US20050268746A1 - Titanium tungsten alloys produced by additions of tungsten nanopowder - Google Patents
Titanium tungsten alloys produced by additions of tungsten nanopowder Download PDFInfo
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- A—HUMAN NECESSITIES
- A61—MEDICAL OR VETERINARY SCIENCE; HYGIENE
- A61L—METHODS OR APPARATUS FOR STERILISING MATERIALS OR OBJECTS IN GENERAL; DISINFECTION, STERILISATION OR DEODORISATION OF AIR; CHEMICAL ASPECTS OF BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES; MATERIALS FOR BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES
- A61L27/00—Materials for grafts or prostheses or for coating grafts or prostheses
- A61L27/02—Inorganic materials
- A61L27/04—Metals or alloys
- A61L27/06—Titanium or titanium alloys
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- A—HUMAN NECESSITIES
- A61—MEDICAL OR VETERINARY SCIENCE; HYGIENE
- A61L—METHODS OR APPARATUS FOR STERILISING MATERIALS OR OBJECTS IN GENERAL; DISINFECTION, STERILISATION OR DEODORISATION OF AIR; CHEMICAL ASPECTS OF BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES; MATERIALS FOR BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES
- A61L31/00—Materials for other surgical articles, e.g. stents, stent-grafts, shunts, surgical drapes, guide wires, materials for adhesion prevention, occluding devices, surgical gloves, tissue fixation devices
- A61L31/02—Inorganic materials
- A61L31/022—Metals or alloys
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/12—Metallic powder containing non-metallic particles
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/045—Alloys based on refractory metals
- C22C1/0458—Alloys based on titanium, zirconium or hafnium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
- C22C27/04—Alloys based on tungsten or molybdenum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
Definitions
- titanium-tungsten alloys and composites Disclosed herein are titanium-tungsten alloys and composites. Also disclosed is a method of making such alloys and composites using nanopowders of tungsten and optionally comprising slow-diffusing beta stabilizers, such as but not limited to V, Nb, Mo, and Ta.
- beta stabilizers such as but not limited to V, Nb, Mo, and Ta.
- W While Ti alloys strengthened by W are generally desirable because they are strong wear resistant alloys, such alloys are difficult, if not impossible, to prepare by typical techniques. For example, in a casting process, W generally completely dissolves in the molten Ti during the melting step. As the resulting ingot solidifies beta-rich large, elongated islands form between the dendrites of the solidified casting. These resulting defects lead to poor mechanical properties in the final product.
- Ti—W alloys are mentioned in the literature for use as sputtering targets and in thin film applications; however, these alloys are tungsten (W) based with typically 10% or less Ti.
- Literature that does describe Ti based alloys comprising W describes W being added to form a particulate dispersion.
- M. Frary, S. M. Abkowitz, and D. C. Dunand “Microstructure and Mechanical Properties of Ti/W and Ti-6Al-4V/W Composites Fabricated by Powder-Metallurgy,” Materials Science and Engineering A344 (2003) 103-112, which is herein incorporated by reference, shows that partially diffused W dispersions in Ti powder (Commercially Pure “CP” Ti) and Ti-based alloys (Ti-6Al-4V) increases strength with an acceptable loss in ductility.
- the alloys described in Frary et al. comprise 3 ⁇ m to 10 ⁇ m tungsten powders that are too large to completely diffuse.
- nanopowder is defined as powders less than 1 micron, such as powders ranging from about 8 angstroms (the detection limit of electron microscopy) to less than 1 micron.
- W nanopowder in the preparation of Ti—W alloys allows the W to completely diffuse into the Ti matrix during a typical P/M sintering cycle.
- completely diffused W nanopowder forms an alpha/beta or all beta microstructure, or as alpha/beta or all beta microstructure containing a dispersion described as “beta phase islands.”
- Beta phase islands are a microscopic beta rich structure dispersed throughout an alpha, alpha/beta or all-beta microstructure.
- These dispersions result in Ti/W alloys with properties that are superior to a dispersion of partially diffused W particulates produced using Ti powder 3 ⁇ m or larger.
- the commercially pure (CP) Ti with 10% W containing dispersions of beta phase islands can have properties superior to Ti-6Al4V.
- the Ti-6Al-4V with 10% W can have annealed properties equivalent to the highly alloyed all-beta alloys that require solution treatment and aging to fully develop their properties (e.g. Ti-13V-11 Cr-3Al).
- W nanopowder can be blended with CP (commercially pure) Ti powder and, in the case of an alloy, blended with Ti powder, other elemental powders or with master alloy powders, which is defined as the mixture of starting metal powders used to form the resulting alloy by powder metallurgy processing.
- the powder blend is compacted, sintered and may or may not be hot isostatic pressed.
- the product may be subjected to additional processing, such as, forging, casting, or extrusion.
- a casting billet may also be prepared in the manner described above and then cast to shape.
- Ti—W master alloy additions can also be prepared by the methods disclosed in this invention. These master alloy additions can be used in casting of Ti—W or may be made into master alloy powder by attrition for use in P/M processing.
