144 results about "Titanium aluminide" patented technology

(a) The metal matrix composite is suitable for the manufacture of flat or shaped titanium aluminide, zirconium aluminide, or niobium aluminide articles and layered metal composites having improved mechanical properties such as lightweight plates and sheets for aircraft and automotive applications, thin cross-section vanes and airfoils, heat-sinking lightweight electronic substrates, bulletproof structures for vests, partition walls and doors, as well as sporting goods such as helmets, golf clubs, sole plates, crown plates, etc. The composite material consists of a metal (e.g., Ti, Zr, or Nb-based alloy) matrix at least partially intercalated with a three-dimensional skeletal metal aluminide structure, whereby ductility of the matrix metal is higher than that of the metal aluminide skeleton. The method for manufacturing includes the following steps: (a) providing an aluminum skeleton structure having open porosity of 50-95 vol. %, (b) filling said skeleton structure with the powder of a reactive matrix metal, (c) compacting the aluminum skeleton/matrix powder composite preform by cold rolling, cold die pressing, cold isostatic pressing, and/or hot rolling, (d) consolidating the initial or compacted composite preform by sintering, hot pressing, hot rolling, hot isostatic pressing, and/or hot extrusion to provide, at least partially, a reaction between aluminum skeleton and matrix metal powder, and (e) diffusion annealing followed by any type of heat treatment needed to provide predetermined mechanical and surface properties of the resulting metal matrix composite. The combination of ductile matrix and metal aluminide skeletal structure results in significant improvement of mechanical properties of the composite material, especially hot strength. This high-strength aluminide-based material can also be used as a core component in multilayer metal matrix composites.

Methods for making various titanium base alloys and titanium aluminides into engineering components such as rings, tubes and pipes by melting of the alloys in a vacuum or under a low partial pressure of inert gas and subsequent centrifugal casting of the melt in the graphite molds rotating along its own axis under vacuum or low partial pressure of inert gas are provided, the molds having been fabricated by machining high density, high strength ultrafine grained isotropic graphite, wherein the graphite has been made by isostatic pressing or vibrational molding, the said molds either revolving around its own horizontal or vertical axis or centrifuging around a vertical axis of rotation.

Electronics packages having a primary metallic material, such as a titanium metallic material, metallurgically bonded to one or more secondary regions within the primary metallic material, the composite regions having desirable thermal conductivity properties and having a coefficient of thermal expansion ("CTE") that generally matches the CTE of the primary metallic material are provided. Electronics packages comprising titanium having heat sinks comprising a metal matrix material such as aluminum silicon carbide or a composite metallic structure such as titanium aluminide/copper, are described. Methods for manufacturing electronics packages having a composite structure are also disclosed.

A filter such as a cigarette filter having a metal reagent which selectively binds with a gaseous component of a gas stream such as tobacco smoke. The metal reagent comprises nanometer or micrometer size clusters of a transition metal or alloy containing a transition metal. The transition metal can be incorporated in an intermetallic compound such as titanium aluminide or iron aluminide. The metal clusters can be incorporated in or on a support material such as silica gel, porous carbon or a zeolite. The metal reagent can remove the gaseous component by selectively binding to unsaturated hydrocarbons such as 1,3-butadiene. The binding can occur by insertion of a metal atom of the metal reagent into a C—H bond or a C—C bond of the gaseous component.

A titanium-aluminide turbine wheel (120, 220, 320, 420) is joined to the end of a shaft (110, 210, 310, 410) by utilizing a titanium surface on the end of the shaft to be joined to the wheel, and electron-beam welding the wheel onto the titanium surface on the shaft. A steel shaft (110, 310, 410) can have a titanium-containing end piece (130, 330, 430) mechanically joined (by brazing, bonding, or welding) to the end of the shaft, and the end piece can be directly electron-beam welded to the wheel. Alternatively, the shaft (210) can be formed as a titanium member and the end (212) of the shaft can be directly electron-beam welded to the wheel (220). In another embodiment, a ferrous end piece (330) is mechanically joined to the titanium-aluminide turbine wheel (320) and then the end piece is directly electron-beam welded to the end of a steel shaft (310). Alternatively, a silver-titanium alloy member (430) is sandwiched between the wheel (420) and a steel shaft (410) and is melted to join the parts together.

A rotor shaft assembly (101) of a type used in a turbocharger, manufactured by mounting a powder compact of a titanium aluminide rotor (203) to a powder compact of a steel shaft (207), with a metal powder admixed with a binder (211) interposed between the rotor and shaft, and debinding and sintering the mounted compact combination. Sintering produces a strong metallurgical bond between the shaft and rotor, providing a near-net rotor shaft assembly (101) and also an inexpensive and efficient method for the manufacture of an assembly capable of withstanding the high forces and temperatures within a turbocharger.

