51974288), the Space Utilization System of China Manned Space Engineering (Grant No. KJZ-YY-NCL06), and the Science and Technology Project of Fujian Province, China (Grant Nos. 2021T3030, 2020T3037).

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References

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Cited By

图 1 不同Sr, B, La添加量的Al-7%Si-0.6%Fe合金中共晶硅的SEM图像　(a) 0; (b) 0.024% B; (c) 0.02% Sr; (d) 0.02% Sr和0.024% B; (e) 0.02% Sr, 0.024% B和0.02% La; (f) 0.02% Sr, 0.024% B和0.1% La

Figure 1. SEM images of eutectic Si in the Al-7%Si-0.6%Fe alloys with different Sr, B and La addition: (a) 0; (b) 0.024% B; (c) 0.02% Sr; (d) 0.02% Sr and 0.024% B; (e) 0.02% Sr, 0.024% B and 0.02% La; (f) 0.02% Sr, 0.024% B and 0.1% La.

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图 2 Al-7%Si-0.6%Fe-0.024%B-0.02%Sr合金的SEI和EDS元素分布　(a) SEI; (b) Al; (c) Si; (d) Sr; (e) Fe

Figure 2. SEI and EDS element distribution of Al-7%Si-0.6%Fe-0.024%B-0.02%Sr alloy: (a) SEI; (b) Al; (c) Si; (d) Sr; (e) Fe.

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图 4 Al-7%Si-0.6%Fe-0.024%B-0.02%Sr-0.1%La合金的SEI和EDS元素分布　(a) SEI; (b) Al; (c) Si; (d) Sr; (e) Fe; (f) La

Figure 4. SEI and EDS element distribution of Al-7%Si-0.6%Fe-0.024%B-0.02%Sr-0.1%La alloy: (a) SEI; (b) Al; (c) Si; (d) Sr; (e) Fe; (f) La.

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图 3 Al-7%Si-0.6%Fe-0.024%B-0.02%Sr-0.02%La合金的SEI和EDS元素分布　(a) SEI; (b) Al; (c) Si; (d) Sr; (e) Fe; (f) La

Figure 3. SEI and EDS element distribution of Al-7%Si-0.6%Fe-0.024%B-0.02%Sr-0.02%La alloy: (a) SEI; (b) Al; (c) Si; (d) Sr; (e) Fe; (f) La.

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图 5 添加0.1%La的Al-7%Si-0.6%Fe合金的反向散射电子图像(BEI)及EPMA元素面分布　(a) BEI; (b) Al; (c) Si; (d) Sr; (e) Fe; (f) La

Figure 5. Backscattered electron image (BEI) and EPMA mappings of the Al-7%Si-0.6%Fe alloy with 0.1%La addition: (a) BEI; (b) Al; (c) Si; (d) Sr; (e) Fe; (f) La.

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图 6 不同Sr, B, La添加量的Al-7%Si-0.6%Fe合金的OM图像　(a) 0; (b) 0.02% Sr; (c) 0.024% B; (d) 0.02% Sr和0.024% B; (e) 0.02% Sr, 0.024% B和0.02% La; (f) 0.02% Sr, 0.024% B和0.04% La; (g) 0.02% Sr, 0.024% B和0.06% La; (h) 0.02% Sr, 0.024% B和0.08% La; (i) 0.02% Sr, 0.024% B和0.10% La

Figure 6. OM images of Al-7%Si-0.6%Fe alloys with different Sr, B, La addition: (a) 0; (b) 0.02% Sr; (c) 0.024% B; (d) 0.02% Sr and 0.024% B; (e) 0.02% Sr, 0.024% B and 0.02% La; (f) 0.02% Sr, 0.024% B and 0.04% La; (g) 0.02% Sr, 0.024% B and 0.06% La; (h) 0.02% Sr, 0.024% B and 0.08% La; (i) 0.02% Sr, 0.024% B and 0.10% La.

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图 7 Al-7%Si-0.6%Fe合金平均晶粒尺寸随La添加量的变化

Figure 7. Average grain size of Al-7%Si-0.6%Fe alloys with different addition of La.

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图 8 不同La添加量的Al-7%Si-0.6%Fe合金的DTA冷却曲线

Figure 8. Differential thermal analysis (DTA) cooling curves for the Al-7%Si-0.6%Fe alloys with different addition of La.

