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面向等离子体材料用先进钨复合材料的改性研究进展与趋势

罗来马,  颜硕,  刘祯,  昝祥,  吴玉程

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文章导航 > 粉末冶金技术  > 2023 >  41(1): 12-29
罗来马, 颜硕, 刘祯, 昝祥, 吴玉程. 面向等离子体材料用先进钨复合材料的改性研究进展与趋势[J]. 粉末冶金技术, 2023, 41(1): 12-29. doi: 10.19591/j.cnki.cn11-1974/tf.2022030012
引用本文: 罗来马, 颜硕, 刘祯, 昝祥, 吴玉程. 面向等离子体材料用先进钨复合材料的改性研究进展与趋势[J]. 粉末冶金技术, 2023, 41(1): 12-29. doi: 10.19591/j.cnki.cn11-1974/tf.2022030012
shu
LUO Laima, YAN Shuo, LIU Zhen, ZAN Xiang, WU Yucheng. Research progress and trend of advanced tungsten composite modification used for plasma facing materials[J]. Powder Metallurgy Technology, 2023, 41(1): 12-29. doi: 10.19591/j.cnki.cn11-1974/tf.2022030012
Citation: LUO Laima, YAN Shuo, LIU Zhen, ZAN Xiang, WU Yucheng. Research progress and trend of advanced tungsten composite modification used for plasma facing materials[J]. Powder Metallurgy Technology, 2023, 41(1): 12-29. doi: 10.19591/j.cnki.cn11-1974/tf.2022030012
shu

面向等离子体材料用先进钨复合材料的改性研究进展与趋势

doi: 10.19591/j.cnki.cn11-1974/tf.2022030012
  • 1.

    合肥工业大学材料科学与工程学院, 合肥 230009

  • 2.

    合肥工业大学有色金属与加工技术国家地方联合工程研究中心, 合肥 230009

  • 3.

    合肥工业大学高性能铜合金材料及成形加工教育部工程研究中心, 合肥 230009

基金项目: 国家重点研发磁约束聚变能发展专项资助项目（2019YFE03120002）；安徽省重点研发项目（202104a05020045）；安徽省自然基金杰出青年基金资助项目（2108085J21）
详细信息
    通讯作者:

    E-mail: luolaima@126.com

  • 中图分类号: TG146.1

Research progress and trend of advanced tungsten composite modification used for plasma facing materials

  • 1.

    School of Materials Science and Engineering, Hefei University of Technology, Hefei 230009, China

  • 2.

    National-Local Joint Engineering Research Centre of Nonferrous Metals and Processing Technology, Hefei University of Technology, Hefei 230009, China

  • 3.

    Engineering Research Center of High Performance Copper Alloy Materials and Processing, Ministry of Education, Hefei University of Technology, Hefei 230009, China

More Information

    摘要
  • 摘要: 核聚变能是解决未来社会能源危机的有效途径之一，但面向等离子体材料在聚变堆体中面临着来自等离子体严重的辐照和热冲击损伤。纯钨因其高热导率、良好的高温强度、低溅射和低蒸气压而被认为是最有希望的面向等离子体候选材料。纯钨在聚变堆工况条件下具有严重的脆性风险，因而对面向等离子体材料用先进钨材料的改性成为近年来的研究热点。钨基复合材料的改性方法主要包括合金化、第二相强化、纤维增韧和复合强化。本文综述了近年来国内外针对核聚变反应堆面向等离子体材料用钨基复合材料的改性方法及其性能，分析了钨基复合材料的改性机制，并展望了面向等离子体材料用钨基复合材料的发展方向。
    Abstract: Fusion energy is one of the effective ways to solve the energy crisis in the future, but the plasma-facing materials (PFMs) face the serious radiation and thermal shock damage from the plasma in the fusion reactor. At present, the pure tungsten is considered as the most promising PFM candidate materials because of the high thermal conductivity, good high-temperature strength, low sputtering, and low vapor pressure. Pure tungsten has the serious brittleness risk under the fusion reactor condition, so the modification of the advanced tungsten materials for PFMs has become the research hotspot in recent years. The modification methods of tungsten matrix composite include alloying, second phase strengthening, fiber reinforcement, and composite toughening. In this paper, the modification methods and performance of the tungsten matrix composites as PFMs used in the nuclear fusion reactors at home and abroad in recent years were reviewed, the modification mechanism of tungsten matrix composites was analyzed and summarized, and the development direction of tungsten matrix composites as PFMs was prospected.
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  • 图  1  Re掺杂对W基体中位错–核心对称性结构的影响[25]

    Figure  1.  Effect of Re doping on the dislocations–core symmetry structure in W matrix[25]

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    图  2  W和W15Re在<100>、<110>和<111>方向上的拉伸应力–应变曲线[26]

    Figure  2.  Tensile stress-strain curves of W and W15Re in <100>, <110>, and <111> directions[26]

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    图  3  工业纯W、W5Re和W10Re三种测试材料在恒定压痕应变速率下的硬度随相应温度（T/Tm）的变化[27]

