Cooling of aluminum plate, cylinder and sphere induced by heat transfer was simulated by use of direct solving method of differential equation. Representative sizes of the plate, cylinder and sphere as well as heat transfer coefficient were varied in the simulation. The results of simulation showed that the cooling rate of surface in Newton’s raw was the ratio of surface area times transfer-induced heat flux to volume times specific heat. Difference in temperature between center and surface was found to be a half Biot number multiplied by the surface temperature in common among plate, cylinder and sphere. Temperature distribution between center and surface was found to be always parabola, the top of which lie at center, causing smooth heat conduction within the volume. Difference between the present result of simulation and Heisler Chart was also made clear.

Thermoelectric properties of a cubic quasicrystalline approximant in Al–Cu–Ir system were investigated experimentally and theoretically. A homogeneous sample with no secondary phase was synthesized using an arc-melting and a spark-plasma-sintering processes followed by heat treatment at 1173 K, and its thermoelectric properties were measured at temperatures between 373 K and 1023 K. Theoretical calculations of the thermoelectric properties were performed under three different approximations, i.e., constant-relaxation-time, constant-mean-free-path, and constant-diffusion-coefficient approximations, for the energy dependence of the relaxation time of the electrons. The experimental Seebeck coefficient was well reproduced, and physically acceptable lattice thermal conductivity was estimated only under constant-diffusion-coefficient approximation for the present material. Thermoelectric figure of merit zT of the present sample was lower than 0.1, and the maximum value of zT ≈ 0.3 achievable by electron doping was predicted by the theoretical calculation under the rigid-band approximation.

The effect of oxygen addition on the spinodal decomposition and hardness variation of α″ martensite during aging in the Ti-4at%Mo alloy was investigated.Ti-4at%Mo-(0, 1.0, 1.5 and 3.0)at%O alloys were arc-melted. The alloy ingots were homogenized at 1473 K for 3.6 ks and then hot-rolled at 1123 K into a 1.5 mm thick sheet. Specimens were solution-treated at 1473 K for 0.6 ks and then quenched in iced brine. The solution-treated specimens were aged at 773 K for up to 86.4 ks. The addition of 3.0at% oxygen in the solution-treated Ti-4at%Mo alloy increased hardness about 200 Hv. The hardness of the alloys during aging at 773 K increased and then decreased showing maximum. The maximum hardness decreased as increasing in oxygen content in the alloy. A modulated structure formed in the α″ martensite laths during aging due to spinodal decomposition. The wave length of modulated structure by spinodal decomposition increased as increasing in oxygen content of the alloy, resulting in decrease of maximum hardness. Oxygen addition in the alloy suppressed spinodal decomposition due to increase of elastic energy for decomposition.

The amount of undercooling required for the nucleation of (β-Sn) in Sn-6.0 mass%Zn alloy was found to be extraordinarily small compared with other Sn-based alloys. One reason for this may be that the solute Zn is oxidized during the process to form ZnO, and this may assist the nucleation of (β-Sn). The disregistry between ZnO and (β-Sn) was analyzed. It was found that crystalline ZnO may be effective for nucleation of (β-Sn), since the disregistry is small. In order to test the nucleation effect of ZnO on β-Sn, dipping experiments were carried out. ZnO powder used in this study was analyzed by X-ray and found to be crystalline. Pure Sn and Sn-2 mass%Ag alloy were chosen as test metals and the undercooling for nucleation of (β-Sn), ΔT, was characterized. It was found that ΔT was large regardless of whether ZnO was dipped in the Sn alloy melt. This indicates that ZnO may not be effective for the nucleation of (β-Sn). Therefore, it can be concluded that low disregistry is a necessary condition but does not ensure nucleation.

The microstructure of oil color named yellow ocher has been investigated. The purpose is to obtain basic data of material properties, and for conservation and restoration of an oil painting. The four specimens used are yellow ocher made in the United Kingdom (specimen A), the French republic (specimen B) and Japan (specimens C and D) on the market. After the color specimens were dried for a year, the specimens are analyzed using an X-ray diffractometer, scanning electron microscope, energy dispersive X-ray spectroscope, and transmission electron microscope. The thin film used for transmission electron microscope observation is thinned in a focused ion beam apparatus. By means of X-ray diffractometry, goethite (αFeOOH), quartz (SiO₂), kaolinite, and muscovite are detected from specimen A, goethite is detected only from specimen B, and goethite and calcite (CaCO₃) are detected from specimen C and D. Colored mineral is goethite and the other minerals detected are colorless minerals. The other trace elements, for example, Mg, Al, and S are detected. It is thought that a part of O detected is introduced into the oil by oxidative polymerization. Acicular grains and aggregation of very fine grains are observed in specimen A by means of transmission electron microscopy. The length and width of the acicular grain are 0.2-0.8 μm and 50-200 nm, respectively, and the grain size is 5-10 nm for aggregated grain. The electron diffraction patterns of these grains indicate goethite. Therefore, color development grain is goethite.