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图 9 不同La添加量的Al-7%Si-0.6%Fe合金的热导率

Figure 9. Thermal conductivities of Al-7%Si-0.6%Fe alloys with different addition of La.

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图 10 不同La添加量的Al-7%Si-0.6%Fe合金的室温拉伸性能

Figure 10. Tensile properties of Al-7%Si-0.6%Fe alloys with different addition of La at room temperature.

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图 11 Al, SrB₆和LaB₆相的晶体结构示意图

Figure 11. Schematic diagram of crystal structure of Al, SrB₆ and LaB₆ phases.

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图 12 添加不同含量La时α-Al相在高角度区间的XRD图谱

Figure 12. XRD spectra of α-Al phase in an elevation-angle zone with different addition of La.

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图 13 添加La前后Al-7%Si-0.6%Fe-0.02Sr-0.024B合金的拉伸断口形貌　(a) 未添加La; (b) 添加0.02% La

Figure 13. Tensile fracture morphology of Al-7%Si-0.6%Fe alloys before and after addition of La: (a) Without La; (b) add 0.02% La.

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表 1 实验合金的化学成分(%)

Table 1. Chemical compositions of alloys (%).

Alloy	B	Sr	La	Si	Fe	Al
Untreated	0	0	0	7	0.6	余量
0.024%B	0.024	0	0	7	0.6	余量
0.02%Sr	0	0.02	0	7	0.6	余量
0.02%Sr+0.024%B	0.024	0.02	0	7	0.6	余量
0.02%La	0.024	0.02	0.02	7	0.6	余量
0.04%La	0.024	0.02	0.04	7	0.6	余量
0.06%La	0.024	0.02	0.06	7	0.6	余量
0.08%La	0.024	0.02	0.08	7	0.6	余量
0.10%La	0.024	0.02	0.10	7	0.6	余量

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表 2 Al-7%Si-0.6%Fe合金中α-Al、共晶Si的形核温度T_N和过冷度ΔT

Table 2. Change of the nucleation temperature and the nucleation undercooling for the α-Al and the eutectic Si with different La addition.

Alloy	T_N(α-Al)/K	ΔT(α-Al)/K	T_N(Si)/K	ΔT(Si)/K
Untreated	883.1	6	846.0	1.1
0.00%La	883.1	3	844.0	3.1
0.04%La	884.2	1.9	843.8	3.3
0.10%La	885.2	0.9	843.8	3.3

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表 3 不同组元间的混合焓变^[28]

Table 3. Enthalpy of mixing between various elements^[28].

Element	B-Sr	B-La	B-Ti	B-V	B-Cr
Enthalpy/ (kJ·mol^–1)	–18	–47	–58	–42	–31

DownLoad: CSV

表 4 Al与SrB₆, Al与LaB₆之间可能的密排和近似密排方向及其错配度

Table 4. Interatomic spacing misfit along possible matching directions between LaB₆ and Al matrix, SrB₆ and Al matrix.

[100]_Al/ [100]_SrB6	[100]_Al/ [110]_SrB6	[100]_Al/ [111]_SrB6	[110]_Al/ [100]_SrB6	[110]_Al/ [110]_SrB6	[110]_Al/ [111]_SrB6	[112]_Al/ [100]_SrB6	[112]_Al/ [110]_SrB6	[112]_Al/ [111]_SrB6
3.68%	46.63%	79.57%	26.69%	3.68%	26.98%	15.35%	19.72%	46.62%
[100]_Al/ [100]_LaB6	[100]_Al/ [110]_LaB6	[100]_Al/ [111]_LaB6	[110]_Al/ [100]_LaB6	[110]_Al/ [110]_LaB6	[110]_Al/ [111]_LaB6	[112]_Al/ [100]_LaB6	[112]_Al/ [110]_LaB6	[100]_Al/ [111]_LaB6
2.67%	45.20%	77.82%	27.40%	2.67%	25.74%	16.17%	18.55%	45.19%

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表 5 SrB₆与Al, LaB₆与Al之间可能的密排和近似密排面对及其错配度

Table 5. Interplanar spacing mismatch between close or nearly close packed planes in LaB₆ and Al matrix, SrB₆ and Al matrix.

