金属铜因具有良好的导电导热性，常被用于电气电子、轨道交通等领域，但由于机械强度及高温性能较差，限制了其在工业及军事领域的应用。本文选用比强度高、高温抗蠕变性能及抗氧化性能优异的金属间化合物Al₃Ti作为增强相，分别采用粉末冶金法和无压渗透法合成Al₃Ti增强铜基复合材料。通过试验对增强体制备方案、复合材料组元配比及熔渗温度、保温时间等工艺参数进行调整优化，研究其对复合材料显微组织、孔隙率以及力学性能等的影响规律。最后对两种方法制备的复合材料进行对比。

首先分别采用冷压与热压成型工艺制备预制体，随后高温烧结合成Al₃Ti颗粒增强体和多孔骨架。结果表明，多孔试样的开孔隙率随冷压载荷增大不断减小。同时，热压成型条件下，高温烧结可获得开孔隙率达74.57%的多孔骨架。而两种成型工艺对物相组成影响较小，始终保持为单一的Al₃Ti相。

随后将冷压成型制备的Al₃Ti颗粒用于粉末冶金法制备铜基复合材料。结果表明，当Al₃Ti和石墨分别为15wt. %和5wt. %时，物相组成中仅包括Cu相及其固溶体、Al₃Ti和石墨，Al₃Ti和石墨始终弥散分布在铜基体上，与基体保持良好界面结合。此时复合材料硬度达145.79 HV_0.5，相比纯铜提高58.76%，摩擦磨损性能最佳，摩擦系数和磨损率相比纯铜分别降低27.27%和71.81%。摩擦磨损试验表明，复合材料摩擦系数和磨损率随Al₃Ti含量增加先减小后增大，磨损机制由粘着磨损、剥层磨损转变为磨粒磨损；随石墨含量增加，摩擦系数先增大后减小，磨损率先减小后增大，磨损机制为磨粒磨损。

最后将热压成型制备的Al₃Ti多孔骨架用作无压渗透法制备铜基复合材料。结果表明，复合材料渗透区宽度随熔渗温度升高不断增大，随保温时间延长先增大后减小，1300°C保温6 h试样渗透区宽度可达1351.90 μm，硬度可达165.91 HV_0.5，相比纯铜提高113.77%。此时显微组织中的灰色颗粒细小均匀地弥散分布在基体上，与基体保持良好的界面结合。然而，无压渗透过程中高的渗透温度导致Al₃Ti发生分解，分解后的Al原子和Ti原子分别向Cu基体扩散形成Cu-Al、Cu-Ti金属间化合物。

在Al₃Ti质量分数为10wt. %时，粉末冶金试样增强相与基体界面结合良好，显微组织中的灰色颗粒为Al₃Ti相，平均尺寸为15.66 μm。1300°C保温6 h的无压渗透试样微观组织中存在的微小孔隙严重影响基体连续性，其中灰色颗粒成分主要为Ti元素，平均尺寸为1.07 μm，相比粉末冶金减小93.17%。此外，无压渗透试样硬度相比粉末冶金试样提高14.48%，粉末冶金试样是通过Al₃Ti增强颗粒的载荷传递强化的，而无压渗透试样是通过Cu-Al、Cu-Ti金属间化合物及Ti颗粒的弥散分布强化的。

Copper is widely used in electrical, rail transport and other fields due to its good conductivity and thermal conductivity, but its poor mechanical strength and high temperature performance limit its application in industrial and military fields. Al₃Ti intermetallic compound with high specific strength, high temperature creep resistance and excellent oxidation resistance was selected as reinforcement phase in this paper. Al₃Ti reinforced copper matrix composites were synthesized by powder metallurgy and pressureless infiltration respectively. The influence of different process parameters on the microstructure, phase composition, porosity and mechanical properties of the composites were studied by adjusting and optimizing the process parameters such as preparation scheme of reinforcement, composition of composites, infiltration temperature and infiltration time. Finally, the composites prepared by the two methods were compared.

The preforms were prepared by cold-pressing and hot-pressing processes respectively, followed by high-temperature sintering to synthesize Al₃Ti particle reinforcement and porous skeleton. The results shown that the open porosity of porous materials decreased with increasing cold-pressing load and high strength porous skeleton with open porosity of 74.57% could be obtained by high temperature sintering under hot-pressing. In addition, the two preform forming processes had little impact on the phase composition and remained as a single Al₃Ti phase.

Subsequently, the Al₃Ti particle reinforcement prepared by cold-pressing was used to prepare copper matrix composites by powder metallurgy. The results shown that when the Al₃Ti and graphite content were 15wt. % and 5wt. % respectively, the phase composition only included copper phase and its solid solution, Al₃Ti, and graphite. Furthermore, Al₃Ti and graphite were always dispersed on the copper matrix, maintaining a good interfacial bonding with matrix. At this time, the hardness of the composite reached 145.79 HV_0.5, which was 58.76% higher than that of pure copper and the wear performance was the best, with the friction coefficient and wear rate reduced by 27.27% and 71.81% compared to pure copper, respectively. The wear tests shown that the friction coefficient and wear rate of the composite first decreased and then increased with the increase of Al₃Ti content, and the wear mechanism changed from adhesive wear and delamination wear to abrasive wear. With the increase of graphite content, the friction coefficient first increased and then decreased, and the wear rate shown opposite trend. The wear mechanism was abrasive wear.

Finally, Al₃Ti porous framework prepared by hot-pressing was used as the pressureless infiltration to prepare copper matrix composites and the width of infiltration zone of composites increased with the increase of infiltration temperature, and increased first and then decreased with the extension of infiltration time. The width of infiltration zone of samples heated at 1300°C for 6 h can reach 1351.90 μm, hardness up to 165.91 HV_0.5, which was 113.77% higher than that of pure copper. At this time, the gray particles in the microstructure were evenly distributed, maintaining a good interfacial bonding with copper matrix. However, Al₃Ti was decomposed due to high infiltration temperature, thus made Al and Ti atoms diffuse to copper matrix to form Cu-Al and Cu-Ti intermetallic compounds respectively.

When the mass fraction of Al₃Ti was 10wt. %, the interfacial bonding between the reinforcement phase and matrix was good and the gray particles were Al₃Ti phase with an average size of 15.66 μm. The existence of micropores in the microstructure of pressureless infiltration sample with insulation at 1300°C for 6 h seriously affected the continuity of matrix, in which the gray particle composition was mainly Ti element with an average size of 1.07 μm, which was 93.17% lower than that of powder metallurgy sample. Furthermore, the hardness of the pressureless infiltration sample was 14.48% higher than that of powder metallurgy. Powder metallurgy specimens were strengthened by load transfer of Al₃Ti reinforced particles, while pressureless infiltration specimens were strengthened by dispersion distribution of Cu-Al, Cu-Ti intermetallics and Ti particles.

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