INDEX

TiO₂ layers, possessing both high bonding strength and excellent antibacterial properties, were successfully formed on practical dental Ti alloys via two-step thermal oxidation.

Distribution of the phase field of the gas phase at 1000 s obtained by proportional control of pulling velocity.

Concentration distribution of Al after 1.4 ms for A = 1.68 μm and λ = 4.7 μm.

Stress amplitude against the inverse extreme FIP per aggregate for (a) slip-induced and (b) twin-induced FIP.

AE amplitude and normalized position at AE hit during fatigue tests of (c) Mg₉₇Zn₁Y₂ alloy and (d) Mg₈₉Zn₄Y₇ alloy. The vertical lines and the adjacent shaded region represent the mean and standard deviation of the transition points determined by MCMC simulation.

Illustration of formation process of calcium phosphate on Ti in Hanks and estimated reaction scheme. The interface between the surface oxide film and calcium phosphate is fuzzy.

(a) Deformation behavior and (b) stress-strain curves of three-layered porous aluminum consisting of AC4CH (70%) / pure aluminum (80%) / A6061 (75%) and corresponding uniform porous aluminum.

Appearance of formed tube when steel ball diameter Φ_b = 15.9 mm.

Simple visualization revealed unusual surfaces with structural gradients that were distinctly different from the structures of uniform films generated by conventional anodization.

Left: controlled potential and resulting current during anodization of thin gold film (100 nm thickness) on sputter-deposited Ti (130 nm thickness) on glass sheet in oxalic acid. Right: cross-sectional SEM image of the sample.

Predicted average diameter and volume fraction of dispersoids, and the corresponding hardness calculated from the two parameters are well agreement with experimental results up to measurable 10000 h. This suggests that the utilized simulation model could enable to predict the unmeasurable terminal strength of the developed P/M alloy extrusions.

Glossiness of the Al layer surface deposited from the AlCl₃/LiAlH₄/dibutyl ether bath containing additives.

Change in slip system of commercial purity Titanium dependent of grain size.

Aging conditions and deformation temperatures dependence of activation volume for plastic flow in Al-Mg-Sc alloys.

Forming limit strain of aluminum alloy A5052-H34 with strain path change under high or low strain rate

The average grain size of the Ti samples and Ti-0.3vol%TiC samples before and after the heat treatment.

Flow diagram for fabrication process of the refiners with L1₂ Modified (Al₁-_xMe_x)₃Ti particles.

Relationship between average grain size and position of macrostructure observation.

High-strength AZ80Mg alloy tube could be successfully fabricated by combined processes of multi-directional forging and warm-temperature extrusion employing superplasticity.

Effect of grain size on the yield strength and total elongation in the pure Mg was divided into three different regions corresponding to the change of the major deformation mode.

Schematic illustration of impression pattern.

XRD patterns of HfNbTaTiZr polycrystals annealed at 673–1173 K for 24 h (a) and stress-strain curves of the HfNbTaTiZr single crystals compressed at different temperatures.

The gradient ratio of α/α₀ and 0.2% proof stress σ_0.2 in Ti-Zr-Fe alloys depending on Zr content. Although the σ_0.2 in as STQ increased with increasing Zr content, the α/α₀ decreased.

The gradient ratio of α/α₀ and 0.2% proof stress σ_0.2 in Ti-Zr-Fe alloys depending on Zr content. Although the σ_0.2 in as STQ increased with increasing Zr content, the α/α₀ decreased.

Microstructure of VGCNF/Al composites in different power dissipation efficiency regions: (a) 673 K-0.01s^-1, (b) 723 K-0.01s^-1, (c) 723 K-1s^-1, (d) 623 K-1s^-1, (e) 573 K-0.1s^-1 and (f) the processing map when the strain was 0.35.

Distribution of dynamic recrystallization fraction by FEM, which is established by dynamic globularization model in terms of JMAK model.

The stepped shape stress-strain curves measured by the dead-weight-type tensile test and the distribution of the strain rate within the PLC band visualized by the DIC method.

High resolution crack initiation and propagation behavior in specimen FLMβ(MS)-HH(WTR), visualized with the imaging-type XMT technique.

