Effect of the solid-state transition of Fe–C phase on the friction and wear behavior and mechanism of Cu–(Fe–C) alloys
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摘要: 采用光學顯微鏡（OM）、掃描電子顯微鏡（SEM）、納米力學探針、力學性能測試以及室溫摩擦磨損實驗研究了Cu–(Fe–C)合金的鑄態組織、形變態組織、Fe–C相形貌、力學性能和摩擦磨損行為。結果表明，Cu–(Fe–C)合金中彌散分布著微米級和納米級的Fe–C相，其中微米級的Fe–C相在淬火和回火過程中發生了固態轉變，這種固態轉變與鋼中的馬氏體轉變和回火轉變類似。合金先在850 ℃淬火，然后在200、400和650 ℃回火，Fe–C相由針狀馬氏體逐漸向顆粒狀回火索氏體轉變，Fe–C相納米硬度分別為9.4、8、4.2和3.8 GPa，實現了對強化相硬度的控制。室溫摩擦磨損實驗結果表明，隨著回火溫度升高，合金的磨損機制逐漸由犁削向黏著磨損和大塑性變形轉變，導致合金的耐磨損性能降低。這一結論可以為通過Fe–C相的固態轉變的方法調控Cu–(Fe–C)合金的摩擦磨損性能提供參考作用。Abstract: The effect of solid-state phase transformation during heat treatment on the friction and wear properties of Cu–3Fe–0.18C alloy prepared by vacuum melting was studied. The as-cast structure, deformed structure, Fe–C phase morphology, mechanical properties, and the friction and wear behavior of Cu–Fe–C alloy were studied by optical microscopy (OM), scanning electron microscopy (SEM), nano-mechanical probe analysis, mechanical properties test, and friction and wear experiments, respectively, at room temperature. The results show that micro- and nano-sized Fe–C phases are dispersed in the Cu–(Fe–C) alloy, and the micron-sized Fe–C phase undergoes solid-state transformation during quenching and tempering, which is similar to the martensite transformation and tempering transformation in steel. After quenched at 850 ℃ and tempering at 200, 400 and 650 ℃, the Fe–C phase gradually transforms from acicular martensite to granular tempered sorbite. The corresponding nano-hardness of the Fe–C phase is 9.4, 8, 4.2 and 3.8 GPa, respectively, and the hardness of the strengthening phase is controlled. Through an analysis of tensile fracture, a large number of dissociation surfaces appear on the fracture surface of the quenched alloy. The crack source is located at the interface between the Fe–C phase and the matrix. With an increase in the tempering temperature, the dissociation surface of the fracture surface of the tempered alloy gradually decreases until it disappears, and the crack source gradually transfers to the matrix. The evolution of fracture surface indicates that the bonding between Fe–C phase and matrix in the quenched alloys is poor. With the increase of the tempering temperature, the bonding interface between the Fe–C phase and the matrix is improved. The experimental results of friction and wear at room temperature show that with the increase of tempering temperature, the wear mechanism of the alloy gradually changes from ploughing to adhesion wear and severe plastic deformation, which results in a decrease in the alloy wear resistance. This paper can provide a reference for controlling the friction and wear properties of Cu–(Fe–C) alloys by the solid-state transformation of the Fe-C phase martensitic decomposition.
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圖 1 Cu–Fe–C合金的鑄態組織。（a）低倍光學顯微鏡照片；（b）高倍光學顯微鏡照片；（c）晶粒細化后的組織；（d）SEM圖像
Figure 1. As-cast structure of Cu–Fe–C alloy: (a) low power optical microscope photos; (b) high power optical microscope photos; (c) grain refined structure; (d) SEM image
圖 2 Cu–(Fe–C)合金熱處理后的SEM像。（a）淬火態；（b） 200 ℃回火態；（c） 400 ℃回火態；（d） 650 ℃回火態
Figure 2. SEM image of Cu–(Fe–C) alloy after heat treatment：(a) quenched；(b) tempered at 200 ℃；(c) tempered at 400 ℃；(d) tempered at 650 ℃
圖 4 不同回火溫度下Cu–Fe–C合金的抗拉強度和硬度
Figure 4. Tensile strength and hardness of Cu–Fe–C alloy at different tempering temperatures
圖 5 不同回火溫度下Fe–C相的納米硬度
Figure 5. Nano-hardness of Fe–C phase at different tempering temperatures
圖 6 不同狀態Cu–Fe–C合金拉伸斷口形貌。（a）淬火態；（b） 200 ℃回火態；（c） 400 ℃回火態；（d） 650 ℃回火態
Figure 6. Tensile fracture morphology of Cu–Fe–C alloys in different states：(a) quenched；(b) tempered at 200 ℃；(c) tempered at 400 ℃；(d) tempered at 650 ℃
圖 7 不同狀態Cu–(Fe–C)合金拉伸斷口縱截面形貌。（a）淬火態；（b）200 ℃回火態；（c）400 ℃回火態；（d）650 ℃回火態
Figure 7. Longitudinal section morphology of tensile fracture of Cu–Fe–C alloys in different states: (a) quenched; (b) tempered at 200 ℃; (c) tempered at 400 ℃; (d) tempered at 650 ℃
圖 9 摩擦表面的磨痕三維形貌照片（a）、（b）和縱截面的深度輪廓曲線（c）、（d）。（a）、（c）淬火態；（b）、（d）650 ℃回火態
Figure 9. 3-D morphology of friction surface (a) & (b) and profile of longitudinal section (c) & (d). (a), (c) quenched; (b), (d) tempered at 650 ℃
圖 10 不同狀態合金摩擦表面形貌。（a）淬火態；（b） 200 ℃回火態；（c） 400 ℃回火態；（d） 650 ℃回火態
Figure 10. Friction surface morphology of alloys in different states: (a) quenched; (b) tempered at 200 ℃; (c) tempered at 400 ℃; (d) tempered at 650 ℃
圖 11 不同狀態合金塑性變形層深度。（a）淬火態；（b） 200 ℃回火態；（c） 400 ℃回火態；（d） 650 ℃回火態
Figure 11. Depth of plastic deformation layer of alloys in different states: (a) quenched; (b) tempered at 200 ℃; (c) tempered at 400 ℃; (d) tempered at 650 ℃
圖 12 不同狀態合金加工硬化層深度。（a）淬火態；（b）200 ℃回火態；（c）400 ℃回火態；（d） 650 ℃回火態
Figure 12. Depth of work hardening layer of alloys in different states: (a) quenched; (b) tempered at 200 ℃; (c) tempered at 400 ℃; (d) tempered at 650 ℃
中文字幕在线观看Point Element Atomic fraction/% Mass fraction/% 1 C 73.67 36.13 Fe 14.43 32.90 Cu 11.84 30.72 2 C 17.59 4.17 Fe 53.56 59.31 Cu 28.86 36.52 3 C 10.59 2.45 Fe 80.65 86.82 Cu 8.76 10.73 
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