搜索

x

留言板

尊敬的读者、作者、审稿人, 关于本刊的投稿、审稿、编辑和出版的任何问题, 您可以本页添加留言。我们将尽快给您答复。谢谢您的支持!

姓名
邮箱
手机号码
标题
留言内容
验证码

液态五元Ni-Zr-Ti-Al-Cu合金快速凝固过程的高速摄影研究

徐山森 常健 吴宇昊 沙莎 魏炳波

引用本文:
Citation:

液态五元Ni-Zr-Ti-Al-Cu合金快速凝固过程的高速摄影研究

徐山森, 常健, 吴宇昊, 沙莎, 魏炳波

Rapid solidification mechanism of liquid quinary Ni-Zr-Ti-Al-Cu alloy investigated by high-speed cinematography

Xu Shan-Sen, Chang Jian, Wu Yu-Hao, Sha Sha, Wei Bing-Bo
PDF
HTML
导出引用
  • 采用电磁悬浮和自由落体两种无容器熔凝技术, 并借助高速摄影实时分析方法, 研究了液态五元Ni40Zr28.5Ti16.5Al10Cu5合金的深过冷能力和快速凝固机制. 在电磁悬浮条件下, 液态合金的过冷度可达290 K (0.21TL). 当深过冷熔体快速凝固时, 高速摄影观察发现悬浮液滴表面呈现点状和环状两种区域形核方式. 合金的快速凝固组织由初生Ni3Ti相、次生Ni10Zr7相和(Ni10Zr7+Ni21Zr8)共晶组成. 初生Ni3Ti相以枝晶方式生长, 枝晶生长速度随熔体过冷度的增大以幂函数关系单调递增, 最高可达12 mm/s, 同时其体积分数逐渐减小至13.4%, 并发生显著组织细化. 在自由落体条件下, 尽管合金液滴凝固组织的相组成并未发生变化, 但随着过冷度的增大, 初生Ni3Ti相的生长被抑制, 凝固组织由晶态向非晶态转变, 且非晶相的体积分数线性增大. 当直径小于275 μm时, 合金液滴实现了完全非晶态凝固.
    The ability to undercool and solidification mechanism of liquid quinary Ni40Zr28.5Ti16.5Al10Cu5 alloy are investigated by electromagnetic levitation (EML) and drop tube (DT) technique. Under the EML condition, the maximum undercooling of levitated alloy can reach up to 290 K (0.21TL). Under the DT condition, the alloy achieves higher undercooling than EML, and solidifies finally into metallic glass. At lower undercooling, the solidification structure of the alloy is composed of primary Ni3Ti phase, secondary Ni10Zr7 phase and eutectic (Ni10Zr7+Ni21Zr8) phase. With the rise of undercooling, the solidification structure displays the following evolution events: phase morphology refinement, primary phase inhibition, phase number reduction, and amorphous phase formation. By using the high-speed cinematography technique, three nucleation modes are distinctly observed on the levitated alloy melt surface at the beginning of solidification, that is, single-point nucleation, multi-point nucleation and annular nucleation. The levitation state corresponding to single-point mode nucleation is relatively stable, and the alloy undercooling is also relatively low. The annular nucleation only occursin the case with high rotation speed, and the undercooling is greater than 208 K. The discrepancy between nucleation modes is due to the He gas flow for forced cooling. The theoretical calculations indicate that the alloy droplets achieve high undercoolingand large cooling rate under the DT condition. The experimental results show that when the droplet diameter decreases to 498 μm, the amorphous phase begins to appear in the alloy particles. It is noteworthy that the amorphous phase is preferentially formed inside the droplet, but not on the outer surface. The morphology of solidification structure reveals that different regions of the droplet have various local undercoolings, which result in the distribution characteristics of amorphous phase. The volume fraction of amorphous phase increases linearly with the decrease of particle diameter. When the droplet diameter decreases to 275 μm, the alloy droplets are completely frozen into glassy particles. The average eutecticspacing values are also measured at different alloy undercoolings. Compared with the classical binary eutectic growth model, the experimental eutectic growth law exhibits a large deviation in index. This indicates that the eutectic growth in multicomponent alloys displays more complex kinetic characteristics.
      通信作者: 魏炳波, bbwei@nwpu.edu.cn
    • 基金项目: 国家自然科学基金(批准号: 51771154, 51327901)和陕西省重点研发计划(批准号: 2019GY-152)资助的课题
      Corresponding author: Wei Bing-Bo, bbwei@nwpu.edu.cn
    • Funds: Project supported by the National Natural Science Foundation of China (Grant Nos. 51771154, 51327901) and the Key Research and Development Program of Shaanxi (Grant No. 2019GY-152)
    [1]

