INDEX

Stress-strain curve of Ti-(1, 2, 3)Mo-3O alloy. The typical mechanical property range of Ti-6Al-4V alloy is shown as a shaded area. The developed alloys have higher strength than the Ti-6Al-4V alloy and moderate ductility.

Mechanical properties of LPBF Ti-10Mo alloys after heat treatment (a) and EBSD analysis results of fractured area of sample with texture (b).

Strong or highly random crystallographic textures obtained in the Ti-15Mo-5Zr-3Al under different fabrication conditions via LPBF where smaller G/R and enhanced polycrystal formation.

3D contour maps of the objective function I1 predicted by the surrogate model. Three design parameters were selected to show a 3D design space with the remaining parameter fixed at average values in (a) and (b) .

This shows the 3D response surfaces of objective function I₂, which were drawn as 3D contour maps. Two of the top four design parameters were selected to show a couple of 3D design spaces.

Distributions of cup height in the circumferential direction at punch strokes of 8 mm, 12 mm, and 16 mm.

Optical micrographs of pure magnesium ((a) and (c)) and 0.5Y ((b) and (d)) after bending test. Mg-0.5Y showed enhanced bendability by activating non-basal slips in the tension side.

Relationship between bending ductility and yttrium content. The bending ductility of magnesium increased with increasing yttrium contents and showed orientation dependence.

Fig. Optical and SEM micrographs of longitudinal sections of polished and gas blow induction-heating nitrided specimens at 1023 K and 1173 K.

HAADF image of the cross-section of the anodized aluminum specimen prepared by anodization in sulfuric acid alone for 60 s.

Surface tension of liquid aluminum measured under a flowing mixture of Ar-He gas at 0.4 L·min^-1 (■), 1 L·min^-1 (■) and 2 L·min^-1 (□).

C-and-N-co-doped rutile single-phase TiO₂ films were formed via oxidation of Ti, and the TiO₂ films showed antibacterial activity under 15 min of visible light irradiation and acceptable cytotoxicity.

Effect of the size of the working electrode area on the occurrence of corrosion phenomena on (a) Al-4.5Cu and (b) Al-4.5Cu-1.5Mg alloys during 3.6-ks immersion in the naturally aerated 0.1 M NaCl (pH 6.0).

Surface appearances of sintered AA7075 before (upper row) and after 20 cycles of dip and dry (lower row).

Representative microstructure and engineering stress-strain curves of as-built Ti-Zr-O alloys.

Variations in (a) Young's modulus and (b) yield stress of each alloy. a, b, and c indicate statistically homogeneous subgroups with P > 0.05 (Tukey HSD multiple comparison test).

Inverse pole figure maps, and (001), (111) and (110) pole figures of pure Al and Al-10 mass%Mg alloy plates SPed for 7 min at peening pressure of 0.2 MPa. The observation is performed on the peened surface.

Two formation scenarios of GP2 zones in Al-Cu alloys and the corresponding time-temperature-transformation diagram.

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.

Effective TC diagrams of the elements (Cf-Cu and Fe matrix) on the 2D cross-section of composites with different volume fractions of Cf-Cu.

Microstructure of composites fabricated by infiltrating molten aluminum alloy into AlN porous bodies with different porosities (a. 71%, b. 76%, c. 79% and d. 84%).

There is no difference in fatigue strength between anodized aluminum alloy and virgin in the regions above 180MPa and below 140MPa. It was confirmed that under axial loading conditions anodizing does not reduce fatigue strength in certain stress amplitude region. In addition, fatigue strength of the anodizing varied at 160 MPa.

Yield stress and elongation to failure plotted against equivalent strain at strain rate of 1 × 10^-5 s^-1.

The compressive residual stress introduced by shot peening improved the fatigue strength of pure titanium by 20% and rendered harmless surface defects at a depth of 0.04 mm.

Microstructure of the boundary between the SUS304 and CP-Ti regions after welding with using Zr-based metallic glass ribbons (a). The corresponding elemental distribution map of (b) Fe, (c) Ti and (d) Zr are also depicted.

The standardized partial regression coefficients for valence s (n_s), p (n_p), and d (n_d) electrons, along with the metallic radius (r_m), from the multiple regression analysis.

An O-site Zn and vacancy pair is formed in the TCO shell in the Al-Zn-Mg alloy, which leads to an increase in the positron lifetime.

Cross-sectional views of blisters in (a) 99.99% (4N) and (b) 99% purity (2N), together with local stress fields around the hydrogen blisters.

Relationship between tensile strength of the joints and shortening.

Various factors control bone matrix orientation. Bone orientation is tightly controlled by genes, diseases, cell adhesion mechanisms, and cell-cell communication substances. These are the most important factors to consider in developing hard tissue-compatible bone medical materials.

Cross-sectional SEM images and EPMA mapping of oxide scale formed on Al-3%Mg alloys and AC4B at 773 K for 25 h in an air.

Manufacturing process of aluminum foam with wire arc additive manufacturing.

Deep cup with good shape accuracy was formed by two-step compression forming which is composed of boss forming and flange compression.

Figure. FE-SEM image of the die-cast AX52 alloy.