(Left) Stress-strain curves of pure magnesium, Mg- 6.2mol%Li, Mg-11.7mol%Li and Mg-0.9mol%Y alloys. (Right) Relationship between frequency of activated slips and nominal strain in pure magnesium, Mg-6.2mol%Li, Mg- 11.7mol%Li and Mg-0.9mol%Y alloys.

TEM images of the aged samples, (a): 180 °C under-aged sample around GB, (b): 180 °C under-aged sample grain interior, (c): 180 °C peak-aged sample around GB.

Antibacterial surface treatment of Ti dental implants was reviewed. Visible-light responsive TiO₂ layers with Au nanoparticles and dissolved Au³⁺ ions were formed on Ti-Au alloys after oxidation in air. They exhibited visible-light photocatalytic activity against Escherichia coli.

Cross-section SEM images and adhesion strength of as-coated OCP and HAp layers formed on WE43.

High resolution electron microscopy image of the amorphous layer found at the welded boundary of 5052Al and zirconium.

Figure HRTEM images of the C15–Al₂Ca precipitate observed in the Mg–5Al–1.5Ca alloy aged at 548 K/10 h (a) and 598 K/1 h (b), taken with B = [11-20]_α. The spots with dark contrast on the planar surface of the precipitate are indicated with arrowheads in (b).

Figure FE-SEM image of α-Mg/C14–Mg₂Ca lamellar microstructure observed in the Mg–14.8 mass% Ca alloy (a). STEM BFI of an α-Mg/C14–Mg₂Ca terrace, together with SADP taken with B = [11-20]_α.

Figure HRTEM image, taken with B = [01-11]_α, of the as-cast α-Mg/C14–Mg₂Ca eutectic alloy creep- ruptured at 473 K under a stress of 40 MPa under (a) multiple and (b) two-beam diffraction conditions. The dislocation alignment is indicated by white arrowheads in (a).

The variation of surface morphology of the specimens subjected to steam coating process. (a) Lath-like crystals, (b) block type crystals, (c) concurrent formation of lath-like and block type crystals, (d) coarse lath-like crystals.

Figure 1 Surface hardness after (a) MFC and (b) WJP processing with various stand-off distances.

Figure 2 SEM images of specimen surfaces after treatment for 2 min: (a) MC-WJP and (b) MC-MFC. Panels (a) and (b) are enlargements of the outlined regions in Figs. 2(b) and 2(c), respectively.

A novel displacement Ni plating process proposed in this study. Fe elements transferred by FPP reduces Ni ion, depositing Ni film onto Al substrate.

Surface SEM image of ideally ordered TiO through-hole membrane obtained by two-layer anodzation process.

SEM image of ordered anodic porous alumina with an inter-hole spacing of 1.8 µm.

Nitrogen analyses by EPMA suggest that a profile of a nitrogen diffusion phase depends on both the plasma nitriding and sintering temperatures.

Average standard deviation of strain components as a function of (a) the average marker distance and (b) the number of utilized markers. Different combinations of binarization thresholds, b_th in 1st and 2nd undeformed sample images, are examined.

Morisita index, which presents spatial distribution of particles, of Al₃Ti particles in Al₃Ti alloy is more than 1 regardless of processing route. This means that both processing routes generate aggregate distributions of Al₃Ti particles.

Cross section of near crack initiation site hot-forged Ti-17 subjected to solution treatments at low and high temperatures (L/STA and H/STA, respectively).

Relationship between sidewall curvature and holding time are shown for four metal sheets.

The alloy prediction and the control of the liquid phase separation in multi-component Ti-Ag alloys by the application of the alloy design technique of High Entropy Alloys.

Microstructure of the rods fabricated at high (a) and low (b) input energy density and variations in the ultimate tensile strength (c) and the elongation (d) at 1023 K of the rods as a function of input energy density.

Crystal direction maps in (a) the start material specimen and the specimens after MDF for (b) 1pass, (c) 3 passes, and (d) 6 passes. The directions were parallel to the final compression axes.

Thermal conductivities (TCs) of graphite flakes (GFs) in Sample1-2. Regions denoted as P1, P2, and P3 correspond to the microstructures. Colors means the TCs of GFs, where red is high TC and blue is low TC.