Lightweight metal matrix composites containing a skeleton structure of titanium, titanium aluminide, or Ti-based alloy are manufactured by low temperature infiltration with molten Mg-based alloy or Mg-Al alloy at 450-750° C., with molten In, Pb, or Sn at 300-450° C., or with molten Ag and Cu at 900-1100° C. The skeleton structure with a density of 25-35% is produced by loose sintering of Ti or Ti-based alloy powders. A primary deformation of the Ti skeleton structure before the infiltration is carried out by cold or hot rolling or forging to obtain a porous flat or shaped preform with a porosity <50% and pores drawn out in one direction such as the direction of future rolling of the composite plate. A secondary deformation of the infiltrated preform is carried out by multistage cold, or especially hot rolling, to refine the microstructure of the infiltrated skeleton structure and transform it into the textured microstructure strengthened by intermetallic phases such as TiAl, Ti3Al, and TiAl3. Subsequent re-sintering or diffusion annealing form a fully dense final structure of the resulting material having improved mechanical properties. The molten Mg-based infiltrate is alloyed with Al, Si, Zr, Nb, and/or V with the addition of TiB2, SiC, and Si3N4 sub-micron particles as infiltration promoters. The molten Ag- or Cu-based infiltrate can be alloyed with elements depressing its melting point. The method allows for control of the microstructure of composite materials by changing parameters of deformation, infiltration, and heat treatment. The method is suitable for the manufacture of flat or shaped metal matrix composites having improved ductility, such as lightweight bulletproof plates and sheets for aircraft and automotive applications, composite electrodes, heat-sinking lightweight electronic substrates, sporting goods such as helmets, golf clubs, sole plates, crown plates, etc.

The lightweight bulletproof metal matrix macrocomposites (MMMC) contain (a) 10-99 vol. % of permeable skeleton structure of titanium, titanium aluminide, Ti-based alloys, and/or mixtures thereof infiltrated with low-melting metal selected from Al, Mg, or their alloys, and (b) 1-90 vol. % of ceramic and/or metal inserts positioned within said skeleton, whereby a normal projection area of each of said inserts is equal to or larger than the cross-section area of a bullet or a projectile body. The MMMC are manufactured as flat or solid-shaped, double-layer, or multi-layer articles containing the same inserts or different inserts in each layer, whereby insert projections of each layer cover spaces between inserts of the underlying layer. The infiltrated metal contains 1-70 wt. % of Al and Mg in the balance, optionally, alloyed with Ti, Si, Zr, Nb, V, as well as with 0-3 wt. % of TiB2, SiC, or Si3N4 sub-micron powders, to promote infiltrating and wetting by Al-containing alloys. The manufacture includes (a) forming the permeable metal powder and inserts into the skeleton-structured preform by positioning inserts in the powder followed by loose sintering in vacuum to provide the average porosity of 20-70%, (b) heating and infiltrating the porous preform with molten infiltrating metal for 10-40 min at 450-750° C., (c) hot isostatic pressing of the infiltrated composite, and (d) re-sintering or diffusion annealing. The positioning of the ceramic inserts in Ti-based powder is carried out by using a metal grid aiding the placement of inserts in a predetermined geometric pattern, and said grid becomes the integral part of the macrocomposite material. The technology is suitable for the manufacture of flat or shaped metal matrix macrocomposites having improved ductility and impact energy absorption such as lightweight bulletproof plates and sheets for airplane, helicopter, and automotive applications.

Methods for making various metallic alloys such as nickel, cobalt and/or iron based superalloys, stainless steel alloys, titanium alloys and titanium aluminide alloys into engineering components by melting of the alloys in a vacuum or under a low partial pressure of inert gas and subsequent casting of the melt in the graphite molds under vacuum or low partial pressure of inert gas are provided, the molds having been fabricated by machining high density, high strength ultrafine grained isotropic graphite, wherein the graphite has been made by isostatic pressing or vibrational molding.

A process for producing sheets of γ-TiAl includes the steps of forming a melt of a γ-TiAl alloy; casting the γ-TiAl alloy to form an as-cast γ-TiAl alloy; encapsulating the as-cast γ-TiAl alloy to form an as-cast γ-TiAl alloy preform; and rolling the as-cast γ-TiAl alloy preform to form a sheet comprising γ-TiAl.

The present disclosure includes a turbocharger. The turbocharger may include a titanium-aluminide turbine and a shaft. A single joint connects the turbine to the shaft. The joint may include an alloy comprising at least 80 atomic percent nickel and palladium.

Molds are fabricated having a substrate of high density, high strength ultrafine grained isotropic graphite, and having a mold cavity coated with titanium carbide. The molds may be made by making the substrate (main body) of high density, high strength ultrafine grained isotropic graphite, by, for example, isostatic or vibrational molding, machining the substrate to form the mold cavity, and coating the mold cavity with titanium carbide via either chemical deposition or plasma assisted chemical vapor deposition, magnetron sputtering or sputtering. The molds may be used to make various metallic alloys such as nickel, cobalt and iron based superalloys, stainless steel alloys, titanium alloys and titanium aluminide alloys into engineering components by melting the alloys in a vacuum or under a low partial pressure of inert gas and subsequently casting the melt in the graphite molds under vacuum or low partial pressure of inert gas.

The present disclosure includes a turbocharger. The turbocharger may include a turbine that includes titanium-aluminide and a shaft that includes titanium. A single joint connects the turbine to the shaft.

Molds are fabricated having a substrate of high density, high strength ultrafine grained isotropic graphite, and having a mold cavity coated with pyrolytic graphite. The molds may be made by making the substrate (main body) of high density, high strength ultrafine grained isotropic graphite, by, for example, isostatic or vibrational molding, machining the substrate to form the mold cavity, and coating the mold cavity with pyrolytic graphite via a chemical deposition process. The molds may be used to make various metallic alloys such as nickel, cobalt and iron based superalloys, stainless steel alloys, titanium alloys and titanium aluminide alloys into engineering components by melting the alloys in a vacuum or under a low partial pressure of inert gas and subsequently casting the melt in the graphite molds under vacuum or low partial pressure of inert gas.