INDEX

NiSi concentration for 9.4µm periodic length and 2.3µm groove depth. The lengths of the x- and y-directions are 75.4µm and 4.7µm, respectively.

Atomic structure during the pressure bonding with groove depths 50 mesh. Chuck velocity was 0.2×10^-4 mesh/step.

Comparison of von Mises stress converted from the ML intensity with that predicted by FE analysis.

The γ band of the rods fabricated at slow and fast scan speed (a) and relationship between the elongation at room temperature and the width of the γ band.

Cross-sectional SEM-EDS results of core-shell structured Ti-N powder and changes in the friction coefficient of Ti-N alloys fabricated by PM process.

Mapping of T_c in an Al-Ti-O triangle, predicted by machine learning based on about 14 000 superconductor dataset, including cuprate and iron based superconductors.

Adding 0.3%N to pure titanium enhanced both strength and ductility through increasing the strain-hardening rate due to the activation of unusual <c+a> slip systems.

True stress-true strain curves under reverse loadings. The solid and broken lines denote the results in the rolling and transverse directions, respectively.

Change in angle between vertebrae in a spine fixed with rods possessing Young’s modulus of 110 GPa throughout and those possessing Young’s moduli of 110 GPa in S1~L3 part and 60 GPa in L3-L2 part, when movable displacement is applied during daily activities.

Appearance, X-ray CT images and fracture surfaces of bonded specimens. Arrows in X-ray CT images indicate areas where polycarbonate has penetrated into the pores of porous aluminum.

Photographs of light heating and press working processes.

Obtained Sample Ⅰ, Ⅲ, and Ⅴ: (a)- (c) top appearance, (d)- (f) side appearance, and (g)- (i) cross-sectional X-ray CT images.

The steady state voltage during constant current anodization decreased with an increasing amount of propanol regardless of the isomer type and the current density.

Macrostructures of Al-25Si ingots. S_950-① reference specimen (neither current nor magnetic field applied), S_950-② (DC current 100A and magnetic field applied), and S_950-③(DC current 130A and magnetic field applied). Imposition of electromagnetic force began at 950 ℃.

Appearance of sheet metal and FEA model.

|G⊥| (phason momentum) dependences of full width at half maximum (Δq)_FWHM of the X-ray peaks for the as-grown sample (A), no compressed sample (B), and the compressed samples with stress of 200 (C), 300 (D), and 400 (E) MPa.

Measured and simulated peaks are compared for stress of 400 MPa (top), 300 MPa (middle), and 0 MPa (bottom) compressed samples, while M=-0.015, -0.01 and 0 were used for the simulations, respectively.

Creep curves recorded at 600 ℃ and 137 MPa for the SLM and forged samples. Creep life is governed by the grain size. A reduction of the porosities by HIP improved the creep rupture life.

Creep curves were recorded at 600 ℃ and 137 MPa for the PBF-LB and forged samples together with the previous study. The creep strain was smaller in the furnace-cooled sample with large volume fraction of the α phase and high Nb contents in β phase, but the effect of the lamellar spacing was small. Heat treatment at 1100 ℃ in β phase effectively improved creep life.

Au-added TiO₂ layers were fabricated by using a combination of Au-sputtering and thermal oxidation of Ti. These layers exhibited higher antibacterial activity under visible-light irradiation, and they also had excellent bonding strength with Ti substrates.

Effect of solution pH used in the conversion treatment on the number of localized corrosion damages on as-polished and conversion-treated AA5083 after galvanic current and potential measurements.

Potentiodynamic anodic and cathodic polarization curves of as-polished and conversion-treated bulk Al₆(Fe, Mn) in the naturally aerated diluted synthetic seawater at pH 8.2 (298 K). The solid and dashed lines indicate the anodic and cathodic polarization curves, respectively.

Optical microscope images of a small area composed of αand βphases (α/ βphase boundary) during the long-time immersion (1 h).

Time variations of the discolored area of the Al matrix around (a) Al-Fe-Si and (b) Al-Fe particles and the Y value of (c) Al-Fe-Si and (d) Al-Fe particles during the OCP measurements in 0.1 M NaCl (pH 6.0).

Representative microstructure and nominal stress-strain curves of hot-extruded Al/ Mg₂Si composites.

