Abstract: A non-limiting embodiment of a titanium alloy comprises, in weight percentages based on total alloy weight: 5.5 to 6.5 aluminum; 1.5 to 2.5 tin; 1.3 to 2.3 molybdenum; 0.1 to 10.0 zirconium; 0.01 to 0.30 silicon; 0.1 to 2.0 germanium; titanium; and impurities. A non-limiting embodiment of the titanium alloy comprises a zirconium-silicon-germanium intermetallic precipitate, and exhibits a steady-state creep rate less than 8×10?4 (24 hrs)?1 at a temperature of at least 890° F. under a load of 52 ksi.

Abstract: According to one embodiment, an alpha-beta titanium alloy comprises, in weight percentages: an aluminum equivalency in the range of about 6.7 to 10.0; a molybdenum equivalency in the range of 0 to 5.0; at least 2.1 vanadium; 0.3 to 5.0 cobalt; titanium; and incidental impurities.

Abstract: A method for heat treating a powder metallurgy nickel-base alloy article comprises placing the article in a furnace at a start temperature in the furnace that is 80° C. to 200° C. below a gamma prime solvus temperature, and increasing the temperature in the furnace to a solution temperature at a ramp rate in the range of 30° C. per hour to 70° C. per hour. The article is solution treated for a predetermined time, and cooled to ambient temperature.

Abstract: A method of producing a beta-titanium alloy elongated product form having a chemical composition as specified in UNS R58150 or ASTM F2066-13. The method comprises solution treating, aging, straightening, stress-relief aging, and cooling the elongated product form. Articles of manufacture comprising or produced from beta-titanium alloy elongated product forms made according to the method also are disclosed.

Abstract: A non-limiting embodiment of a titanium alloy comprises, in weight percentages based on total alloy weight: 2.0 to 5.0 aluminum; 3.0 to 8.0 tin; 1.0 to 5.0 zirconium; 0 to a total of 16.0 of one or more elements selected from the group consisting of oxygen, vanadium, molybdenum, niobium, chromium, iron, copper, nitrogen, and carbon; titanium; and impurities. A non-limiting embodiment of the titanium alloy comprises an intentional addition of tin and zirconium in conjunction with certain other alloying additions such as aluminum, oxygen, vanadium, molybdenum, niobium, and iron, to stabilize the ? phase and increase the volume fraction of the ? phase without the risk of forming embrittling phases, which was observed to increase room temperature tensile strength while maintaining ductility.

Abstract: A non-limiting embodiment of a titanium alloy comprises, in percent by weight based on total alloy weight: 5.1 to 6.5 aluminum; 1.9 to 3.2 tin; 1.8 to 3.1 zirconium; 3.3 to 5.5 molybdenum; 3.3 to 5.2 chromium; 0.08 to 0.15 oxygen; 0.03 to 0.20 silicon; 0 to 0.30 iron; titanium; and impurities. A non-limiting embodiment of the titanium alloy comprises an intentional addition of silicon in conjunction with certain other alloying additions to achieve an aluminum equivalent value of at least 6.9 and a molybdenum equivalent value of 7.4 to 12.8, which was observed to improve tensile strength at high temperatures.

Abstract: According to one embodiment, an alpha-beta titanium alloy comprises, in weight percentages: an aluminum equivalency in the range of about 6.7 to 10.0; a molybdenum equivalency in the range of 0 to 5.0; at least 2.1 vanadium; 0.3 to 5.0 cobalt; titanium; and incidental impurities.

Abstract: A non-limiting embodiment of a titanium alloy comprises, in weight percentages based on total alloy weight: 5.5 to 6.5 aluminum; 1.5 to 2.5 tin; 1.3 to 2.3 molybdenum; 0.1 to 10.0 zirconium; 0.01 to 0.30 silicon; 0.1 to 2.0 germanium; titanium; and impurities. A non-limiting embodiment of the titanium alloy comprises a zirconium-silicon-germanium intermetallic precipitate, and exhibits a steady-state creep rate less than 8×10?4 (24 hrs)?1 at a temperature of at least 890° F. under a load of 52 ksi.

Abstract: Nickel-based alloys having improved localized corrosion resistance, improved stress-corrosion cracking (SCC) resistance and impact strength are disclosed. The improvements come from the provision of compositions that are resistant to deleterious phase formation and from the addition of alloying elements that improve corrosion resistance, impact strength, and SCC resistance. The nickel-based alloys of the present invention have controlled amounts of Ni, Cr, Fe, Mo, Co, Cu, Mn, C, N, Si, Ti, Nb, Al, and B. When subjected to post-cladding heat treatments or welding, the nickel-based alloys retain their corrosion resistance and possess desirable impact strengths.

Abstract: Certain embodiments of a melting and casting apparatus comprising includes a melting hearth; a refining hearth fluidly communicating with the melting hearth; a receiving receptacle fluidly communicating with the refining hearth, the receiving receptacle including a first outflow region defining a first molten material pathway, and a second outflow region defining a second molten material pathway; and at least one melting power source oriented to direct energy toward the receiving receptacle and regulate a direction of flow of molten material along the first molten material pathway and the second molten material pathway. Methods for casting a metallic material also are disclosed.