    Zhao P, Heinrich J C, Poirier D R 2005 Int. J. Numer. Meth. Fluids 49 233Google Scholar

    [2]

    Sánchez Lamazares J L, Sanchez T, Santos J D, Pérez M J, Sanchez M L, Hernando B 2008 Appl. Phys. Lett. 92 4358

    [3]

    Wu M, Liu T, Dong M, Sun J M, Dong S L, Qiang W 2017 J. Appl. Phys. 121 064901Google Scholar

    [4]

    Lü P, Wang H P 2017 Scr. Mater. 137 31Google Scholar

    [5]

    Chen F, Zhang T Q, Wang J, Zhang L T, Zhou G F 2015 J. Alloy. Compd. 640 375

    [6]

    翟秋亚, 杨扬, 徐锦锋, 郭学锋 2007 物理学报 56 6118Google Scholar

    Zhai Q Y, Yang Y, Xu J F, Guo X F 2007 Acta Phys. Sin. 56 6118Google Scholar

    [7]

    Haein C Y, Xu D H, William L J 2003 Appl. Phys. Lett. 82 1030Google Scholar

    [8]

    Duwez P, Willens R H, Klement J W 1960 J. Appl. Phys. 31 1137

    [9]

    沙莎, 王伟丽, 吴宇昊, 魏炳波 2018 物理学报 67 046402Google Scholar

    Sha S, Wang W L, Wu Y H, Wei B 2018 Acta Phys. Sin. 67 046402Google Scholar

    [10]

    Greaves G N, Wilding M C, Fearn S, Langstaff D, Kargl F, Cox S, Vu Van Q, Majérus O, Benmore C J, Weber R, Martin C M, Hennet L 2008 Science 322 566Google Scholar

    [11]

    Kavouras A, Krammer G 2003 Rev. Sci. Instrum. 74 4468Google Scholar

    [12]

    Baer S, Andrade M A, Esen C, Adamowski J C, Schweiger G, Ostendorf A 2011 Rev. Sci. Instrum. 82 105111Google Scholar

    [13]

    Wall J J, Weber R, Kim J, Liaw P K, Choo H 2007 Mater. Sci. Eng. A 445 219

    [14]

    Skinner L B, Benmore C J, Weber J K R, Du J, Neuefeind J, Tumber S K, Parise1 J B 2014 Phys. Rev. Lett. 112 157801Google Scholar

    [15]

    Lan S, Blodgett M, Kelton K F, Ma J L, Fan J, Wang X L 2016 Appl. Phys. Lett. 108 831

    [16]

    杨尚京, 王伟丽, 魏炳波 2015 物理学报 64 056401Google Scholar

    Yang S J, Wang W L, Wei B 2015 Acta Phys. Sin. 64 056401Google Scholar

    [17]

    Royer Z L, Tackes C, Lesar R, Napolitano R E 2013 J. Appl. Phys. 113 214901Google Scholar

    [18]

    Lee J, Rodriguez J E, Hyers R W, Matson D M 2015 Metall. Mater. Trans. B 46 2470Google Scholar

    [19]

    Cao L, Cochrane R F, Mullis A M 2015 Intermetallics 60 33Google Scholar

    [20]

    Xu D, Duan G, Johnson W L, Garland C 2004 Acta Mater. 52 3493Google Scholar

    [21]

    Lee E S, Ahn S 1994 Acta Metall. Mater. 42 3231Google Scholar

    [22]

    Wang W L, Li Z Q, Wei B 2011 Acta Mater. 59 5482Google Scholar

    [23]

    Alford T L, Gale W F, Totemeir T C 2015 Smithells Metals Reference Book (Elsevier) 8−2

    [24]

    Inoue A 2000 Acta Mater. 48 279Google Scholar

    [25]

    Jackson K A, Hunt J D 1988 Dyna. Curv. Front. 236363

    [26]

    Kurz W, Trivedi R 1991 Metall. Trans. A 22 3051Google Scholar

  • 图 1  五元Ni40Zr28.5Ti16.5Al10Cu5合金的相组成和相变特征 (a) X射线衍射图谱; (b) DSC热分析曲线; (c) 电磁悬浮状态下的冷却曲线

    Fig. 1.  Phase constitution and transition characteristics of quinary Ni40Zr28.5Ti16.5Al10Cu5 alloy: (a) XRD pattern; (b) DSC thermogram; (c) cooling curve at levitated state.

