INDEX

Phase field of the pore obtained in a system with multiple nucleation.

Variation of start temperature of β→ω_i transformation as a function of oxygen concentration in Ti-20 at%Nb alloys. The oxygen addition accelerated and then suppressed the β→ω_i transformation.

SEM-EDS (a) and XRD results (b) of core-shell structured Ti-N powder, tensile properties of Ti-N alloys fabricated by AM and PM process (c) and their fractured surfaces after tensile test (d).

Comparison of the 0.2% proof stress between the machine learning (neural network) result and experimental result (Ti-17 alloy with various kinds of microstructures).

Fatigue behavior and dislocation structure of pure Al strongly depend on the activity of cross slip.

Fatigue-induced dislocation structure in pure Al can be easily rearranged by the activity of cross slip.

TEM high-resolution lattice images and diffractograms of (a) Al, Al₃Ti, and AlTi₃, and (b) AlTi and ω-Ti in sample processed by HPT for 100 revolutions.

Mapping of T_c in an Al-Ti-Mg triangle, predicted by machine learning. The arrows indicate the compositions corresponding to the stable phases. The red circles represent samples prepared via the HPT processing.

3D DCT reconstruction of grains in Al-Zn-Mg alloy. Colors according to IPF key shown in the inset.

Stress-strain curves of monotonic tensile test on three grain sizes (a) and Bauschinger test on UFG-1 (b), UFG-2 (c) and CG (d) specimen.

Stress components of equal plastic work. Solid and open circles represent experimental and simulation results of the dislocation-density-based hardening model.

(Left) Fatigue S-N plots of Mg-0.026 at% Ce single crystals with different orientations.
(Right) Fatigue crack propagation mechanism of (a) pure magnesium single crystal and (b) Mg-Ce single crystals.

Schematic illustration of surface modified layers created and wear behavior of Gas Blow IH nitriding(N series), FPP treated(F series), and GBIH nitride with post-treatment with FPP(N+Fseris) specimens.

Our approach offers a new strategy for preparing hard anodic films with low porosity under mild anodization conditions to prevent burning.

Anticorrosive magnesium hydroxide composite films were prepared on magnesium alloy by steam coating. The corrosion resistance was lowered with an increase in the immersion time.

Change in value of true strain measured in radial direction (from major axis of ellipse), circumferential direction (from minor axis of ellipse) and thickness direction at sequentially numbered locations (measurement point) of deep-drawn cup.

Photo current transient, photocurrent responses, calculated photoelectrochemical action spectra, and the resultant electronic band structures of passive films formed on Ti in Hanks and saline.

Anisotropic compression behavior of ordered open-cell porous titanium.

A gap can be observed between CF and Al matrix in the uncoated CFs/Al sample, while an interfacial layer can be seen between CF and Al matrix in the Ni-coated CFs/Al sample.

As the ceramic particle content increased, the yield strength and tensile strength of the AMCs enhanced, while the elongation of those decreased.

Effect of particle parameters on maximum hydrostatic stress. It is found that most effective parameter for stress concentration of particle in early stage is particle shape (local neck).

Effect of baking temperature for plaster mold on relative density of centrifugally cast Al. Plaster molds were fabricated with and without zbond 90 infiltration.

Relative density, ρ, of the samples with 0vol%, 0.1vol%, 0.5vol% and 1.0vol% TiC heterogeneous nucleation site particles plotted against energy density, E.

The temperature increasing of 100°C slightly affect crate size and the number of ejecta from aluminum alloy 6-61-T6 at hypervelocity impact. They were slightly decreased by the addition of plastic sheet.

SEM-EBSD crystal orientation maps showing the variation in the crystal orientation due to the formation of deformation bands in a mille-feuille structured Al/Al₂Cu alloy.

Snapshots of Mg-Y-vacancy systems and averaged coordination numbers of Y atoms in the second-nearest neighbor shell in Mg-3.0 at.%Y alloys obtained from KMC calculations at various temperatures.

Fig. 1 Yield Strength (solid mark) and Vickers Hardness (open mark) as a function of d^-1/2 (d : grain size).

Relation between stress amplitude (σ_a) and number of cycles to failure (N) for the un-treated and electroless Ni-P plated specimens.

Distribution of different textures: a) Sintered pure Al, b) Hot-rolled pure Al, c) Sintered Csf/Al, d) Hot-rolled Csf/Al, e) Sintered Cu-Csf/Al, f) Hot-rolled Cu-Csf/Al.

(a) is a variation of Al₂O₃/Al composite tensile strength and elongation with increasing ARB cycles, and SEM pictures showing the fractography of Al₂O₃/Al composites processed by (b) 8, (c) 14, and (d) 18 ARB cycles.

Schematic illustrations of upscaling CHPT process for multi-wires

Reduction of surface roughness and introduction of compressive residual stress by SP construction were effective to improve the fatigue strength.