TEM images showing the microstructure around Al/graphite interfaces in (a) SPSed sample and (b) HEed sample without rotation.

Results of tensile tests of the samples DRFed at various forging stresses. The ultimate tensile strength (UTS) tended to increase with increasing forging stress. UTS over 400 MPa can be achieved.

Effect of shear strain components on equivalent strain. (a) orientation map, (b) equivalent strain, (c) strain along the tensile direction, ε_z , (d) γ_yx shear strain and (e) γ_zx shear strain.

The concept of pre-deformed Al-Ti refiners with fragmented Al₃Ti (D0₂₂) heterogeneous nucleation site particles and refiners containing L1₂ modified (Al1−_xMe_x)₃Ti heterogeneous nucleation site particles.

Negative to positive strain rate sensitivity of aluminum alloy 2024 plate was confirmed just after solution heat treatment. Parameters of material model were determined.

Relation between the yield stress and the inverse of the square root of (a) lamellar thickness and (b) colony diameter in directionally solidified Al/Al₂Cu mille-feuille structured crystals.

Temperature–concentration diagram of the nucleation barrier in the Al-Cu system. The black, red, and blue surfaces represent the nucleation barriers of the GP1, GP2, and θ′ precipitates, respectively.

Liquid miscibility gap estimated by the thermodynamic calculation and solidification microstructure of the rapidly-solidified Al-Co-La-Bi alloys.

Relation between stress amplitude (σ _a) and number of cycles to failure (N) for the un-treated and various surface treated specimens.

Relation between stress amplitude (σ _a) and number of cycles to failure (N) for the four types of specimens.

Relation between stress amplitude (σ _a) and number of cycles to failure (N) for the un-treated, Ni-P low-P type-plated, high-P type-plated and zinc plated specimens.

Fig. 5 Load-displacement curves of the three alloy substrates un-treated and plated in the three ways, subjected to the three-point bending test.

Relations between stress (σ) and number of cycles to failure (N) for specimens; ●plated or ○not plated after furnace-cooling.

Inverse pole figure (IPF) maps of RD, grain boundary (GB) maps, and phase maps of the RD-ND planes (center) of the composite samples processed by 5, 8 and 11 ARB cycles.

SEM morphologies, XRD diffraction patterns, and Vickers hardness values of the various layers and interfaces of the FGC.

Hardness variation of the HPT-processed samples of (a) Al4Cu1.5Mg, (b) Al4Cu3Mg and (c) Al5Cu3Mg alloys during aging at 423 K.

Crystal models and calculated hydrogen trapping energies from DFT calculations. A magnified image of the most strongly hydrogen-trapped site in each model is shown.

The load-displacement curves of the tensile shear tests and the corresponding microstructure of the nuggets of the C1020/SUS304 dissimilar resistance welded plates.

Before transfer learning, there are (a) source and (b) target domains. (c) By selecting useful source classes, discriminative representations can be learned.

Hydrogen release during SSRT of 7075-T6 aluminum alloys (a): Zn-plating (wet), (b): anodized (wet).

Outer diameter before and after reaching maximum strength and welding area of each joint.

Microstructure of the rods fabricated at high and low input energy density (a) and variations in the yield stress and elongation at room temperature of the rods as a function of the width of the γ band.

(a) Shape change of U-bent specimen of Ti-10V-2Fe-3Al alloy during temperature increase to 400℃.
(b) Shape change of U-bend specimen during holding at 420℃ for 1 hour after the temperature rise in (a).

3D perspective view of Al₇Cu₂Fe particles, Mg₂Si particles and voids captured at the ε_a of 4.2% in the specimen with high hydrogen concentration. Al₇Cu₂Fe, Mg₂Si, and voids(pores) are shown in light blue, gray, and red, respectively. The aluminum matrix is not displayed.

Cylindrical cup drawing was simulated by using the proposed TGC model. The simulation accurately predicted the cup height.

Nitrogen maps for sintered compacts fabricated from gas-nitrided powders, as measured by EPMA.

Figure HRTEM image of the Mg–2.8 mass% Ca alloy aged at 423 K for 3 h, taken with B = [11-20]_α (a). The C14–Mg₂Ca precipitate was taken with B = [1-21-3]_α (b).

