Papers by Author: Toshitada Shimozaki

Abstract: In general, only one Kirkendall plane can be seen in a diffusion couple. However, bifurcate or trifurcate Kirkendall planes have been reported in Ti/TiAl3 or Co/CoSi2 multi-phase diffusion couples (M-couple) [1,2]. The authors [3] have previously shown a numerical technique to analyze the movement of multiple markers (M-M) embedded in a M-couple taking the molar volume change effect to the diffusion direction into account. Using this technique, one can visualize the places where vacancies (lattice planes) are annihilated or generated in the couple. Here, we try to demonstrate the bifurcate or trifurcate Kirkendall planes in the M-couple and clarify the limited conditions of bifurcate or trifurcate Kirkendall planes by using this numerical technique.

Abstract: The movement of multiple markers (M-M) embedded in a multiple phases diffusion couple (M-couple) has been numerically analyzed for binary two phases models taking the molar volume change effect to the diffusion direction into account. From the results obtained by this analysis the places where vacancies are annihilated or generated can be visualized. It has been clarified that a part of M-M is necessarily shown by a linear line due to parabolic movement of the inter-phase interface. Some other interesting results obtained in this study will be reported.

Abstract: Oxidation resistance of TiAl3, one of the candidates of coating materials for high temperature structural materials such as Ti3Al and TiAl, has been studied. Specimens were prepared by forming TiAl3 in Al/Ti/Al reaction diffusion couples at 923 K and then TiAl3 layer was exposed to air by dissolving Al plate in a 1N NaOH solution. The obtained TiAl3/Ti/TiAl3 couples were annealed in air in the temperature range from 1173 K to 1468 K. The oxidation rate was compared with that determined by using bulk TiAl3. The present data show a bend on the Arrhenius plot of parabolic phase growth rate constant, k2, at 1323 K. Above 1323K, the constant coincides well with the extrapolated values of bulk data while the value in the lower temperature range is larger than that of bulk specimens. During the oxidation experiments, intermetallic compounds Ti3Al, TiAl and TiAl2 were formed between Ti and TiAl3. Interdiffusion coefficients in the Ti3Al, TiAl phases determined from these diffusion couples are more than one order of magnitude larger than the interdiffusion coefficients determined by previous investigators from single-phase diffusion couples but coincide with the coefficients determined from multi-phase diffusion couples. This difference between interdiffusion coefficients has been discussed and explained by the effect of boundary diffusion in the diffusion layers formed in the multi-phase diffusion couples.

Abstract: Interdiffusion in Fe/Pt multilayer thin films has been studied. [Fe(1nm)/Pt(1.5nm)]20 multilayers were prepared by DC magnetron sputtering technique and subsequently annealed at temperatures of 543 - 633K in vacuum lower than 10-6 torr. X-ray diffraction (XRD) studies on these multilayer systems revealed the interdiffusion coefficients from slope of the best straight line fit of first peak intensity versus annealing time. The temperature dependence of interdiffusion in the range of 543 - 633K can be described by D=4.98×10-24 exp (0.88eV/kT) m2S-1. The coercivity, measured by Vibrating Sample Magnetometer, of the multilayer with annealing time at 603K increased, which is believed to the increase of surface roughness by interdiffusion at the interfaces of Fe and Pt multilayers, enhancement of composition gradient; and/or formation of Fe-Pt reaction phase at the interface of Fe and Pt.

Abstract: The impurity diffusion coefficients of Cu in Fe have been determined in the temperature range of 1073 - 1163 K by means of Laser Induced Breakdown Spectrometry (LIBS). The volume diffusion coefficients for Cu impurity diffusion in a-iron found in this work are in good agreement with the previously published result. The grain boundary diffusion coefficient gb D s d was also calculated using the volume diffusivity and processing the tails of the measured profiles. The values of the activation energy for volume and grain boundary diffusion were approximately 280 and 161 kJmol-1, respectively. This indicates the possibility of a monovacancy diffusion mechanism in case of volume diffusion. The results for the diffusion coefficients are Dv= 2.2 ×10-2exp(-280 kJmol-1/RT) m2s-1 and gb D s d = 2.6 ×10-11exp(-161 kJmol-1/RT) m3s-1.