Abstract: A method of refining a microstructure of a titanium material can include providing a solid titanium material at a temperature below about 400° C. The titanium material can be heated under a hydrogen-containing atmosphere to a hydrogen charging temperature that is above a ? transus temperature of the titanium material and below a melting temperature of the titanium material, and held at this temperature for a time sufficient to convert the titanium material to a substantially homogeneous ? phase. The titanium material can be cooled under the hydrogen-containing atmosphere to a phase transformation temperature below the ? transus temperature and above about 400° C., and held for a time to produce ? phase regions. The titanium material can also be held under a substantially hydrogen-free atmosphere or vacuum at a dehydrogenation temperature below the ? transus temperature and above the ? phase decomposition temperature to remove hydrogen from the titanium material.

Abstract: A method of refining a microstructure of a titanium material can include providing a solid titanium material at a temperature below about 400° C. The titanium material can be heated under a hydrogen-containing atmosphere to a hydrogen charging temperature that is above a ? transus temperature of the titanium material and below a melting temperature of the titanium material, and held at this temperature for a time sufficient to convert the titanium material to a substantially homogeneous ? phase. The titanium material can be cooled under the hydrogen-containing atmosphere to a phase transformation temperature below the ? transus temperature and above about 400° C., and held for a time to produce ? phase regions. The titanium material can also be held under a substantially hydrogen-free atmosphere or vacuum at a dehydrogenation temperature below the ? transus temperature and above the ? phase decomposition temperature to remove hydrogen from the titanium material.

Abstract: A method of refining a microstructure of a titanium material can include providing a solid titanium material at a temperature below about 400° C. The titanium material can be heated under a hydrogen-containing atmosphere to a hydrogen charging temperature that is above a ? transus temperature of the titanium material and below a melting temperature of the titanium material, and held at this temperature for a time sufficient to convert the titanium material to a substantially homogeneous ? phase. The titanium material can be cooled under the hydrogen-containing atmosphere to a phase transformation temperature below the ? transus temperature and above about 400° C., and held for a time to produce ? phase regions. The titanium material can also be held under a substantially hydrogen-free atmosphere or vacuum at a dehydrogenation temperature below the ? transus temperature and above the ? phase decomposition temperature to remove hydrogen from the titanium material.

Abstract: A method of refining a microstructure of a titanium material can include providing a solid titanium material at a temperature below about 400° C. The titanium material can be heated under a hydrogen-containing atmosphere to a hydrogen charging temperature that is above a ? transus temperature of the titanium material and below a melting temperature of the titanium material, and held at this temperature for a time sufficient to convert the titanium material to a substantially homogeneous ? phase. The titanium material can be cooled under the hydrogen-containing atmosphere to a phase transformation temperature below the ? transus temperature and above about 400° C., and held for a time to produce ? phase regions. The titanium material can also be held under a substantially hydrogen-free atmosphere or vacuum at a dehydrogenation temperature below the ? transus temperature and above the ? phase decomposition temperature to remove hydrogen from the titanium material.

Abstract: A method of refining a microstructure of a titanium material can include providing a solid titanium material at a temperature below about 400° C. The titanium material can be heated under a hydrogen-containing atmosphere to a hydrogen charging temperature that is above a ? transus temperature of the titanium material and below a melting temperature of the titanium material, and held at this temperature for a time sufficient to convert the titanium material to a substantially homogeneous ? phase. The titanium material can be cooled under the hydrogen-containing atmosphere to a phase transformation temperature below the ? transus temperature and above about 400° C., and held for a time to produce ? phase regions. The titanium material can also be held under a substantially hydrogen-free atmosphere or vacuum at a dehydrogenation temperature below the ? transus temperature and above the ? phase decomposition temperature to remove hydrogen from the titanium material.

Abstract: A method of refining a microstructure of a titanium material can include providing a solid titanium material at a temperature below about 400° C. The titanium material can be heated under a hydrogen-containing atmosphere to a hydrogen charging temperature that is above a ? transus temperature of the titanium material and below a melting temperature of the titanium material, and held at this temperature for a time sufficient to convert the titanium material to a substantially homogeneous ? phase. The titanium material can be cooled under the hydrogen-containing atmosphere to a phase transformation temperature below the ? transus temperature and above about 400° C., and held for a time to produce ? phase regions. The titanium material can also be held under a substantially hydrogen-free atmosphere or vacuum at a dehydrogenation temperature below the ? transus temperature and above the ? phase decomposition temperature to remove hydrogen from the titanium material.

Abstract: A method for producing a substantially spherical metal powder is described. A particulate source metal includes a primary particulate and has an average starting particle size. The particulate source metal is optionally ball milled and mixed with a binder in a solvent to form a slurry. The slurry is granulated to form substantially spherical granules, wherein each granule comprises an agglomeration of particulate source metal in the binder. The granules are debinded at a debinding temperature to remove the binder from the granules forming debinded granules. The debinded granules are at least partially sintered at a sintering temperature such that particles within each granule fuse together to form partially or fully sintered solid granules. The granules can then be optionally recovered to form a substantially spherical metal powder.

Abstract: A method for producing a substantially spherical metal powder is described. A particulate source metal includes a primary particulate and has an average starting particle size. The particulate source metal is optionally ball milled and mixed with a binder in a solvent to form a slurry. The slurry is granulated to form substantially spherical granules, wherein each granule comprises an agglomeration of particulate source metal in the binder. The granules are debinded at a debinding temperature to remove the binder from the granules forming debinded granules. The debinded granules are at least partially sintered at a sintering temperature such that particles within each granule fuse together to form partially or fully sintered solid granules. The granules can then be optionally recovered to form a substantially spherical metal powder.