    Figure  3.  Evolution of hardness with the homologous temperature (T/Tm) for the industrial pure W, W5Re, and W10Re at the constant indentation strain rates[27]

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    图  4  W‒K合金中钾泡三种复合形式：（a）晶间型；（b）晶内型；（c）晶间/晶内型[16]

    Figure  4.  Three forms of the potassium bubbles in W‒K alloys: (a) inter-type; (b) intra-type; (c) inter/intra-type[16]

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    图  5  （a）放电等离子烧结制备W–K合金硬度与烧结温度和压力的关系及（b）其金相组织[31]

    Figure  5.  （a）Relationship of the hardness, sintering temperature, and pressure of the W–K alloys prepared by SPS and（b） the corresponding metallographic microstructures [31]

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    图  6  （a）W–5%Mo（质量分数）合金1450 ℃非等温烧结过程中科肯达尔孔隙引起的膨胀和显微组织以及（b）1600 ℃放电等离子烧结W–5%Mo合金相对密度与温度的关系和显微组织[32]

    Figure  6.  Expansion and microstructure of the W–5%Mo alloys (mass fraction) caused by Kirkendal pores in the non-isothermal sintering at 1450 ℃ (a) and the relationship between the relative density and temperature and the corresponding microstructure of the W–5%Mo alloys prepared by SPS at 1600 ℃ (b)[32]

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    图  7  纯W和W–5%Ta（质量分数）合金在不同剂量He+辐照下的结构损伤[33]

    Figure  7.  Structural damage between pure W and W–5%Ta alloys (mass fraction) irradiated with different doses of He+[33]

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    图  8  不同辐照能量的W–Nb合金扫描电镜形貌[34]：（a）50 eV；（b）80 eV

    Figure  8.  SEM images of the W–Nb alloys with different irradiation energies[34]: (a) 50 eV; (b) 80 eV

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    图  9  不同氦能W25富钨区高倍透射电镜形貌[34]：（a）50 eV；（b）80 eV

    Figure  9.  High-magnification TEM images of W25 in the tungsten rich region with different helium energies[34]: (a) 50 eV; (b) 80 eV

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    图  10  W–Y2O3合金显微形貌[37]：（a）表面结构；（b）室温断口形貌

    Figure  10.  SEM images of the W–Y2O3 alloys[37]: (a) surface structure; (b) fracture morphology at room-temperature

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    图  11  冷冻干燥样品微观结构及粒度分布[38]：（a）不添加分散剂微观结构；（b）不添加分散剂粒度分布；（c）添加分散剂微观结构；（d）添加分散剂粒度分布

    Figure  11.  SEM images and particle size distribution of the freeze-dried samples[38]: (a) SEM images without dispersant; (b) particle size distribution without dispersant; (c) SEM images with dispersant; (d) particle size distribution with dispersant

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    图  12  纯W和W–2%Y2O3复合材料经氦离子辐照后表面形貌[39]：（a）纯W表面辐照区；（b）纯W表面非辐照区；（c）W–2%Y2O3表面辐照区；（d）W–2%Y2O3表面非辐照区

    Figure  12.  Surface morphology of the pure tungsten and W–2%Y2O3 composites irradiated by helium ions[39]: (a) pure tungsten surface in irradiated zone; (b) pure tungsten surface in non-irradiated zone; (c) W–2%Y2O3 surface in irradiated zone; (d) W–2%Y2O3 surface in non-irradiation zone

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    图  13  纯W和W–La2O3合金横截面显微形貌[41]：（a）纯W；（b）0.1% La2O3掺杂W合金；（c）1.0% La2O3掺杂W合金；（d）5.0% La2O3掺杂W合金

    Figure  13.  Cross-sectional images of the W and W–La2O3 alloys[41]: (a) pure W; (b) 0.1% La2O3 doped W alloys; (c) 1.0% La2O3 doped W alloys; (d) 5.0% La2O3 doped W alloys

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    图  14  不同碳化物掺杂钨合金高温退火后表面显微形貌[43]：（a）W–10TaC，1600 ℃；（b）W–10ZrC，1600 ℃；（c）W–10TiC，8 h；（d）W–10ZrC，8 h

    Figure  14.  SEM images of the W alloys doped by different carbides after high-temperature annealing[43]: (a) W–10TaC, 1600℃; (b) W–10ZrC, 1600 ℃; (c) W–10TiC, 8 h; (d) W–10ZrC, 8 h

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    图  15  不同烧结温度下W–0.5ZrC复合材料相对密度[44]

    Figure  15.  Relative density of the W–0.5ZrC composites at different sintering temperatures[44]

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    图  16  不同热流密度热冲击后W–ZrC试样的表面及加载区裂纹形貌[45]：（a）0.22 GW·m−2；（b）0.33 GW·m−2；（c）0.44 GW·m−2；（d）0.22 GW·m−2；（e）0.33 GW·m−2；（f）0.44 GW·m−2；（g）0.22 GW·m−2裂纹深度；（h）0.33 GW·m−2裂纹深度；（i）0.44 GW·m−2裂纹深度

