Zhenying Huang

Oxidation layer in sliding friction surface of high-purity Ti3SiC2

It has been shown in the last few years that the ternary carbide Ti3SiC2 has an excellent combination of properties in electric and thermal conductivity, refractoriness, oxidation resistance, damage tolerance, stress-strain characteristics and machinability [1–4]. Such unusual combination suggested it could be used as tribological materials. Myhra et al. [5] measured the kinetic friction coefficient of the basal planes of Ti3SiC2 to be as low as 2–5×10−3. But they measured the friction coefficient of a polycrystalline Ti3SiC2 to be 0.12, when it is sliding against a lightly peened stainless steel sheet under a load of 0.15 to 0.9 N. El-Raghy et al. [6] investigated effects of grain size on the friction and wear for a high-purity Ti3SiC2 sample sliding against a 440C steel pin in pin-on-disk type tests, under 5 N normal load, 0.1 m/s sliding speed and 46.3 m sliding distance. The results showed that irrespective of the grain size, the steady friction coefficient is about 0.83, being almost 7 times the value measured by Myhra et al. [5]. Sun et al. [7] studied the friction and wear behavior of a Ti3SiC2-based material contained ∼7 wt% TiC phase, using it as a disk sliding against a AISI 52100 steel pin in pin-on-disk tests, with the test parameters of 7 m/s sliding speed and four normal loads from 7.7 to 14.7 N. The results showed that the steady state friction coefficient increases from 0.4 to 0.5 with increase in the normal load applied. Such large difference in the measured friction coefficient is perhaps related with the friction surface status. In the previous works we found very limited literature on the friction and wear of Ti3SiC2, only Sun et al. [7] noted the presence of oxidation behavior. They observed that the worn surface of the Ti3SiC2-based disk was covered with very fine grains and partially compacted layers, which randomly distribute over the worn surface. They concluded that the debris made up of the Ti3SiC2 disk and steel pin materials was crushed into the fine grains, and sometimes compacted into layers on the Ti3SiC2 disk. However, whether the Ti3SiC2 material itself can be oxidized or not remains a question to date. It has been observed [2, 8] that polycrystalline Ti3SiC2 is oxidizable in air, in the temperature range from 900 to 1400 ◦C. The scale that formed is dense, adhesive, and layered. The outer layer was pure TiO2, and the inner layer consisted of a mixture of SiO2 and TiO2. This suggested that similar oxidation could also occur on the friction surface of a polycrystalline Ti3SiC2, because the real frictional temperature could be enough to induce the Ti3SiC2 oxidization when asperities of the Ti3SiC2 surface were severely impacted with that of the steel disk during sliding friction [9], though the apparent temperature of the entire Ti3SiC2 block may be lower. This idea was verified in the present study for the first time. A high-purity polycrystalline Ti3SiC2 sample was prepared with the following processing. Commercial Ti (70 μm, >99.0% purity), Si (70 μm, >99.0% purity), C (graphite, 50 μm, >98.0% purity) and Al (70 μm, >99.5% purity) powders were mixed with a mole ratio of 3Ti:1Si:2C:0.2Al. The mixed powders were ball-milled for 8 hrs in ethanol solution by a rotary drum-type ball-miller. The ball-milled slurry was dried at 60 ◦C. The dried mixture was pulverized with a pestle, and screened through a 100-mesh sieve. The mixture powders were precompressed at 8 MPa in a graphite die, then hot-pressed in the self-same graphite die under 1450 ◦C and 25 MPa pressure for 2 hrs, with flowing argon gas. The heating rate was of 40 ◦C/min, and the cooling rate was of about 10 ◦C/min. The phase composition of the resultant products was analyzed by X-ray diffraction (XRD) with Cu Kα radiation, and the microstructure was observed by a scanning electron microscopy (SEM). The analyzed and observed results are shown in Fig. 1a and b, respectively. The content of Ti3SiC2 phase was estimated to be about 98 vol%, and the average grain size was estimated to be about 5 μm. The frictional oxidation behavior of the Ti3SiC2 sample was examined using a block-on-disk type tester developed by Beijing Jiaotong University. The test principle is illustrated in Fig. 2. The Ti3SiC2 sample prepared was cut into several blocks with dimensions of 10 × 10 × 12 mm. A low carbon steel disk with dimensions of 300 mm in diameter and 10 mm in thickness was used as the counterpart sliding against the Ti3SiC2 block. Tests were conducted at room temperature within a relative humidity of 22–25%. The sliding speed was of 20 m/s, and the normal pressure was changed from 0.1 to 0.8 MPa. The friction surface was observed using the said scanning electron microscopy. The chemical status of the friction surface was analyzed using an energy dispersion spectroscopy (EDS) equipped in the scanning electron microscopy. A general fact we found from the present tests is that all friction surfaces of the Ti3SiC2 blocks were covered by a layer consisting of the frictional products, and that the compactness and roughness of the layer depended on the normal pressure applied. Fig. 3a and b are typical SEM photographs exhibiting the friction surfaces of the Ti3SiC2 blocks, which underwent 24 000 m sliding distance under 0.2 and 0.8 MPa normal pressures, respectively. As could been seen, the layer formed under 0.2 MPa was partially compact, and its surface looked

Fabrication, mechanical properties, and tribological behaviors of Ti2AlC and Ti2AlSn0.2C solid solutions

Highly pure and dense Ti2AlC and Ti2AlSn0.2C bulks were prepared by hot pressing with molar ratios of 1:1.1:0.9 and 1:0.9:0.2:0.85, respectively, at 1450 °C for 30 min with 28 MPa in Ar atmosphere. The phase compositions were investigated by X-ray diffraction (XRD); the surface morphology and topography of the crystal grains were also analyzed by scanning electron microscopy (SEM). The flexural strengths of Ti2AlC and Ti2AlSn0.2C have been measured as 430 and 410 MPa, respectively. Both Vickers hardness decreased slowly as the load increased. The tribological behavior was investigated by dry sliding a low-carbon steel under normal load of 20–80 N and sliding speed of 10–30 m/s. Ti2AlC bulk has a friction coefficient of 0.3–0.45 and a wear rate of (1.64–2.97)×10−6 mm3/(N·m), while Ti2AlSn0.2C bulk has a friction coefficient of 0.25–0.35 and a wear rate of (2.5–4.31)×10−6 mm3/(N·m). The influences of Sn incorporation on the microstructure and properties of Ti2AlC have also been discussed.

Friction Behaviors and Effects on Current-Carrying Wear Characteristics of Bulk Ti3AlC2

The friction behaviors of high-purity bulk Ti3AlC2 against low-carbon steel with or without current-carrying friction and its effect on wear characteristics were investigated. Experiments are performed on a block-on-disk-type friction tester with sliding speeds from 20 to 60 m/s, pressures from 0.4 to 0.8 MPa, and nominal current densities of 0, 50, and 100 A/cm2. The results show that the coefficient of friction increases with increase sliding speed and current density and decreases with increasing normal pressure. The stability of the friction and wear rate of Ti3AlC2 was only slightly affected by the changes in sliding speed and normal pressure in the conditions that without current or low current density. However, it causes a significant impact in the current density of 100 A/cm2. The stability of friction decreases with increasing sliding speed or decreasing normal pressure, and higher stability corresponds to a lower wear rate during the current-carrying friction process. Standard deviations of kinetic friction coefficients, as a characterization of stability, show a strong linear correlation with the wear rate. However, when sliding speeds are higher than 50 m/s or normal pressures are less than 0.5 MPa, the current-carrying wear rate of Ti3AlC2 increases rapidly.