Abstract: A method for producing a substantially spherical metal powder is described. A particulate source metal includes a primary particulate and has an average starting particle size. The particulate source metal is optionally ball milled and mixed with a binder in a solvent to form a slurry. The slurry is granulated to form substantially spherical granules, wherein each granule comprises an agglomeration of particulate source metal in the binder. The granules are debinded at a debinding temperature to remove the binder from the granules forming debinded granules. The debinded granules are at least partially sintered at a sintering temperature such that particles within each granule fuse together to form partially or fully sintered solid granules. The granules can then be optionally recovered to form a substantially spherical metal powder.

Abstract: A functionally graded cemented tungsten carbide material produced via heat treating a sintered cemented tungsten carbide is disclosed and described. The heat treating process comprises at least a step that heats the sintered material to the multi-phase temperature range in which multiple phases including solid tungsten carbide, liquid metal binder, and solid metal binder coexist. Additionally, the material, after the heat treating process comprises a surface layer with lower metal binder content than the nominal value of metal binder content of the bulk of the material. The material is used to make tools for rock drilling, machining of metal alloys, and machining of non-metallic materials. The material can also be used to make engineered wear parts that are used in mechanical systems and applications where wear resistance is required or desired.

Abstract: A method for producing a substantially spherical metal powder is described. A particulate source metal includes a primary particulate and has an average starting particle size. The particulate source metal is optionally ball milled and mixed with a binder in a solvent to form a slurry. The slurry is granulated to form substantially spherical granules, wherein each granule comprises an agglomeration of particulate source metal in the binder. The granules are debinded at a debinding temperature to remove the binder from the granules forming debinded granules. The debinded granules are at least partially sintered at a sintering temperature such that particles within each granule fuse together to form partially or fully sintered solid granules. The granules can then be optionally recovered to form a substantially spherical metal powder.

Abstract: A method of preparing a functionally graded cemented tungsten carbide material via heat treating a sintered cemented tungsten carbide is disclosed and described. The heat treating process comprises at least a step that heats the sintered material to the multi-phase non-equilibrium temperature range in which multiple phases including solid tungsten carbide, liquid metal binder, and solid metal binder coexist. Additionally, the material, after the heat treating process comprises a surface layer with lower metal binder content than the nominal value of metal binder content of the bulk of the material.

Abstract: A functionally graded cemented tungsten carbide material produced via heat treating a sintered cemented tungsten carbide is disclosed and described. The heat treating process comprises at least a step that heats the sintered material to the multi-phase temperature range in which multiple phases including solid tungsten carbide, liquid metal binder, and solid metal binder coexist. Additionally, the material, after the heat treating process comprises a surface layer with lower metal binder content than the nominal value of metal binder content of the bulk of the material. The material is used to make tools for rock drilling, machining of metal alloys, and machining of non-metallic materials. The material can also be used to make engineered wear parts that are used in mechanical systems and applications where wear resistance is required or desired.

Abstract: The present disclosure provides compositions and methods directed to polycrystalline diamond materials. In one embodiment, a polycrystalline diamond material can comprise sintered polycrystalline diamond and a binder alloy, where the binder alloy is a liquid at a sintering temperature of the polycrystalline diamond, forms an intermetallic compound at a low temperature below the sintering temperature, and is substantially all intermetallic phase.

Abstract: A polycrystalline abrasive composite cutter, including a tool body with a top cutting surface and a flank surface. The composite cutter, joined to a substrate, constitute a shear cutter for a PDC bit, roller-cone bit insert, or other tool that can be highly useful for petroleum drilling or other applications. The body of the polycrystalline abrasive composite cutter includes a plurality of polycrystalline abrasive layers (90) and a plurality of arresting layers (100). The polycrystalline abrasive layers (90) and the arresting layers (100) are arranged to alternate throughout the tool body in a direction normal to the top cutting surface (92) and in a direction normal to a flank surface (94).

Abstract: A method of preparing a functionally graded cemented tungsten carbide material via heat treating a sintered cemented tungsten carbide is disclosed and described. The heat treating process comprises at least a step that heats the sintered material to the multi-phase non-equilibrium temperature range in which multiple phases including solid tungsten carbide, liquid metal binder, and solid metal binder coexist. Additionally, the material, after the heat treating process comprises a surface layer with lower metal binder content than the nominal value of metal binder content of the bulk of the material.

Abstract: A light metal solid solution alloy for reversible hydrogen storage can include a light metal solid solution alloy of M1 and M2. M1 and M2 are different and independently selected from the group consisting of Li, Mg, Al, Na, Be, and Si. Furthermore, the starting materials and formation conditions are chosen such that the resulting alloy has a hydrogenated state and a dehydrogenated state which are each solid solutions.

Abstract: A polycrystalline abrasive composite cutter, including a tool body with a top cutting surface and a flank surface. The composite cutter, joined to a substrate, constitute a shear cutter for a PDC bit, roller-cone bit insert, or other tool that can be highly useful for petroleum drilling or other applications. The body of the polycrystalline abrasive composite cutter includes a plurality of polycrystalline abrasive layers (90) and a plurality of arresting layers (100). The polycrystalline abrasive layers (90) and the arresting layers (100) are arranged to alternate throughout the tool body in a direction normal to the top cutting surface (92) and in a direction normal to a flank surface (94). According to the design, the arresting layers (100) can be oriented so as to substantially arrest crack propagation through the polycrystalline abrasive material.