Figure. Plots of minimum creep rate vs. aging time at 523 K for the Mg-5Al-1.5Ca alloy after homogenization, where the creep tests were carried out at 448 K under a stress of 70 MPa.

Figure. FE-SEM image of the Mg-14Ca alloy creep-interrupted at 498 K under a stress of 40 MPa for 99.7 h (3.6×10⁵ s).

Results of hammering test and finite element simulation
(Mg = AZ31 magnesium alloy, Al = A5052 aluminum alloy, St = S50C steel)

V-groove friction test for AZ80 (a: Schematic view of V-groove friction test, b: Calibration curve and experimental result, c: Test piece after V-groove friction test).

“Mg grain stress and phase stress” estimated by in-situ neutron diffraction analysis during the tensile deformation of Mg/LPSO two-phase extruded alloy.

Hot rolling process for explosively welded Mg/Al cladding plates, results of tensile tests for hot rolled samples, and interfacial microstructures of hot rolled samples.

(a–b) Creep rate-strain curves of the LAZ941 and the LZ91 alloys. (c) Creep elongation as a function of creep temperature. (d) The appearance of specimens before and after superplastic deformation.

Aluminate ions released from LDHAlO₂ coating was expected to precipitate with the corrosion products and repaired the initiating corrosion pits.

Correlation between TNF-α concentration and removal torque value in each coating thickness group.

Cross slip patterns on a plane normal to the elongated direction of WW specimen after the eight biaxial compressions for which the cumulative strain was 2. a3, b3, c3 and d3 mean slip systems activated during the compression.

IQ and IPF maps for S.T., as-ECAP, and specimens subjected to short-time heating at 250°C and 400°C after ECAP processing (ECAP+250°C and ECAP +400°C, respectively).

Summary of effects of CR0.5 cooling temperature range on microstructures and mechanical properties.

Appearance and cross section of joined workpiece after shot lining.

Wear depth of shot peened and join workpieces after abrasion test.

Phase field of pore with the parameters optimized for the target value of 2.0 mm.

Change of layer speeds in the roll bite (with wire brushing, D=70mm).

Microstructures of (a) pure Ti, (b) Ti-10Zr, (c) Ti-20Zr, and (d) Ti-30Zr alloys fabricated from TiH₂ and ZrH₂ powders by spark plasma sintering and corresponding element distributions.

Deformation rate dependence of mechanical properties in CP-Ti; twinning frequency and dislocation slip mode depend on deformation rate and grain size.

Stress - strain curves attained by tensile tests along the longitudinal direction of the processed AZ80Mg alloy rods; (a) as-DRFed rods and (b) DRFed rods followed by extrusion. For comparison, the flow curves of the as-hot extruded rod and it subjected to cold extrusion are also shown.

SEM secondary electron images ((a) and (c)) and backscattered electron images ((b) and (d)) of the 25Ti-1h functionally graded grinding wheel sample focused on diamond ((a) and (b)) and Al₃Ti ((c) and (d)).

(a) Crystal structure of TiC and (b) atomic arrangement of the (001)TiC plane superimposed on the atomic arrangement of (001)_Ti6Al4V.

Suitable stress–strain relations after necking were obtained the step wise modeling method. Flow stress at plastic strain of 0.03 and 0.10 decrease slightly.

Chemical compositions affected stress-strain curves. Perforation hole area slightly decreased with yield stress of 6000 series aluminum alloys.

XRD analysis showed that the sample that was reacted with the addition of a catalyst and a long reaction time with a small temperature change was the most effective in suppressing the formation of baemite.

Stress-strain curves of rolled pure titanium sheets in (a) conventional tensile test, (b) interrupted tensile test with time interval and (c) interrupted tensile test without interval time.

(Left) Electron microscope images of kink deformed Al-Cu layered structure, (Right) Development of kink deformation in layered structure based on FEM analysis.

The strain rate dependence of embrittlement susceptibility index, I(δ) of the AZ31 and AZ61 alloys.

Minimum creep rate plotted against the respective applied stresses in double logarithmic plots. The thick lines represent the relationship between the creep rate and stress calculated using the CLLM, while the fitting lines represent the experimental data for each single-phase material.

The presence of a hydrogen trapping site in Al₆Mn, as determined by DFT calculations, could be explored experimentally using muon.

Hydrogen absorption curves of catalyzed Mg as powder and pellets at room temperature under 0.5 MPa of H₂ gas.

Photograph of the continuous casting using electromagnetic force for Al–7wt%Si alloys.

Photographs of the water droplets formed on the anodic porous alumina in which the pore diameter increases in a gradient from the center to both ends.

Machine learning analysis of over 1,000 papers identified that incorporating Ti and V into Al-Si and Al-Cu alloys is crucial for improving high-temperature strength in casting materials.

Vanadium addition (0.5 wt%) enhances high-temperature strength in Al-7Si alloys by forming Al₁₀V intermetallic particles, inhibiting dislocation movement, and improving stress distribution, particularly with Ti co-addition.

Compressive stress-strain curves of AM porous Al-4.8Mg-0.7Sc alloy and AM porous Al-10Si-0.3Mg alloy. Unit-cell structures are fcc-Voronoi, rhombic dodecahedron.

Temperature dependence of absorbed-impact energy. The values with arrows above 350 K at 200 m/min are underestimated.