Abstract: A method of processing a metal alloy includes heating to a temperature in a working temperature range from a recrystallization temperature of the metal alloy to a temperature less than an incipient melting temperature of the metal alloy, and working the alloy. At least a surface region is heated to a temperature in the working temperature range. The surface region is maintained within the working temperature range for a period of time to recrystallize the surface region of the metal alloy, and the alloy is cooled so as to minimize grain growth. In embodiments including superaustenitic and austenitic stainless steel alloys, process temperatures and times are selected to avoid precipitation of deleterious intermetallic sigma-phase. A hot worked superaustenitic stainless steel alloy having equiaxed grains throughout the alloy is also disclosed.

Abstract: Processes and methods related to processing and hot working alloy ingots are disclosed. A metallic material layer is deposited onto at least a region of a surface of an alloy ingot before hot working the alloy ingot. The processes and methods are characterized by a reduction in the incidence of surface cracking of the alloy ingot during hot working.

Abstract: Processes and methods related to processing and hot working alloy ingots are disclosed. A metallic material layer is deposited onto at least a region of a surface of an alloy ingot before hot working the alloy ingot. The processes and methods are characterized by a reduction in the incidence of surface cracking of the alloy ingot during hot working.

Abstract: A non-limiting embodiment of a titanium alloy comprises, in weight percentages based on total alloy weight: 2.0 to 5.0 aluminum; 3.0 to 8.0 tin; 1.0 to 5.0 zirconium; 0 to a total of 16.0 of one or more elements selected from the group consisting of oxygen, vanadium, molybdenum, niobium, chromium, iron, copper, nitrogen, and carbon; titanium; and impurities. A non-limiting embodiment of the titanium alloy comprises an intentional addition of tin and zirconium in conjunction with certain other alloying additions such as aluminum, oxygen, vanadium, molybdenum, niobium, and iron, to stabilize the ? phase and increase the volume fraction of the ? phase without the risk of forming embrittling phases, which was observed to increase room temperature tensile strength while maintaining ductility.

Abstract: A non-limiting embodiment of a titanium alloy comprises, in percent by weight based on total alloy weight: 5.1 to 6.5 aluminum; 1.9 to 3.2 tin; 1.8 to 3.1 zirconium; 3.3 to 5.5 molybdenum; 3.3 to 5.2 chromium; 0.08 to 0.15 oxygen; 0.03 to 0.20 silicon; 0 to 0.30 iron; titanium; and impurities. A non-limiting embodiment of the titanium alloy comprises an intentional addition of silicon in conjunction with certain other alloying additions to achieve an aluminum equivalent value of at least 6.9 and a molybdenum equivalent value of 7.4 to 12.8, which was observed to improve tensile strength at high temperatures.

Abstract: A dual hardness steel article comprises a first air hardenable steel alloy having a first hardness metallurgically bonded to a second air hardenable steel alloy having a second hardness. A method of manufacturing a dual hard steel article comprises providing a first air hardenable steel alloy part comprising a first mating surface and having a first part hardness, and providing a second air hardenable steel alloy part comprising a second mating surface and having a second part hardness. The first air hardenable steel alloy part is metallurgically secured to the second air hardenable steel alloy part to form a metallurgically secured assembly, and the metallurgically secured assembly is hot rolled to provide a metallurgical bond between the first mating surface and the second mating surface.

Abstract: According to one embodiment, an alpha-beta titanium alloy comprises, in weight percentages: an aluminum equivalency in the range of about 6.7 to 10.0; a molybdenum equivalency in the range of 0 to 5.0; at least 2.1 vanadium; 0.3 to 5.0 cobalt; titanium; and incidental impurities.

Abstract: According to one embodiment, an alpha-beta titanium alloy comprises, in weight percentages: an aluminum equivalency in the range of about 6.7 to 10.0; a molybdenum equivalency in the range of 0 to 5.0; at least 2.1 vanadium; 0.3 to 5.0 cobalt; titanium; and incidental impurities.

Abstract: A method of processing a workpiece to inhibit precipitation of intermetallic compounds includes at least one of thermomechanically processing and cooling a workpiece including an austenitic alloy. During the at least one of thermomechanically working and cooling the workpiece, the austenitic alloy is at temperatures in a temperature range spanning a temperature just less than a calculated sigma solvus temperature of the austenitic alloy down to a cooling temperature for a time no greater than a critical cooling time.

Abstract: A method for heat treating a powder metallurgy nickel-base alloy article comprises placing the article in a furnace at a start temperature in the furnace that is 80° C. to 200° C. below a gamma prime solvus temperature, and increasing the temperature in the furnace to a solution temperature at a ramp rate in the range of 30° C. per hour to 70° C. per hour. The article is solution treated for a predetermined time, and cooled to ambient temperature.