Abstract: A steel comprises, by mass percent, C: 0.10 to 0.15%, Si: not less than 0.02% and less than 0.10%, Mn: more than 0.90% and not more than 2.50%, P?0.030%, S?0.050%, Cr: 0.80 to 2.0%, V: 0.05 to 0.50%, Al: 0.01 to 0.07%, N?0.0080%, O?0.0030%, and one or more selected from Mo, Cu, Ni, Ti, Nb, Zr, Pb, Ca, Bi, Te, Se and Sb, the balance being Fe and impurities. The composition satisfies [35?Mn/S?200], [20?(669.3×loge C?1959.6×loge N?6983.3)×(0.067×Mo+0.147×V)?80], [140×Cr+125×Al+235×V?160] and [150?511×C+33×Mn+56×Cu+15×Ni+36×Cr+5×Mo+134×V?200].

Abstract: The disclosure provides a creep resistant alloy having an overall composition comprised of iron, chromium, molybdenum, carbon, manganese, silicon, nickel, vanadium, niobium, nitrogen, tungsten, cobalt, tantalum, boron, copper, and potentially additional elements. In an embodiment, the creep resistant alloy has a molybdenum equivalent Mo(eq) from 1.475 to 1.700 wt. % and a quantity (C+N) from 0.145 to 0.205. The overall composition ameliorates sources of microstructural instability such as coarsening of M23C6carbides and MX precipitates, and mitigates or eliminates Laves and Z-phase formation. A creep resistant martensitic steel may be fabricated by preparing a melt comprised of the overall composition followed by at least austenizing and tempering. The creep resistant alloy exhibits improved high-temperature creep strength in the temperature environment of around 650° C.

Abstract: An aluminum alloy member resistant to cracking and having high strengths and excellent stress corrosion cracking resistance is manufactured by expanding a 7xxx aluminum alloy hollow extrusion at a rate of 5% or more. Specifically, a 7xxx aluminum alloy hollow extrusion containing Zn of 3.0-9.5%, Mg of 0.4-2.5%, Cu of 0.05-2.0%, and Ti of 0.005-0.2%, in mass percent, and prepared through press quenching is subjected to a reversion treatment, to pipe expansion within 72 hours after the reversion treatment, and to temper aging. The reversion treatment includes heating at a temperature rise rate of 0.4° C./second or more, holding in a temperature range of 200-550° C. for longer than 0 second, and cooling at a rate of 0.5° C./second or more. The ratio Y (?rs/?0.2) of the tensile residual stress ?rs to the 0.2% yield stress ?0.2 after temper aging and the total content X of Mg and Zn satisfy Expression (1): Y??0.1X+1.4 ??(1).

Abstract: A method of manufacturing a high strength cold rolled steel sheet includes hot-rolling and cold-rolling a steel slab annealing the steel sheet at an annealing temperature of 750° C. to 830° C.; subjecting the steel sheet to first cooling at an average cooling rate of 3° C./sec to 40° C./sec in a temperature range from the annealing temperature to 480° C.; subjecting the steel sheet to second cooling at an average cooling rate of 8° C./sec to 80° C./sec in a temperature range from 480° C. to Tc (° C.) given by formula (6): Tc=435?40×[% Mn]?30×[% Cr]?30×[% V]??(6) wherein [% A] is the content (% by mass) of alloying element A; and subjecting the steel sheet to third cooling at an average cooling rate of 0.3° C./sec to 30° C./sec in a temperature range from Tc (° C.) to 200° C.

Abstract: Ni base superalloy components containing relatively large amounts of Al and Ti are known to be difficult to build up by a weld build up process without cracking. As the Al and Ti content of the superalloy is increased to improve the strength, the susceptibility to cracking is increased. It is shown herein that reducing the ?? phase in the additive built up material improves robustness against cracking. A stepwise, controlled heating and cooling process is described to be used in cooperation with an additive build up process to reduce the ?? present and thereby reduce cracking.

Abstract: A novel FeMnAlC alloy, comprising 23˜34 wt. % Mn, 6˜12 wt. % Al, and 1.4˜2.2 wt. % C with the balance being Fe, is disclosed. The as-quenched alloy contains an extremely high density of nano-sized (Fe,Mn)3AlCx carbides (??-carbides) formed within austenite matrix by spinodal decomposition during quenching. With almost equivalent elongation, the yield strength of the present alloys after aging is about 30% higher than that of the optimally aged FeMnAlC (C?1.3 wt. %) alloy systems disclosed in prior arts. Moreover, the as-quenched alloy is directly nitrided at 450˜550° C., the resultant surface microhardness and corrosion resistance in 3.5% NaCl solution are far superior to those obtained previously for the optimally nitrided commercial alloy steels and stainless steels, presumably due to the formation of a nitrided layer consisting predominantly of AlN.