(200)_Al/ (100)_SrB6	(200)_Al/ (110)_SrB6	(200)_Al/ (111)_SrB6	(220)_Al/ (100)_SrB6	(220)_Al/ (110)_SrB6	(220)_Al/ (111)_SrB6	(111)_Al/ (100)_SrB6	(111)_Al/ (110)_SrB6	(111)_Al/ (111)_SrB6
3.68%	26.70%	40.23%	46.63%	3.67%	15.47%	79.40%	26.84%	3.42%
(200)_Al/ (100)_LaB6	(200)_Al/ (110)_LaB6	(200)_Al/ (111)_LaB6	(220)_Al/ (100)_LaB6	(220)_Al/ (110)_LaB6	(220)_Al/ (111)_LaB6	(111)_Al/ (100)_LaB6	(111)_Al/ (110)_LaB6	(111)_Al/ (111)_LaB6
2.67%	27.41%	40.73%	45.20%	2.65%	16.17%	77.65%	26.60%	2.56%

DownLoad: CSV

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[12]	Timelli G, Caliari D, Rakhmonov J 2016 J. Mater. Sci. Technol. 32 515 Google Scholar
[13]	Birol Y 2012 Mater. Sci. Technol. 28 363 Google Scholar
[14]	Barrirero J, Engstler M, Ghafoor N 2014 J. Alloys Compd. 611 410 Google Scholar
[15]	Chen J K, Hung H Y, Wang C F, Tang N K 2017 Int. J. Heat Mass Transf. 105 189 Google Scholar
[16]	Li J H, Wang X D, Ludwig T H, Tsunekawa Y, Arnberg L, Jiang J Z 2015 Acta Mater. 84 153 Google Scholar
[17]	Jiang H X, Li S X, Zheng Q J, Zhang L L, He J, Song Y, Deng C K, Zhao J Z 2020 Mater. Des. 195 108991 Google Scholar
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[22]	Heo U, Han D W, Kim S, Mo C B 2022 Mater. Today Commun. 32 104005 Google Scholar
[23]	Bakhtiyarov S I, Overfelt R A, Teodorescu S G 2001 J. Mater. Sci. 36 4643 Google Scholar
[24]	Huang L, Gunther E, Doetsch C, Mehling H 2010 Thermochim. Acta 509 93 Google Scholar
[25]	Birol Y 2012 Mater. Sci. Technol. 28 70 Google Scholar
[26]	Cui X L, Wu Y Y, Gao T, Liu X F 2014 J. Alloys Compd. 615 906 Google Scholar
[27]	Lu T, Pan Y, Wu J L, Tao S W, Chen Y 2015 Int. J. Min. Met. Mater. 22 405 Google Scholar
[28]	Takeuchi A, Inoue A 2005 Mater. Trans. 46 2817 Google Scholar
[29]	Lu S Z, Hellawell A 1987 Metall. Trans. 18A 1721
[30]	Li C L, Pan Y, Lu T, Jing L J, Pi J H 2018 Met. Mater. Int. 24 1133 Google Scholar
[31]	Luo Q, Li X L, Li Q 2023 J. Mater. Sci. Technol. 135 97 Google Scholar
[32]	Zhang M X, Kelly P M 2005 Scr. Mater. 52 963 Google Scholar
[33]	Jing L J, Pan Y, Lu T, Pi J H, Gu T F 2018 T. Nonferr. Metal. Soc. 28 1687 Google Scholar
[34]	Easton M A, StJohn D H 2001 130th TMS Annual Meeting New Orleans, La, February 11–15, 2000 p927
[35]	Zhou S H, Napolitano R E 2006 Acta Mater. 54 831 Google Scholar
[36]	Zhang L L, Jiang H X, He J, Zhao J Z 2020 Scr. Mater. 179 99 Google Scholar
[37]	Li S B, Du W B, Wang X D 2018 Acta Metall. Sin. 54 911 Google Scholar
[38]	Hou J P, Wang Q, Zhang Z J, Tian Y Z, Wu X M, Yang H J, Li X W, Zhang Z F 2017 Mater. Des. 132 148 Google Scholar
[39]	Mayadas A F, Shatzkes M 1970 Phys.Rev.B. 1 1382 Google Scholar
[40]	Weng W P, Nagaumi H, Sheng X D, Fan W Z, Chen X C, Wang X N 2019 Light Metals Symposium at the 148th TMS Annual Meeting San Antonio, TX, March 10–12, 2019 p193
[41]	Sauvage X, Bobruk E V, Murashkin M Y 2015 Acta Mater. 98 355 Google Scholar
[42]	Ma S M, Wang X M 2019 Mater. Sci. Eng. A 754 46 Google Scholar

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Vol. 73, Issue 7 - 2024-04-05

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