3D perspective view of Al₇Cu₂Fe particles, Mg₂Si particles and voids captured at the ε_a of 4.2% in high-hydrogen Al-Zn-Mg-Cu alloy using synchrotron X-ray nano tomography.

The β”-eye was formed on the layered vacancy–solute complex from a solid solution of Al-Mg-Si alloys during first-principles-based Monte Carlo simulations.

Distributions of tensile strength obtained using microscale tensile test as a function of distance from the tool center for the steel/aluminum alloy interface.

EPMA analysis results of high-Ca type Al-Mg-Ca thermal spray coating at a 5 mm wide damage of the exposure specimen after 11 months exposure.

In-situ observation of microstructural evolution of 10MoA due to rapid lamp heating. Acicular martensite appeared within 2 s after the start of heating, indicating that martensite is formed during heating rather than cooling.

Fig. HRTEM image, taken with B = [01-11]_α, of the α/C14 lamellar interface for the 723 K/1 h-aged α-Mg/C14-Mg₂Ca eutectic alloy crept at 473 K under a stress of 40 MPa, where the creep test was interrupted at a strain of 1.3%.

Fig. Plots of minimum creep rate vs. lamellar spacing for the α-Mg/C14-Mg₂Ca eutectic alloy, where the creep tests were carried out at 473 K under a stress of 40 MPa.

Continuous observation of microstructure during locally heated dieless drawing.

(Left) STEM images of heat treated and hot extruded Mg-Zn-Gd alloys containing solute-enriched stacking faults (SESF).
(Right) Asymmetric XRD peak profiles originating from intergrowth-like precipitations of SESF.

Ideally ordered anodic porous alumina with an interhole distance of 1 µm prepared by the present process.

Schematic drawings of computational domain and simulated temperature distribution during conventional and ultrasonic DC casting process.

A inverse pole figure map and (0001) pole map are shown. Average crystal grain size of extruded material was 136.7 [µm], and the average crystal grain size of the forged material was 42.5 [µm].

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

Interfacial microstructure of explosively welded magnesium/aluminum alloy cladding plates.

Main and cross interdiffusion coefficients (a) , (b) , (c) and (d) in ternary Ti-Al-Zr alloys at 1473 K.

Left: Box plots of polarization resistance (R_p) for the initial 4 weeks in medium. Right: Schematic illustration of corrosion mechanisms of CAp- and HAp-coated WE43 in medium.

Fig. XPS wide scan spectra of specimens surface after immersed in the solutions for 7 d at 25°C.

Nano-hardness around grain boundaries at aging temperature of 180°C ; (a) at under-aged around HAGB, (b) at peak-aged around HAGB, (c) at under-aged around LAGB, (d) at peak-aged around LAGB.

XRD patterns of TNTZ subjected to thermal oxidation processing at a temperature of 723K for 40, 50, and 60s.

Orientation distribution function (ODF) at the section of φ2=0° for (a) Specimen before forging, (b) Specimen forged by four times at a true strain of 0.18, (c) Specimen forged by four times at a true strain of 0.18, (d) main reference orientations.

Distribution of the extreme inverse FIP per aggregate for (a) Mg_99.2Zn_0.2Y_0.6, (b) Mg₉₇Zn₁Y₂ and (c) Mg₈₉Zn₄Y₇ alloy at different stress amplitudes.

Reconstructed tomography of (a) absorption coefficient (b) Zn concentration from absorption coefficient (c) absolute integrated intensity (d) volume fraction of GP zones (e) calculated UTS distribution.

Microstructure of the magnesium target near the crater impacted at room temperature, (a) observed image with SEM, (b-e) IPF (left) and GOS (right) maps in the square portions indicated in (a).

A novel titanium-powder-production process based on the shuttle of disproportionation reaction and its backward reaction of titanium ions in molten salt.

Energy landscape of dislocation motion indicating minimum energy paths including the energy differences for the three core configurations and the energy barriers for motion of three cores in their planes.

Variation of lattice parameters as a function of milling time for the specimens fabricated via intermittent MA and continuous MA.

Precipitates at dislocations or apart from dislocation in HRTEM images of T8 sample aged for 10.8 ks.

Pre-deformation hinders the first hardening but promotes the second hardening until peak. Two types of S phases were observed to form along a dislocation line.

The CS sample has excellent mechanical properties. The direct evidence of Cu aggregation on an edge dislocation was observed.

Cyclic deformation leads to a significant strengthening effect on Al-Mg-Cu alloys due to clusters and dislocations. The mechanical properties are further enhanced by the combination of cyclic deformation and aging.

Simultaneous strength-ductility enhancement of L-PBF processed Al-12%Si alloy due to the homogeneously distributed nanoscale Si precipitates for enhancing the strain hardening.

Negative strain rate sensitivity of strength of the L-PBF processed Al-12%Si alloy due to dynamic precipitation at ambient temperature.