Research progress and trend of advanced tungsten composite modification used for plasma facing materials
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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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Key words:
- fusion reactor /
- plasma-facing materials /
- tungsten composites /
- modification methods /
- performance
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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]
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
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
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
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
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
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W 138.5±3.5 84.0±3.5 W–2%Y2O3 136.5±3.0 120.5±3.5 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–Re 8.81±0.15 18.92 19.40 97.5 342.6±12.5 250.43±8.61 W–Re–0.5HfC 7.63±0.20 18.94 19.35 97.9 369.4±10.3 305.26±12.42 W–Re–1.0HfC 5.82±0.18 18.95 19.24 98.5 381.8±13.4 400.15±11.05 W–Re–5.0HfC 3.85±0.12 18.57 18.81 98.8 447.1±8.6 605.28±10.61 W–Re–10.0HfC 2.14±0.13 17.68 18.38 96.2 659.4±15.3 852.35±5.62 -
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