We success the fabrication of dense component of Ti-20at.%X (X = Cr and Nb) alloys by Selected laser melting (SLM) process, from a mixture of powders element powders.

Fig. 1 Transmission electron microscopy of sample processed by HPT and aged at 503 K. (a) Al/Al₃Zr boundary, (c) coherent Al₃Zr precipitates in Al grain, (d) magnified view of Al₃Zr precipitate, (e) thin layer of AlZr in Al/Al boundary and (f) magnified view of AlZr. Al₃Zr-T, Al₃Zr-C and AlZr-O denote Al₃Zr with D0₂₃ structure, Al₃Zr with L1₂ structure and AlZr with Bf structure, respectively.

Fig. 2 Electrical conductivity against microhardness for Al-5%Zr alloy processed by HPT and aging, in comparison with reported data in literature.

Indentation tests using a spherical indenter were applied to on (1210). The indentation morphology, twins and slip lines depend on alloying elements.

Fig. 1 SEM micrographs of the fracture surfaces near V-notch root; specimens of (a) and (d) hot-extruded, (b) and (e) 1st pass MDFed, (c) and (f) 3rd pass MDFed. (d), (e) and (f) are the enlarged images of the frames A, B and C in (a), (b) and (c). Main crack propagation direction is indicated by white arrows. Areas surrounded by black-dashed lines in (d), (e) and (f) show brittle fracture manner.

The time for starting temperature rise measured by infrared detector and thermocouple has an agreement with the prediction. A high responsiveness for both is observed.

Obtained aluminum foam. (a) Star shaped model. (b) Photo of star shaped aluminum foam. (c) Horizontal cross-sectional X-ray CT image of (b). (d) Vertical cross-sectional X-ray CT image of (b).

(a) Foaming behavior of three precursors. The precursors were moved from left to right. The right side of each figure shows the enlarged images of the precursor. (b) T – t relationships corresponding to (a).

Foaming and press forming behaviors: (a) at start of start heating, (b) foaming, (c) at end of heating, (d) press forming.

Press forming behavior during foaming obtained using video camera and by X-ray radiography system.

Press formed dies and obtained AC4CH/pAl samples. (a) Triangular die. (b) Waveform surface die. (c) Triangular AC4CH/pAl sample. (d) Waveform surface AC4CH/pAl sample.

(a) - (e) foaming behavior and (f) temperature history of A1050 and ADC12 precursors (A1050: d = 25 mm, ADC12: d = 40 mm).

(a) Photograph of precursor used. (b) Setup of precursor for roll forming. (c), (d) Precursor foaming. (e)-(g) Roll forming of softened aluminum foam immediately after precursor foaming.

Sequential cutting images at t＝10 s and their temperature distributions.

Dislocation dynamics simulations for the dislocation overcoming the {111} plate-shaped precipitates. Marked difference in the stress-strain curves found in the dislocation interaction with the {111} variants.

Strain disturbance inside/outside the precipitate under cold rolling condition. Tensile and compressive residual stresses around the inhomogeneiry reflecting the microstructural evolution in the vicinity of the inhomogeneity.

Prediction of deformed shape and strain disturbance inside/outside the precipitate under cold rolling (left). EBSD colour coded map of the plastic deformation of the matrix phase around the inhomogeneity (right).

Microstructures of designed Al-based cast alloys strengthened by T-Al₆Mg₁₁Zn₁₁ intermetallic phases using a eutectic reaction in the Al–Mg–Zn ternary system.

Dislocations introduced by cold-rolling affect the precipitation process during aging, causing a different age-hardening behavior. There are two distinct routes to form two types of S phase.

S-I and S-II phases as well as GPBX zones were observed by HAADF-STEM, their atomic structures were determined.

Hydrogen release behavior during SSRT, together with change in the local axial strain under Wet condition of an Al-Zn-Mg alloy.

Relation between stress (σ) and number of cycle to failure (N) for electroless Ni-P plated specimens.

XANES spectra near (a) Si-K edge and (b) Mg-K edge of Al-Mg-Si alloys and reference samples for natural aging times from 0.6ks to 8.8×10⁴ks.