    Figure  16.  Surface and crack morphology in the loaded areas of the W–ZrC samples after 100 shots with the different heat flux[45]: (a) 0.22 GW·m−2; (b) 0.33 GW·m−2; (c) 0.44 GW·m−2; (d) 0.22 GW·m−2; (e) 0.33 GW·m−2; (f) 0.44 GW·m−2; (g) cracking depth at 0.22 GW·m−2; (h) cracking depth at 0.33 GW·m−2; (i) cracking depth at 0.44 GW·m−2

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    图  17  不同热流密度下试样裂纹宽度扫描电子显微形貌[45]：（a）0.33 GW·m−2；（b）0.44 GW·m−2

    Figure  17.  SEM images of the crack width with the different heat flux[45]: (a) 0.33 GW·m−2; (b) 0.44 GW·m−2

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    图  18  应变速率5×10−4 s−1下热等静压压坯拉伸伸长率随TiC质量分数的变化[46]：（a）W–(0～1.5)TiC–H2；（b）W–(0～1.5)TiC–Ar

    Figure  18.  Tensile elongation at the medium strain rate of 5×10−4 s−1 for the hot isostatic pressing compacts as the function of TiC mass fraction[46]: (a) W–(0~1.5)TiC–H2; (b) W–(0~1.5)TiC–Ar

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    图  19  钨纤维增韧钨基复合材料光学显微形貌[48]

    Figure  19.  Optical image of the tungsten matrix composites toughened by tungsten fibers[48]

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    图  20  纯W及其合金在500 ℃下的应力–应变曲线[53]

    Figure  20.  Stress-strain curves of the pure W and the alloys tested at 500 ℃[53]

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    图  21  添加TiC的W–K–TiC合金抗拉强度、维氏显微硬度与晶粒尺寸平方根倒数关系[54]

    Figure  21.  Relationship of the tensile strength, Vickers micro-hardness, and the square root reciprocal of grain size for the W–K–TiC alloys with TiC addition[54]

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    图  22  W–ZrC–Re试样在不同温度下退火后的断裂表面微观形貌[57]

    Figure  22.  SEM images of the fracture surface for the W–ZrC–Re samples after annealing at different temperatures[57]

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    图  23  W–Y2O3合金中W晶界氧化物粒子透射电镜高角环形暗场相（high angle annular dark field，HAADF）和能量色散X射线光谱[58]：（a）La3+掺杂HAADF；（b）La3+掺杂EDX；（c）Hf4+掺杂HAADF；（d）Hf4+掺杂EDX

    Figure  23.  HAADF images and EDX of the oxide particles at W grain boundary for W–Y2O3 alloys[58]: (a) HAADF of La3+ doping; (b) EDX of La3+ doping; (c) HAADF of Hf4+ doping; (d) EDX of Hf4+ doping

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    图  24  试样断口扫描电子显微形貌和平均晶粒尺寸[59]：（a）W–1TiC；（b）不同Ti含量W–1TiC–xTi平均晶粒尺寸；（c）W–1TiC–0.5Ti；（d）W–1TiC–0.7Ti

    Figure  24.  SEM micrographs of the fracture surface and the average grain size of samples[59]: (a) W–1TiC; (b) the average grain size of the W–1TiC–xTi samples with different Ti contents; (c) W–1TiC–0.5Ti; (d) W–1TiC–0.7Ti

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    表  1  纯W和W–2%Y2O3在氦离子辐照下不同区域的表面粗糙度[39]

    Table  1.   Surface roughness of pure tungsten and W–2%Y2O3 in different regions under helium ion irradiation[39]

    试样辐照区 / nm非辐照区 / nm
    纯W138.5±3.584.0±3.5
    W–2%Y2O3136.5±3.0120.5±3.5
    下载: 导出CSV

    表  2  放电等离子烧结W–3Re–xHfC复合材料的测量密度、理论密度、相对密度和维氏硬度[55]

    Table  2.   Measurement density, theoretical density, relative density, and Vickers hardness of W–3Re–xHfC composites prepared by SPS[55]

    试样平均晶粒尺寸 / μm测量密度 / (g·cm−3)理论密度 / (g·cm−3)相对密度 / %维氏硬度，HV抗压强度 / MPa
    W–Re8.81±0.1518.9219.4097.5342.6±12.5250.43±8.61
    W–Re–0.5HfC7.63±0.2018.9419.3597.9369.4±10.3305.26±12.42
    W–Re–1.0HfC5.82±0.1818.9519.2498.5381.8±13.4400.15±11.05
    W–Re–5.0HfC3.85±0.1218.5718.8198.8447.1±8.6605.28±10.61
    W–Re–10.0HfC2.14±0.1317.6818.3896.2659.4±15.3852.35±5.62
    下载: 导出CSV
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