Abstract: A high strength, high toughness steel alloy is disclosed. The alloy has the following weight percent composition. Element C 0.30-0.47 Mn 0.8-1.3 Si 1.5-2.5 Cr 1.5-2.5 Ni 3.0-5.0 Mo + ½ W 0.7-0.9 Cu 0.70-0.90 Co ?0.01 max. V + ( 5/9) × Nb 0.10-0.25 Ti 0.005 max. Al 0.015 max. Fe Balance Included in the balance are the usual impurities found in commercial grades of steel alloys produced for similar use and properties including not more than about 0.01% phosphorus and not more than about 0.001% sulfur. Also disclosed is a hardened and tempered article that has very high strength and fracture toughness. The article is formed from the alloy having the broad weight percent composition set forth above. The alloy article according to this aspect of the invention is further characterized by being tempered at a temperature of about 500° F. to 600° F.

Abstract: A method involves depositing a seed layer comprising at least A1 phase FePt. A main layer of A1 phase FePt is deposited over the seed layer. The main layer includes FePt of a different stoichiometry than the seed layer. The seed and main layers are annealed to convert the A1 phase FePt to L10 phase FePt. The annealing involves heating the substrate prior to depositing at least part of the A1 phase FePt of the main or seed layers.

Abstract: A high-strength aluminum alloy material having a chemical composition which includes Zn: more than 7.2% (mass %, the same applies hereafter) and 8.7% or less, Mg: 1.3% or more and 2.1% or less, Cu: 0.01% or more and 0.10% or less, Zr: 0.01% or more and 0.10% or less, Cr: less than 0.02%, Fe: 0.30% or less, Si: 0.30% or less, Mn: less than 0.05%, Ti: 0.001% or more and 0.05% or less, the balance being Al and unavoidable impurities, is provided. It has a proof stress of 350 MPa or more, and a metallographic structure formed of a recrystallized structure, and L* and b* values, as defined in JIS Z8729 (ISO 7724-1), are 85 or more and 95 or less and 0 or more and 0.8 or less, respectively, as measured after anodization using a sulfuric acid bath.

Abstract: The present invention provides a method for manufacturing a hot stamped body having a vertical wall, the method including: a hot-rolling step; a coiling step; a cold-rolling step; a continuous annealing step; and a hot stamping step, in which the continuous annealing step includes a heating step of heating the cold-rolled steel sheet to a temperature range of equal to or higher than Ac1° C. and lower than Ac3° C.; a cooling step of cooling the heated cold-rolled steel sheet from the highest heating temperature to 660° C. at a cooling rate of equal to or less than 10° C./s; and a holding step of holding the cooled cold-rolled steel sheet in a temperature range of 550° C. to 660° C. for one minute to 10 minutes.

Abstract: Disclosed is a copper alloy containing 1.0% to 3.6% of Ni, 0.2% to 1.0% of Si, 0.05% to 3.0% of Sn, 0.05% to 3.0% of Zn, with the remainder including copper and inevitable impurities. The copper alloy has an average grain size of 25 ?m or less and has a texture having an average area percentage of cube orientation of 20% to 60% and an average total area percentage of brass orientation, S orientation and copper orientation of 20% to 50%. The copper alloy has a KAM value of 0.8 to 3.0 and does not suffer from cracking even when subjected to U-bending. The copper alloy has excellent balance between strengths (particularly yield strength in a direction perpendicular to the rolling direction) and bending workability.

Abstract: Austenitic stainless steel having high temperature strength and excellent nitric acid corrosion resistance is provided. The austenitic stainless steel according to the present embodiment including, in mass percent, C: at most 0.050%, Si: 0.01 to 1.00%, Mn: 1.75 to 2.50%, P: at most 0.050%, S: at most 0.0100%, Ni: 20.00 to 24.00%, Cr: 23.00 to 27.00%, Mo: 1.80 to 3.20%, and N: 0.110 to 0.180%, the balance being Fe and impurities, a grain size number of crystal grains based on JIS G0551 (2005) is at least 6.0, and an area fraction of a ? phase is at most 0.1%.

Abstract: A Cu—Co—Si alloy having an improved balance between electrical conductivity and strength is provided. Disclosed is a copper alloy for electronic materials, which contains 0.5% to 4.0% by mass of Co and 0.1% to 1.2% by mass of Si, with the balance being Cu and unavoidable impurities, and in which the mass % ratio of Co and Si (Co/Si) is 3.5?Co/Si?5.5, an area ratio of discontinuous precipitation (DP) cells is 5% or less, and an average value of a maximum width of discontinuous precipitation (DP) cells is 2 ?m or less.