    图 2   初生 Ni3Ti相快速生长引起的再辉过程(a) 单点形核; (b) 多点形核; (c) 环区形核

    Fig. 2.  Recalescence process caused by rapid growth of primary Ni3Ti phase(a) Single-point nucleation; (b) multi-point nucleation; (c) annular region nucleation.

    图 3  悬浮状态下合金液滴的旋转速率与过冷度关系

    Fig. 3.  Rotation rateversus undercooling of levitated alloy droplet

    图 4  初生Ni3Ti相枝晶生长与组织特征  (a) 枝晶生长速度; (b) 最大尺寸和体积分数

    Fig. 4.  Dendritic growth and microstructure of primary Ni3Ti phase: (a) Dendritic growth velocity; (b) maximum length and volume fraction.

    图 5  电磁悬浮条件下Ni40Zr28.5Ti16.5Al10Cu5合金的微观组织形态 (a)母合金; (b) ΔT=115 K; (c) ΔT=200 K; (d) ΔT=290 K

    Fig. 5.  Solidification microstructures of electromagnetically levitated Ni40Zr28.5Ti16.5Al10Cu5 alloy. (a) Master alloy; (b) ΔT=115 K; (c) ΔT=200 K; (d) ΔT=290 K.

    图 6  合金液滴深过冷与共晶生长特征 (a)过冷度随液滴直径变化; (b) 共晶间距随过冷度变化

    Fig. 6.  Liquid undercooling and eutectic growth of alloy droplets: (a) Estimated undercoolings of freely falling alloy droplets; (b) average eutectic spacing versus undercooling.

    图 7  合金液滴内部温度场随直径和位置的变化关系 (a) 温度分布; (b) 温度梯度; (c) 冷却速率

    Fig. 7.  Internal temperature field of alloy droplet versus diameter and location (a) Temperature distribution; (b) temperature gradient; (c) cooling rate.

    图 8   自由落体条件下不同直径合金液滴的凝固组织形貌 (a) 957 μm直径; (b) A区放大; (c) B区放大(d) 428 μm直径; (e) C区放大; (f) D区放大

    Fig. 8.  Microstructural morphology of solidified alloy droplets with different diameters.(a) 957 μm diameter; (b) Enlarged A in (a); (c) Enlarged B in (a)(d) 428 μm diameter; (b) Enlarged C in (d); (c) Enlarged D in (d)

    图 9  合金液滴凝固组织中非晶相分布规律

    Fig. 9.  Amorphous phase distribution versus alloy droplet diameter

    图 10  合金凝固组织特征随液滴直径变化规律 (a) 非晶相体积分数; (b) 共晶相平均间距

    Fig. 10.  Variation of solidification microstructures with alloy droplets diameter: (a) Typical structure parameters; (b) average eutectic spacing.

    表 1  理论计算用热物性参数[23]

    Table 1.  Physical parameters used in calculations

    物理参数 数值
    初始温度, T0/K 1500
    环境温度, Ti/K 298
    热导率, κ/W·m–1·K–1 65.4
    液相线温度, TL/K 1400
    Stefan-Boltzmann常数, σSB/W·m–1·K–1 5.67 × 10–8
    熔体密度, ρ/kg·m–3 6.15 × 103
    位置参数, r/r0 0.1—1.0
    熔体热辐射系数, εh 0.2
    熔体比热, Cp, /J·kg–1·K–1 601
    下载: 导出CSV
  • [1]

    Zhao P, Heinrich J C, Poirier D R 2005 Int. J. Numer. Meth. Fluids 49 233Google Scholar

    [2]

    Sánchez Lamazares J L, Sanchez T, Santos J D, Pérez M J, Sanchez M L, Hernando B 2008 Appl. Phys. Lett. 92 4358

    [3]

    Wu M, Liu T, Dong M, Sun J M, Dong S L, Qiang W 2017 J. Appl. Phys. 121 064901Google Scholar

