The aligned film of amorphous carbon (a-C) nanorods was prepared by catalytic chemical vapor deposition (CCVD) on an anodic aluminum oxide (AAO) template at 650 8C. The morphology and microstructure of aligned film of amorphous carbon nanorods were examined by scanning electron microscopy (SEM) and Raman scattering spectroscopy. The friction and wear properties of aligned film of amorphous carbon nanorods on the AAO template in vacuum (1.12

Ni-P-Carbon nanotube (CNT) composite coatings as well as Ni-P-SiC and Ni-P-graphite coatings were prepared by electroless plating. The tribological properties of these composite coatings were investigated using a ring-on-block test rig under lubricated condition. The Ni-P-CNT composite coatings exhibited not only high wear resistance but also low friction coefficient compared with the Ni-P-SiC and Ni-P-graphite composite coatings. The favorable effects of CNTs on the tribological properties of the electroless coatings are attributed to improved mechanical properties and unique topological structure of the hollow nanotubes. In addition to preventing the rough contact between the two mating metal surfaces, the shorter CNTs can easily slide or roll within the surfaces of friction pairs. Therefore, the wear rate and friction coefficient of Ni-P-CNT composite coatings can be substantially reduced.

ZnO nanoparticles and nanorods as anode active materials were investigated by charge-discharge cycle measurements. The ZnO nanomaterials with larger specific surface area exhibited higher electrochemical activity than conventional ZnO particles. The discharge capacity delivered by ZnO nanorods exceeded 500 mA hg−1 until the 175th cycle. It also exhibited higher midpoint discharge voltage than conventional ZnO. The morphologies of ZnO had a significant effect on the electrochemical properties of the anodes. In the initial cycles, the morphologies of ZnO did not essentially change due to the extension effect, and the electrochemical performance of the electrodes was relatively stable. With increasing the cycles, according to the texture growth mechanism, the large flaky ZnO parallel to the substrate surface predominated to reduce the electrochemical performance. Due to the intensive extension effect, the growth mode of ZnO nanorods changed. The eventual morphology was erect small flaky ZnO crystals that suppressed the production of Zn dendrite and enhanced the capacity maintenance.

The wear behavior of aged Cu-Cr-Zr alloys dry sliding against a brass counterface were investigated on a pin-on-disk wear tester under electric current conditions. The worn surfaces of the aged Cu-Cr-Zr alloys were analyzed by scanning electron microscope (SEM) and energy dispersive X-ray spectrum (EDS). The results indicated that the aging treatments had an effect on the microstructure, hardness and wear resistance of Cu-Cr-Zr alloy. At the constant current density, the wear rate of Cu-Cr-Zr alloy decreased with aging temperature, and reached the minimum at 500℃, then increased with further increasing aging temperature. An appropriate aging treatment may improve the wear resistance of the materials due to the formation of fine, dispersive and coherent precipitates within the matrix. An increase in electrical current resulted in an increase in wear rate of both the Cu-Cr-Zr alloy pin, and the brass disk. Adhesive wear, abrasive wear and arc erosion were the dominant mechanisms during the electrical sliding processes. Compared with commercially used Cu-Ag alloy wire (CTHA110) under the same test conditions, the Cu-Cr-Zr alloy treated at 500℃ for 2 h exhibited much better wear resistance.

Steady-state friction and wear behaviour of as-cast and T6-treated hypoeutectic Al-Si-Mg-matrix composites reinforced with 19.5 vol.% of Al18B4O33 whiskers dry sliding against 5CrNiMo steel counterface have been investigated as a function of applied load and sliding speed. Owing to the severe interfacial cracking and fracture of whiskers which occurs under higher applied load conditions, the composites exhibited a transition from mild wear to severe wear over the applied load range from 45 to 230 N. By comparison with the as-cast composite, the T6-treated composite, with reduced whisker strength and weak whisker/matrix inter-face, had relatively low wear resistance. Under low applied loads, increasing sliding speed caused deep surface damage, thus indu-cing an increase in wear rate and coefficient of friction. As the sliding speed further increased, the formation of a mainly Al2O3 transfer layer on the worn surface and the strain-hardening of the subsurface layer contributed to decreases in wear rate and coef-ficient of friction of the composites.