Numerical simulations of solidification microstructure evolution process for commercial-purity aluminum alloys inoculated by Al-Ti-B refiner

Song Yan; Jiang Hong-Xiang; Zhao Jiu-Zhou; He Jie; Zhang Li-Li; Li Shi-Xin

doi:10.7498/aps.70.20201431

Abstract

Solidification microstructure of aluminum alloy has a great influence on the properties of the casting. An aluminum alloy with the structure of fine equiaxed grains has low casting defects and presents excellent mechanical properties. Recently, chemical inoculation by adding grain refiner is the technique most extensively used to achieve a fine, equiaxed grain structure of Al alloy in the industrial production. In order to investigate the detailed solidification microstructure evolution of the alloy, many numerical models have been proposed. Cellular automaton method is one of the powerful tools for simulating the morphology evolution of detailed grains in the solidification process of alloy. However, the present cellular automata model has a shortcoming, that is, its calculation of the nucleation rate is based on the experimental number density of grains. In this work, a population dynamics-cellular automaton model is developed for describing the solidification microstructure evolution of the inoculated aluminum alloy. The model takes account of the heterogeneous nucleation of α-Al nucleus, the initial spherical growth of α-Al grains and the dendritic growth process. The model is used for simulating the solidification microstructure evolution of the commercial-purity aluminum (CP-Al) inoculated by Al-5Ti-1B master alloy. The results indicate that the heterogeneous nucleation process of α-Al can be divided into the two stages. In the early stage of nucleation, there are enough effective particles in the melt. The nucleation rate of α-Al increases with the increase of the undercooling of the melt. After a short time, the nucleation of α-Al is dominated by the number density of the effective particles in the melt. Nucleation process stops when the recalescence takes place. The effects of the additive amount of Al-5Ti-1B master alloy and the cooling rate of the melt on the solidification microstructure of the CP-Al are investigated by using the established model. The final solidification structures of CP-Al are predicted. And a comparison between the predicted results and the experimental ones shows that they are in good agreement with each other.

Keywords:

Authors and contacts

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

Corresponding author: Jiang Hong-Xiang, hxjiang@imr.ac.cn ; Zhao Jiu-Zhou, jzzhao@imr.ac.cn ;

Funds: Project supported by the Chinese Academy of Sciences Strategic Priority Program on Space Science, China (Grant No. XDA15013800), the Natural Science Foundation of Liaoning Province, China (Grant No. 2020-MS-005), and the National Natural Science Foundation of China (Grant Nos. 51771210, 51501207, 51971227)

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References

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[2]	Guo G R, Tie D 2017 Acta Metall. Sinica 30 409 Google Scholar
[3]	Liu Z 2017 Metall. Mater. Trans. 48 4755 Google Scholar
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[5]	Zhang L L, Jiang H X, Zhao J Z, He J 2017 J. Mater. Process. Technol. 246 205 Google Scholar
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[9]	Easton M, StJohn D 2005 Metall. Mater. Trans A. 36A 1911 Google Scholar
[10]	Qian M, Cao P, Easton M A, McDonald S D, StJohn D H 2010 Acta Mater. 58 3262 Google Scholar
[11]	Wheeler A A, Boettinger W J, McFadden G B 1992 Phys. Rev. A 45 7424 Google Scholar
[12]	Boussinot G, Apel M 2017 Acta Mater. 122 310 Google Scholar
[13]	陈云, 康秀红, 李殿中 2009 物理学报 58 390 Google Scholar Chen Y, Kang X H, Li D Z 2009 Acta Phys. Sin. 58 390 Google Scholar
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图 1 0.01% Al-5Ti-1B中间合金细化处理工业纯铝凝固过程中, 熔体过饱和度S = C_l – C_e, α-Al形核驱动力ΔG_V, 异质形核率I随时间的变化. 熔体冷速为3.5 K/s

Figure 1. The supersaturation of the melt S = C_l – C_e (dash line), the driving force of nucleation ΔG_V (dot line) and the heterogeneous nucleation rate I (solid line) of α-Al during cooling the CP-Al melt inoculated by 0.01% Al-5Ti-1B master alloy at the cooling rate of 3.5 K/s.

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图 2 0.01% Al-5Ti-1B中间合金细化处理工业纯铝凝固过程中, α-Al晶核半径r分布随时间的变化. 熔体冷速为3.5 K/s

Figure 2. The radius distribution of α-Al nucleus at different time during cooling the CP-Al melt inoculated by 0.01% Al-5Ti-1B master alloy at the cooling rate of 3.5 K/s.

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图 3 0.01% Al-5Ti-1B中间合金细化处理工业纯铝凝固过程中, α-Al晶核总数量n_all, 球状晶n_spherical以及树枝晶数目n_dendrities随时间的变化. 熔体冷速为3.5 K/s

Figure 3. The number density of all nucleus n_all in the Al melt, the number density of spherical nucleus n_spherical and the number density of dendrities n_dendrities during cooling the CP-Al melt inoculated by 0.01% Al-5Ti-1B master alloy at the cooling rate of 3.5 K/s.