    [4]

    Lü P, Wang H P 2017 Scr. Mater. 137 31Google Scholar

    [5]

    Chen F, Zhang T Q, Wang J, Zhang L T, Zhou G F 2015 J. Alloy. Compd. 640 375

    [6]

    翟秋亚, 杨扬, 徐锦锋, 郭学锋 2007 物理学报 56 6118Google Scholar

    Zhai Q Y, Yang Y, Xu J F, Guo X F 2007 Acta Phys. Sin. 56 6118Google Scholar

    [7]

    Haein C Y, Xu D H, William L J 2003 Appl. Phys. Lett. 82 1030Google Scholar

    [8]

    Duwez P, Willens R H, Klement J W 1960 J. Appl. Phys. 31 1137

    [9]

    沙莎, 王伟丽, 吴宇昊, 魏炳波 2018 物理学报 67 046402Google Scholar

    Sha S, Wang W L, Wu Y H, Wei B 2018 Acta Phys. Sin. 67 046402Google Scholar

    [10]

    Greaves G N, Wilding M C, Fearn S, Langstaff D, Kargl F, Cox S, Vu Van Q, Majérus O, Benmore C J, Weber R, Martin C M, Hennet L 2008 Science 322 566Google Scholar

    [11]

    Kavouras A, Krammer G 2003 Rev. Sci. Instrum. 74 4468Google Scholar

    [12]

    Baer S, Andrade M A, Esen C, Adamowski J C, Schweiger G, Ostendorf A 2011 Rev. Sci. Instrum. 82 105111Google Scholar

    [13]

    Wall J J, Weber R, Kim J, Liaw P K, Choo H 2007 Mater. Sci. Eng. A 445 219

    [14]

    Skinner L B, Benmore C J, Weber J K R, Du J, Neuefeind J, Tumber S K, Parise1 J B 2014 Phys. Rev. Lett. 112 157801Google Scholar

    [15]

    Lan S, Blodgett M, Kelton K F, Ma J L, Fan J, Wang X L 2016 Appl. Phys. Lett. 108 831

    [16]

    杨尚京, 王伟丽, 魏炳波 2015 物理学报 64 056401Google Scholar

    Yang S J, Wang W L, Wei B 2015 Acta Phys. Sin. 64 056401Google Scholar

    [17]

    Royer Z L, Tackes C, Lesar R, Napolitano R E 2013 J. Appl. Phys. 113 214901Google Scholar

    [18]

    Lee J, Rodriguez J E, Hyers R W, Matson D M 2015 Metall. Mater. Trans. B 46 2470Google Scholar

    [19]

    Cao L, Cochrane R F, Mullis A M 2015 Intermetallics 60 33Google Scholar

    [20]

    Xu D, Duan G, Johnson W L, Garland C 2004 Acta Mater. 52 3493Google Scholar

    [21]

    Lee E S, Ahn S 1994 Acta Metall. Mater. 42 3231Google Scholar

    [22]

    Wang W L, Li Z Q, Wei B 2011 Acta Mater. 59 5482Google Scholar

    [23]

    Alford T L, Gale W F, Totemeir T C 2015 Smithells Metals Reference Book (Elsevier) 8−2

    [24]

    Inoue A 2000 Acta Mater. 48 279Google Scholar

    [25]

    Jackson K A, Hunt J D 1988 Dyna. Curv. Front. 236363

    [26]

