Research progress on the interface and grain control in carbon nanotube reinforced aluminum matrix composites
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摘要: 随着碳纳米管增强铝基复合材料制备工艺的不断完善，碳纳米管的难分散问题被妥善解决，复合材料的强度有所提高，但复合材料的高模量、高强度没有得到充分利用，并出现“强度–塑性”倒置现象。本文总结了近年来对碳/铝复合材料界面结构、晶粒结构与复合构型设计的调控手段，讨论了界面结构强度对碳纳米管载荷传递效率的影响，分析了出现倒置现象的原因，并针对复合材料塑韧性差的问题，提出了调控思路，为制备强度高、韧性强的碳纳米管增强铝基复合材料提供依据。Abstract: With the continuous improvement on the preparation process of the carbon nanotube-reinforced aluminum matrix composites, the difficult dispersion problem of the carbon nanotubes has been properly solved, and the composite strength has been improved, but the high modulus and high strength of the composites have not been fully utilized, and the “strength-plastic” inversion phenomenon has appeared. The adjustment methods of interface structure, grain structure, and composite configuration design of the carbon/aluminum composites in recent years were summarized in this paper, the influence of interface structure strength on the load transfer efficiency of the carbon nanotubes was discussed, the causes of inversion phenomenon were analyzed, and the control ideas were proposed to solve the problem of poor plastic toughness of the composites, providing the basis for preparing the carbon nanotube-reinforced aluminum matrix composites with high strength and toughness.
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Key words:
- carbon nanotubes /
- aluminum matrix composites /
- interface strength /
- interface control /
- grain control
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图 1 基体–增强体界面结构示意图：（a）I型；（b）II型；（c）III型
Figure 1. Schematic diagrams of the interface structure between the matrix and reinforcements: (a) type I; (b) type II; (c) type III
图 3 原始碳纳米管和包覆SiC碳纳米管的滴铝接触角测量（真空、800 ℃）[10]：（a）光学形貌；（b）原始碳纳米管滴铝接触角；（c）包覆SiC碳纳米管滴铝接触角
Figure 3. Contact angle measurement of the pristine CNTs pellet and SiC/CNTs pellet after the sessile drop of aluminum at 800 ℃ in vacuum[10]: (a) optical image; (b) contact angle measurement of the pristine CNTs pellet; (c) contact angle measurement of the SiC/CNTs pellet
图 7 碳纳米管在硼酸溶液中的吸附机理（a），CNTs@H3BO3混合粉末扫描电子显微形貌及能谱分析（b）～（b3）以及对选定区域元素的成分分析（c）[24]
Figure 7. Mechanisms of the CNTs adsorption in boric acid solution (a), the scanning electron microscope (SEM) image and the corresponding energy spectrum analysis of the CNTs@H3BO3 hybrid powders (b)～(b3), and the element component analysis in the selected area (c)[24]
图 10 原料、碳纳米管–硅粉混合物及CNTs/SiC复合粉末显微形貌[46]：（a）纳米硅粉；（b）碳纳米管；（c）CNTs–Si粉末混合物；（d）～（f）热处理后5CNTs–1Si、5CNTs–3SiC和1CNTs–1SiC复合粉末；（g）～（i）1CNTs–1SiC复合粉末显微结构及相应区域的碳、硅元素分布
Figure 10. SEM images of the raw materials, CNTs–Si powder mixtures, and CNTs/SiC composite powders[46]: (a) raw Si nano-powders; (b) raw CNTs powders; (c) CNTs–Si powder mixtures; (d)~(f) 5CNTs–1Si, 5CNTs–3SiC and 1CNTs–1SiC composite powders after heat treatment; (g)~(i) microstructure of the 1CNTs–1SiC composite powders and the corresponding carbon and Si element distribution
图 16 不同晶粒结构CNTs/Al–Cu–Mg复合材料典型工程应力–应变曲线（a）和三峰晶粒结构CNTs/Al–Cu–Mg复合材料屈服强度–延伸率关系（b）[28,57-68]
Figure 16. Representative engineering stress-strain curves of the CNTs/Al–Cu–Mg composites with different grain structures (a) and the relationship between the yield strength and elongation of the CNTs/Al–Cu–Mg composites with different grain structures (b)[28,57-68]
表 1 含有质量分数1.5%碳纳米管的CNTs/Al复合材料拉伸性能[52]
Table 1. Tensile properties of the CNTs/Al composites with 1.5% CNTs (mass fraction)[52]
材料 球磨方式 最终拉伸强度 / MPa 均匀延伸率 / % 平均晶粒尺寸 / nm 总延伸率 / % CNTs/Al 低速球磨 367±2 3.2±0.1 337 6.3±0.4 变速球磨 376±3 3.9±0.2 308 12.4±1.3 高速球磨 408±1 1.5±0.0 217 4.0±0.3 
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表 2 Al及CNTs/Al复合材料的晶粒结构参数和力学性能[57]
Table 2. Structural parameters and mechanical properties of the Al and the CNTs/Al composites[57]
材料（体积分数） 平均晶粒宽度 / nm 平均晶粒直径 / nm 抗拉强度 / MPa 均匀延伸率 / % 断裂延伸率 / % Al（350 ℃） 443 881 233±2 5.3±0.2 17.4±0.9 Al（320 ℃） 326 510 284±1 3.5±0.3 13.7±0.8 Al（300 ℃） 295 463 298±3 2.5±0.3 11.6±1.3 1%CNTs/Al（350 ℃） 438 832 269±6 5.2±0.3 15.3±0.8 2%CNTs/Al（350 ℃） 426 756 315±2 5.1±0.2 11.1±0.6 1%CNTs/Al（320 ℃） 308 573 315±5 3.2±0.3 12.6±1.1 2%CNTs/Al（350 ℃） 297 435 355±2 3.6±0.1 14.8±1.0
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