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图 4 0.01% Al-5Ti-1B中间合金细化处理工业纯铝凝固微观组织演变过程　(a) 固相分数 = 0.1%; (b) 固相分数 = 1.0%; (c) 固相分数 = 25.0%; (d) 固相分数 = 70.0%. 熔体冷速为3.5 K/s. 计算区域尺寸为600 μm × 600 μm × 600 μm

Figure 4. Solidification microstructure evolution during cooling the CP-Al melt inoculated by 0.01% Al-5Ti-1B master alloy at a cooling rate of 3.5 K/s: (a) Solid fraction = 0.1%; (b) solid fraction = 1.0%; (c) solid fraction = 25.0%; (d) solid fraction = 70.0%. The size of computational domain is 600 μm × 600 μm × 600 μm.

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图 5 不同数量Al-5Ti-1B中间合金细化工业纯铝凝固时异质形核率I, 熔体过冷度ΔT随时间的变化. 熔体冷速为3.5 K/s

Figure 5. Calculated heterogeneous nucleation rate I of α-Al and the undercooling of the melt ΔT for the CP-Al inoculated by different amount of Al-5Ti-1B master alloy at a cooling rate of 3.5 K/s.

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图 6 不同数量Al-5Ti-1B中间合金细化工业纯铝凝固组织模拟结果　(a) 0.005%; (b) 0.01%; (c) 0.4%; (d) 1.0%. 熔体冷速为3.5 K/s. 计算区域尺寸为900 μm × 900 μm × 900 μm

Figure 6. Simulated solidification microstructure for the CP-Al melt inoculated by different amount of Al-5Ti-1B master alloy at a cooling rate of 3.5 K/s: (a) 0.005%; (b) 0.01%; (c) 0.4%; (d) 1.0%. The size of computational domain is 900 μm × 900 μm × 900 μm.

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图 7 不同数量Al-5Ti-1B中间合金细化工业纯铝晶粒尺寸预测结果与实验结果. 熔体冷速为3.5 K/s. 误差棒为标准偏差

Figure 7. Predicted and measured grains size vs. the additive amount of Al-5Ti-1B master alloy for the inoculated CP-Al at a cooling rate of 3.5 K/s. The error bars represent the standard deviations.

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图 8 不同冷却速度下经0.5% Al-5Ti-1B中间合金细化处理, 工业纯铝凝固时α-Al形核率随时间的变化　(a) 1.0 K/s; (b) 2.0 K/s; (c) 5.5 K/s; (d) 10.0 K/s

Figure 8. Calculated heterogeneous nucleation rate of α-Al during cooling the CP-Al inoculated by 0.5% Al-5Ti-1B master alloy at the different rate: (a) 1.0 K/s; (b) 2.0 K/s; (c) 5.5 K/s; (d) 10.0 K/s.

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图 9 0.5%Al-5Ti-1B中间合金细化工业纯铝, 在不同冷却速度凝固后凝固组织的模拟结果　(a) 1.0 K/s; (b) 2.0 K/s; (c) 5.5 K/s; (d) 10 K/s. 计算区域尺寸为900 μm × 900 μm × 900 μm

Figure 9. Simulated solidification microstructure for the CP-Al melt inoculated by 0.5% Al-5Ti-1B master alloy at the different cooling rate of the melt: (a) 1.0 K/s; (b) 2.0 K/s; (c) 5.5 K/s; (d) 10 K/s. The size of computational domain is 900 μm × 900 μm × 900 μm.

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图 10 0.5%Al-5Ti-1B中间合金细化工业纯铝, 在不同冷却速度下凝固后晶粒尺寸预测结果与实验结果. 误差棒为标准偏差

Figure 10. Predicted and measured grains size vs. the cooling rate of the melt for the CP-Al inoculated by 0.5%Al-5Ti-1B master alloy. The error bars represent the standard deviations.

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表 1 工业纯铝成分^[30]

Table 1. The composition of solute in the CP-Al alloys used by Greer et al.^[30].

Element	Liquidus slope, m	Partition coefficient, k	Solute composition/% (weight percent)	Q
Fe	–2.925	0.030	0.0825	0.234
Si	–6.62	0.120	0.0475	0.276
Ga	–2.52	0.140	0.0125	0.028
Ni	–3.50	0.004	0.0051	0.018
V	9.71	3.330	0.0079	0.167
Ti	25.63	7.000	0.0042	0.63
Na	–7.84	0.013	0.0015	0.012

DownLoad: CSV

表 2 模拟使用的工业纯铝参数^[22,30,32]

Table 2. The parameters of CP-Al alloys used in the simulations^[22,30,32].