    Kurz W, Trivedi R 1991 Metall. Trans. A 22 3051Google Scholar

  • [1] 金英捷, 耿德路, 林茂杰, 胡亮, 魏炳波. 静电悬浮条件下液态Zr60Ni25Al15合金的热物理性质与快速凝固机制. 物理学报, 2024, 0(0): 0-0. doi: 10.7498/aps.73.20232002
    [2] 武博文, 胡亮, 耿德路, 魏炳波. 液态Zr35Al23Ni22Gd20合金的亚稳相分离与双相非晶形成机理. 物理学报, 2023, 72(21): 216401. doi: 10.7498/aps.72.20231002
    [3] 徐山森, 常健, 翟斌, 朱先念, 魏炳波. 液态五元Zr57Cu20Al10Ni8Ti5合金的微观结构演变与非晶形成机制. 物理学报, 2023, 72(22): 226401. doi: 10.7498/aps.72.20231169
    [4] 沙莎, 王伟丽, 吴宇昊, 魏炳波. 深过冷条件下Co7Mo6金属间化合物的枝晶生长和维氏硬度研究. 物理学报, 2018, 67(4): 046402. doi: 10.7498/aps.67.20172156
    [5] 陈克萍, 吕鹏, 王海鹏. 微重力条件下Cu-Zr共晶合金的液固相变研究. 物理学报, 2017, 66(6): 068101. doi: 10.7498/aps.66.068101
    [6] 谷倩倩, 阮莹, 代富平. 微重力下Fe-Al-Nb合金液滴的快速凝固机理及其对显微硬度的影响. 物理学报, 2017, 66(10): 106401. doi: 10.7498/aps.66.106401
    [7] 朱海哲, 阮莹, 谷倩倩, 闫娜, 代富平. 落管中Ni-Fe-Ti合金的快速凝固机理及其磁学性能. 物理学报, 2017, 66(13): 138101. doi: 10.7498/aps.66.138101
    [8] 林茂杰, 常健, 吴宇昊, 徐山森, 魏炳波. 电磁悬浮条件下液态Fe50Cu50合金的对流和凝固规律研究. 物理学报, 2017, 66(13): 136401. doi: 10.7498/aps.66.136401
    [9] 魏绍楼, 黄陆军, 常健, 杨尚京, 耿林. 液态Ti-Al合金的深过冷与快速枝晶生长. 物理学报, 2016, 65(9): 096101. doi: 10.7498/aps.65.096101
    [10] 杨尚京, 王伟丽, 魏炳波. 深过冷液态Al-Ni合金中枝晶与共晶生长机理. 物理学报, 2015, 64(5): 056401. doi: 10.7498/aps.64.056401
    [11] 宋其晖, 石万元. 横向静磁场对电磁悬浮液滴稳定性的影响. 物理学报, 2014, 63(24): 248504. doi: 10.7498/aps.63.248504
    [12] 王小娟, 阮莹, 洪振宇. Al-Cu-Ge合金的热物理性质与快速凝固规律研究. 物理学报, 2014, 63(9): 098101. doi: 10.7498/aps.63.098101
    [13] 闫娜, 王伟丽, 代富平, 魏炳波. 三元Co-Cu-Pb偏晶合金的快速凝固组织形成规律研究. 物理学报, 2011, 60(3): 036402. doi: 10.7498/aps.60.036402
    [14] 殷涵玉, 鲁晓宇. 深过冷Cu60Sn30Pb10偏晶合金的快速凝固. 物理学报, 2008, 57(7): 4341-4346. doi: 10.7498/aps.57.4341
    [15] 梅策香, 阮 莹, 代富平, 魏炳波. 深过冷Ag-Cu-Ge三元共晶合金的相组成与凝固特征. 物理学报, 2007, 56(2): 988-993. doi: 10.7498/aps.56.988
    [16] 臧渡洋, 王海鹏, 魏炳波. 深过冷三元Ni-Cu-Co合金的快速枝晶生长. 物理学报, 2007, 56(8): 4804-4809. doi: 10.7498/aps.56.4804
    [17] 张蜡宝, 代富平, 熊予莹, 魏炳波. 深过冷Ni-15%Sn合金熔体表面张力研究. 物理学报, 2006, 55(1): 419-423. doi: 10.7498/aps.55.419
    [18] 刘向荣, 王 楠, 魏炳波. 无容器条件下Cu-Pb偏晶的快速生长. 物理学报, 2005, 54(4): 1671-1678. doi: 10.7498/aps.54.1671
    [19] 姚文静, 杨 春, 韩秀君, 陈 民, 魏炳波, 过增元. 微重力条件下Ni-Cu合金的快速枝晶生长研究. 物理学报, 2003, 52(2): 448-453. doi: 10.7498/aps.52.448
    [20] 马伟增, 季诚昌, 李建国. 直流磁场控制电磁悬浮熔炼旋转稳定性的理论分析. 物理学报, 2002, 51(10): 2233-2238. doi: 10.7498/aps.51.2233
计量
  • 文章访问数:  7432
  • PDF下载量:  89
  • 被引次数: 0
出版历程
  • 收稿日期:  2019-06-13
  • 修回日期:  2019-07-10
  • 上网日期:  2019-10-01
  • 刊出日期:  2019-10-05

/

返回文章
返回