The purpose of this study is to investigate the influence of Nb content of Ti-xNb-7Al alloys (x=20-35 mass%, abbreviated as xNbA) on β (bcc)→α″ (orthorhombic) transformation with tempering through microstructure, isothermal age-hardening, and shape change of a U-shaped specimen with heating. Full α″-martensite structure was obtained on the quenched 20 NbA. With increasing of Nb content, residual β-phase increased, and single β-phase was obtained in the alloys of more than 25 NbA. From the result, the M_S temperature commonly decreases with increasing of Nb content. The hardness of 20 NbA and 23 NbA rapidly increased in a few seconds by isothermal aging at 450°C, and the hardness of the alloys of more than 25 NbA abruptly increased after an incubation period for 30-60 s. No compositional distribution between α″ and matrix in the aged 23 NbA was found by STEM-EDS analysis, but the obvious distribution of Nb was detected in 35 NbA. U-shaped specimen of 20 NbA exhibited no shape change by heating. On the other hand, the specimen of 23 NbA composed of β+α″ phases showed the shape recovery (SR) first due to work induced α″→β inverse transformation, then deformed toward the bending direction (SA: shape advance) due to β→α″ transformation. The specimens of more than 28 NbA composed of single β-phase exhibited only SA without SR. The starting temperature of SA (M_SA: β→α″) with heating increases with increasing of Nb content. Merging M_S (upper) and M_SA (lower), it is proposed that the whole M_S of xNbA alloy forms a bow shape curve. It is suggested that the low Nb alloys inside the M_S curve transform immediately without atom diffusion by tempering at 450°C, but the higher Nb alloys outside the curve need an incubation period to distribute Nb concentration with atom diffusion, and martensitic α″ transformation will abruptly occur in the local domains less than 25 NbA which is the inside of the curve.

In this study, thermal fatigue tests at maximum temperature 1073 K were performed using 13%Cr-Nb-Si and 18%Cr-Nb-Mo steels as representative heat-resistant ferritic stainless steels for automotive exhaust systems. The changes in the microstructure, the crystal orientation and the hysteresis loop during thermal fatigue in the temperature range from 473 K to 1073 K were investigated. As a result of comparing thermal fatigue life under these conditions, 18%Cr-Nb-Mo steel with high temperature strength was found to have a longer thermal fatigue life than 13%Cr-Nb-Si steel. During the thermal fatigue process, the material was softened by reducing of the amount of solute Nb, and the coarsening of Nb precipitation. By this softening, the form of the hysteresis loops changed with the increase in cycles. By considering the softening of the material, the change in the hysteresis loops could be predicted to some extent. Furthermore, by EBSD analysis, it was recognized that the dynamic recovery and recrystallization accompanied by the uniaxial and fine grain formation occurred during the thermal fatigue process. From the viewpoint of change of the microstructure, the thermal fatigue damage was quantified by the ratio of the low-angle grain boundary, and the change of this index with the progress of the cycle in 18%Cr-Nb-Mo steel had a smaller than 13%Cr-Nb-Si steel. It was thought that this point was caused by the retardation of recrystallization by solute Mo.

The dislocation structures in polycrystalline Fe-1 mass% Si after cyclic deformation were observed using high voltage electron microscopy in order to investigate the formation mechanism of the dislocation structures. Vein, wall, and cell structures were found in a deformed specimen. Detailed orientation and structure of the walls were analyzed. Burgers vectors of dislocations in the walls were a/2[111] and a/2[1  11]. A set of walls was arranged parallel to the (110) plane and it was found to be a part of labyrinth structure consisting of the (110) and (001) walls. It is suggested that the formation mechanism of the labyrinth structure in bcc metal is reasonably understood by extending the mechanisms in fcc metals.

The interface-precipitation has been observed as row carbide arrange since 1960’s. Whereas the interface-precipitated carbides in steels were NbC, TiC, VC and Cr₂₃C₆ in the early stage, composite TiC containing Mo and W has been also become to observe recently. Several kinds of the mechanism of the interface-precipitation have been suggested and ledge mechanism and bowing mechanism which combined interface barging and carbide precipitation are widely accepted since the mechanisms successfully explained a large amount of the experimental results. Fine interface-precipitates in low carbon steel realize high strength steel sheets, plates, bars and rods which are non-quenched and tempered. Especially, in sheet products, in which fine carbides can be easily generated, ferritic steel of 1180 MPa in tensile strength is successfully obtained by dispersing fine carbides with the diameter of several nano-meters.

The viscosities of the lead-free solders are important to simulate the process of the manufacturing process. In this article, current status of the viscosity measurements for the lead-free solders are reviewed. In addition, we introduced the current work of the viscosity measurements for the lead-free solders by using the rotational viscometer with concentric cylinder spindle geometry.