Parameter	Value
Cooling rate of the CP-Al melt/(K·s^–1)	3.5
Strength of the anisotropy of the interfacial energy, ε	0.04
Gibbs-Thomson coefficient, $\varGamma $/mK	1.42 × 10⁷
Heat capacity of Al melt, C_P/(J·K^–1·m³)	2.58 × 10⁶
Average jump distance of Al atoms in Al melt, δ/m	2.87 × 10^–10
Boltzmann’s constant, k_B	1.38 × 10^–23

DownLoad: CSV

[1]	Murty B S, Kori S A, Chakraborty M 2002 Int. Mater. Rev. 47 3 Google Scholar
[2]	Guo G R, Tie D 2017 Acta Metall. Sinica 30 409 Google Scholar
[3]	Liu Z 2017 Metall. Mater. Trans. 48 4755 Google Scholar
[4]	Greer A L 2016 J. Chem. Phys. 145 211704 Google Scholar
[5]	Zhang L L, Jiang H X, Zhao J Z, He J 2017 J. Mater. Process. Technol. 246 205 Google Scholar
[6]	Jiang H X, Sun Q, Zhang L L, Zhao J Z 2018 J. Alloys Compd. 748 774 Google Scholar
[7]	StJohn D H, Qian M, Easton M A, Cao P 2011 Acta Mater. 59 4907 Google Scholar
[8]	Quested T E, Greer A L 2004 Acta Mater. 52 5233 Google Scholar
[9]	Easton M, StJohn D 2005 Metall. Mater. Trans A. 36A 1911 Google Scholar
[10]	Qian M, Cao P, Easton M A, McDonald S D, StJohn D H 2010 Acta Mater. 58 3262 Google Scholar
[11]	Wheeler A A, Boettinger W J, McFadden G B 1992 Phys. Rev. A 45 7424 Google Scholar
[12]	Boussinot G, Apel M 2017 Acta Mater. 122 310 Google Scholar
[13]	陈云, 康秀红, 李殿中 2009 物理学报 58 390 Google Scholar Chen Y, Kang X H, Li D Z 2009 Acta Phys. Sin. 58 390 Google Scholar
[14]	单博炜, 林鑫, 魏雷, 黄卫东 2009 物理学报 58 1132 Google Scholar Shan B W, Lin X, Wei L, Huang W D 2009 Acta Phys. Sin. 58 1132 Google Scholar
[15]	赵九洲, 李璐, 张显飞 2014 金属学报 50 641 Google Scholar Zhao J Z, Li L, Zhang X F 2014 Acta Metall. Sin. 50 641 Google Scholar
[16]	Gandin C A, Rappaz M 1994 Acta Metall. Mater. 42 2233 Google Scholar
[17]	Zhu M F, Hong C P 2001 ISIJ Int. 41 436 Google Scholar
[18]	石玉峰, 许庆彦, 柳百成 2013 物理学报 61 108101 Google Scholar Shi Y F, Xu Q Y, Liu B C 2013 Acta Phys. Sin. 61 108101 Google Scholar
[19]	潘诗琰, 朱鸣芳 2009 物理学报 58 278 Google Scholar Pan S Y, Zhu M F 2009 Acta Phys. Sin. 58 278 Google Scholar
[20]	Zhang X F, Zhao J Z, Jiang H X, Zhu M F 2012 Acta Mater. 60 2249 Google Scholar
[21]	Mullins W W, Sekerka R F 1963 J. Appl. Phys. 34 323 Google Scholar
[22]	张丽丽, 江鸿翔, 赵九洲, 李璐, 孙倩 2017 金属学报 53 1091 Google Scholar Zhang L L, Jiang H X, Zhao J Z, Li L, Sun Q 2017 Acta Metall. Sin. 53 1091 Google Scholar
[23]	邓聪坤, 江鸿翔, 赵九洲, 何杰, 赵雷 2020 金属学报 56 212 Google Scholar Deng C K, Jiang H X, Zhao J Z, He J, Zhao L 2020 Acta Metall. Sin. 56 212 Google Scholar
[24]	张显飞 2012 博士学位论文 (沈阳: 中国科学院金属研究所) Zhang X F 2012 Ph. D. Dissertation (Shenyang: Institute of Metal Research, Chinese Academy of Sciences) (in Chinese)
[25]	江鸿翔, 赵九洲 2011 金属学报 47 1099 Google Scholar Jiang H X, Zhao J Z 2011 Acta Metall. Sin. 47 1099 Google Scholar
[26]	陈海林 2008 博士学位论文 (长沙: 中南大学) Chen H L 2008 Ph. D. Dissertation (Changsha: Central South University) (in Chinese)
[27]	Ansara I, Dinsdale A T, Rand M H 1998 Cost 507: Thermochemical Database for Light Metal Alloys (Vol. 2) (Luxembourg: Office for Official Publications of the European Communities)
[28]	Xu Y J, Zhao D D, Li Y J 2018 Metall. Mater. Trans. A 49 1770 Google Scholar
[29]	傅献彩, 沈文霞, 姚天杨, 侯文华 2007 物理化学(上册) (北京: 高等教育出版社) 第168页 Fu X C, Shen W X, Yao T Y, Hou W H 2007 Physical Chemistry (Vol. 1) (Beijing: Higher Education Press) p168 (in Chinese)
[30]	Greer A L, Bunn A M, Tronche A 2000 Acta Mater. 48 2823 Google Scholar
[31]	Quested T E, Greer A L 2005 Acta Mater. 53 4643 Google Scholar
[32]	Men H, Fan Z 2011 Acta Mater. 59 2704 Google Scholar

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