Abstract: A thick-walled high-strength hot rolled steel sheet has a high tensile strength TS of 521 MPa or more and excellent low-temperature toughness. The steel material forming the sheet contains 0.02%-0.08% C, 0.01%-0.10% Nb, and 0.001%-0.05% Ti and is heated; C, Ti, and Nb satisfies (Ti+(Nb/2))/C<4.

Abstract: The present invention relates to an implant, in particular an intraluminal endoprosthesis, the body of which comprises at least predominantly a material with iron as the main constituent. For accelerating the degradation, the material comprises sulfur as first minor constituent with a concentration of more than 0.2% by weight and not more than 1% by weight, preferably not more than 0.5% by weight, and comprises as second minor constituent at least one element of the group which comprises calcium, manganese and magnesium. Furthermore, a method for producing such an implant is described.

Abstract: The present invention relates to methods for producing metal-supported thin layer skeletal catalyst structures, to methods for producing catalyst support structures without separately applying an intermediate washcoat layer, and to novel catalyst compositions produced by these methods. Catalyst precursors may be interdiffused with the underlying metal support then activated to create catalytically active skeletal alloy surfaces. The resulting metal-anchored skeletal layers provide increased conversion per geometric area compared to conversions from other types of supported alloy catalysts of similar bulk compositions, and provide resistance to activity loss when used under severe on-stream conditions. Particular compositions of the metal-supported skeletal catalyst alloy structures can be used for conventional steam methane reforming to produce syngas from natural gas and steam, for hydrodeoxygenation of pyrolysis bio-oils, and for other metal-catalyzed reactions inter alia.

Abstract: The present invention aim at providing a steel for steam turbine blades which is excellent in terms of strength and toughness. The steel of the present invention has a composition which contains, in terms of % by mass, 0.02-0.10% of C, up to 0.25% of Si, 0.001-0.10% of Mn, up to 0.010% of P, up to 0.010% of S, 8.5-10.0% of Ni, 10.5-13.0% of Cr, 2.0-2.5% of Mo, 0.001-0.010% of N, 1.15-1.50% of Al, less than 0.10% of Cu, up to 0.20% of Ti, and the remainder being incidental impurities and Fe, and which satisfies 6.0?Ni/Al?8.0, 9.0?Nieq?11.0 and 17.0?Creq?19.0, in which Nieq=[Ni]+0.11[Mn]?0.0086([Mn]2)+0.44[Cu]+18.4[N]+24.5[C] Creq=[Cr]+1.21[Mo]+0.48[Si]+2.2[Ti]+2.48[A1].

Abstract: An R—Fe—B based porous magnet according to the present invention has an aggregate structure of Nd2Fe14B type crystalline phases with an average grain size of 0.1 ?m to 1 ?m. At least a portion of the magnet is porous and has micropores with a major axis of 1 ?m to 20 ?m.

Abstract: A steel for high-strength spring has an Ac3 transformation temperature as an indicator of the decarburization performance, which is calculated by Equation (1) below, is from 859 to 885° C., a maximum hardened diameter DI as an indicator of the hardening performance, which is calculated by Equation (2) below, is from 70 to 238 mm, and a temper hardness HRC as an indicator of the spring performance, which is calculated by Equation (3) below, is from 50 to 55. Ac3=910?203×?{square root over (C)}?15.2Ni+44.7Si+104V+31.5Mo+13.1W??(1) DI=DO×fSi×fMn×fP×fS×fCu×fNi×fCr??(2) HRC=38.99+17.48C+2.55Si?2.28Ni+2.37Cr+8.04Ti??(3) wherein, D0=8.65×?{square root over (C)}, fSi=1+0.64×% Si, fMn=1+4.10×% Mn, fP=1+2.83×% P, fS=1?0.62×% S, fCu=1+0.27×% Cu, fNi=1+0.52×% Ni, and fCr=1+2.33×% Cr.

Abstract: [Problem] To suppress the generation of particles by reducing the average particle diameter to several dozen ?m or less. [Solution] After forming a preform of a tungsten powder, the preform is sintered. The preform is formed so as to have a relative density of 70-90% (inclusive) and an oxygen content of 100-500 ppm (inclusive). The sintering is carried out by a hot isostatic pressing method at 1,700-1,850° C. (inclusive). Consequently, a tungsten target which has an average particle diameter of 20 ?m or less with a standard deviation of 10 ?m or less, a relative density of 99% or more and an oxygen content of 10 ppm or less can be obtained. This tungsten target is capable of significantly reducing the generation of particles during sputtering.