Figure HRTEM images, taken with B=[1213]_C14, of the α-Mg/C14–Mg₂Ca eutectic alloy creep- ruptured at 473 K under a stress of 40 MPa. The dislocations are visible within the C14–Mg₂Ca lamella in (a) and (b) as shown by white arrowheads, while they are not observable in (c). The dislocation alignment is detected within the α-Mg lamella as shown by an arrowhead in (c).

Distribution of cumulative plastic shear strain and predicted fatigue crack initiation life.

Fig. Relationship between friction coefficient and wear amount. The Fe-rich specimens showed reduced wear compared to the peened specimens without Fe (Gl series) and smooth ones. However, in some cases, the Fe-rich ones exhibited accelerated wear unexpectedly.

Fig. 1 Surface roughness of samples processed using MFC as function of number of round trips.

Fig. 2 Hardness of samples processed using MFC as function of number of round trips.

Fig. 3 Residual stress for various alloy samples processed using MFC as function of number of round trips. (a) Front surface and (b) back surface.

The microstructures, mechanical properties, and biocompatibility of α+β-type Ti-xNb-yO alloys were investigated. The Ti-5Nb-(0.5–0.75)O alloys had higher elongation and strength and comparable cytotoxicity than Ti-6Al-4V alloy.

Microstructure observation of AlCrN and Nitriding dies by EBSD (Extrusion conditions: billet temperature 450 ℃, ram speed 1.0 mm/s).

SEM microstructure (BEC) of Al–10vol% (Al_2.5Cu_0.5Ti) specimen fabricated by SPS and heat treated at 650 ℃ for 3, 5, and 10min, respectively.

Dark field STEM images of interfacial microstructure for explosively welded AZ80/A6005C cladding plates ((a) as welded, (b) annealed at 373 K and (c) annealed at 473 K for 86.4 ks). WD: Welding Direction.

Transmission electron microscopy bright field (TEM-BF) images and selected area electron diffraction (SAED) patterns of the rapidly-solidified melt-spun ribbons of examined alloys in this study.

The typical creep curves of the duplex LAZ941 alloy before and after heat treatment.

The inverse pole figure maps, the pole figures, and the creep curves of the AZ31 alloys before and after PCA process.

Corrosion initiates at crack sites in the HAp and PEG-HAp coating layer propagates as the coating is peeled off. The PEG modification inhibits the corrosion propagation.

Polarization curves of A6061 and A1050 in 20 mass% NaCl solutions at different temperature.

We fabricated sticky and slippery superoleophobic aluminum surfaces, measuring more than 150° in the advancing contact angle of dodecane, via electrochemical etching and anodizing.

Critical void growth rate at tested temperature of RT and 83 K as a function of stress triaxiality in AZ31Mg alloy and fractographs observed on notched round bar specimen with notch-root-radius of R =1 tensile-tested at RT and 83 K. (Vertical direction to a display surface is corresponding to tensile direction).

Comparison of corrosion rates of various alpha/beta and beta type- titanium alloys in Hank’s solution.

Principle of excellent biocompatibility of titanium from the viewpoint of its surface.

Bonding method of laminated sheet by shot peening. Dissimilar material is a laminated sheet composed of ceramic powders and the resin sheets.

Appearances of cutting side wall of five-layer clad cup. There was a gap in the side wall, and a regular wave shape was observed.

Microstructures and stress-plastic strain curves of Ti-6Al-2Sn-4Zr-2Mo-Si alloy having the (α+α’) duplex microstructures.

Ideally ordered anodic porous alumina formed on the AK substrate with a convex lens shape.

Anodic porous alumina with gradient hole sizes.

Fig.(a) shows XANES spectra near Sn-K edge of Sn added Al-Mg-Si alloys and Fig.(b) shows the enlarged view of the area enclosed by the red dotted line in Fig.(a). For NA times from 0.6ks to 36ks, the absorption edge energy shifted 0.6eV to the lower energy side.

Relationship between XANES and calculated normalized difference absorption edge spectra for Si-K edge from 0.3ks to 2.7ks of aging at 353K. The baseline for the XANES normalized difference absorption edge spectra is the AQ spectrum and that for the calculated one is the Si-Va spectrum.