- the total diffusion of W results in an alpha/beta phase microstructure in CP titanium typical of commercial alpha/beta alloys. In alpha/beta alloys the total diffusion of W results in a near beta or all beta microstructure.
- the Ti—W alloys also have properties that are superior to conventional Ti-6Al-4V. Further the Ti—W alpha/beta and all-beta alloys can be solution treated and aged in much the same way as conventional heat treatable Ti alloys.
- this uniform dispersion of beta phase islands can be controlled within the Ti matrix by adjusting the P/M sintering time and/or by manipulating the W powder size to a range from 8 angstroms to less then 3 ⁇ m, such as less than 1 ⁇ m.
- the beta phase island dispersion results in improved room and elevated temperature properties.
- the above-described method based on tungsten (W) can be used with other beta stabilizers, such as but not limited to V, Nb, Mo, and Ta.
- the powder size of the particular beta stabilizer is related to the beta stabilizer's diffusivity at the sintering temperature of Ti.
- the creation of a uniform dispersion of beta phase is dependent on, among other things, the size of the beta stabilizer powder.
- the beta stabilizer powder is less then 3 ⁇ m, such as less than 1 ⁇ m.
- the powder size used according to the present disclosure is also related to the beta stabilizer's diffusivity at the sintering temperature.
- the powder size range can depend on the desired matrix microstructure (i.e. alpha/beta or all beta), the size and number of beta phase islands and the desired amount of partially diffused beta stabilizer (residual undiffused particulate) with the beta phase islands, such as at the center of the beta phase islands.
- Partially dissolved particles of the beta-stabilizing addition such as partially dissolved particles of W, V, Nb, Mo, or Ta, may be present within, such as at the center of, the beta phase islands and may contribute to the strengthening mechanism.
- Ti metal matrix composites containing particulate reinforcement of titanium carbide (TiC), titanium boride (TiB) or titanium diboride (TiB 2 ) can also be enhanced by W nanopowder additions or the addition of sub-sieve sized powder of other beta stabilizers.
- FIG. 1 is a scanning electron micrograph of a titanium-tungsten alloy according to the present invention.
- One aspect of the present disclosure is directed to a composition of a titanium based alloy comprising a titanium material and tungsten in an amount ranging from 0.5% to 40% by weight.
- the W powder addition used to make the alloy has an average diameter of less then 3 ⁇ m in size, such as less than 1 ⁇ m, and ranging from 8 angstroms to less then 1 ⁇ m as measured by the Fisher sub-screen size method, electron microscopy and/or photon correlation spectroscopy.
- the titanium in the Ti/W alloy described herein may comprise CP Ti powder or a Ti alloy, such as Ti-6Al-4V.
- the composition may comprise an alternative or additional slow diffusing beta stabilizer chosen from but not limited to V, Nb, Mo, and Ta. Such stabilizers will lead to an alloy containing dispersions of beta phase islands or an all beta structure with dispersions of partially dissolved beta stabilizer.
- the beta phase islands contain undiffused particulate beta stabilizer at the core of the islands.
- Beta flecks are generally a form of beta phase islands that are well-known as a defect. See, for example, “Powder Metallurgy of Titanium Alloys,” by Froes and Smugeresky, The Metallurgical Society of AIME, Warrendale, Pa. 1980; ASM Online Handbook, “Wrought Titanium and Titanium Alloys—Wrought Titanium Processing,”; “Processing of Titanium and Titanium Alloys—Secondary Fabrication,” Y. G. Zhou, J. L. Tang, H. Q. Yu, and W. D.
- beta fleck defects The occurrence of beta fleck defects is generally unpredictable, and usually results in poor properties, and thus may lead to the premature failure of a component. Contrary to the teachings of the prior art, the present disclosure provides for the creation of uniform dispersions of beta phase islands that can improve the mechanical properties of Ti and its alloys.
- the beta fleck defect occurs in alpha-beta and near beta alloys where segregation of alloying elements results in localized regions depleted in alpha stabilizers (e.g. aluminum) or with an excess of beta stabilizers (e.g. molybdenum). These regions then transform to the beta phase resulting in beta flecks. Contamination of powder or castings by tramp particles of a beta stabilizer, such as W, can also result in beta flecks.
- alpha stabilizers e.g. aluminum
- beta stabilizers e.g. molybdenum
- the alloy has a microstructure that comprises all-alpha phase, alpha/beta phases and all beta phase, or all-alpha phase and alpha/beta phases comprising a dispersion of beta phase islands.
- the beta phase islands optionally include partially diffused beta stabilizer within the beta phase islands, such as at the center of the beta phase islands.
- the part may be further processed by techniques including, but not limited to casting, forging, and extrusion.
- the alloy described herein may be used in implantable medical devices, such as orthopedic implants, including spinal implants, disc prostheses, nucleus prostheses, bone fixation devices, bone plates, spinal rods, rod connectors, knees, and hip prostheses, dental implants, implantable tubes, wires, and electrical leads.
- implantable medical devices such as orthopedic implants, including spinal implants, disc prostheses, nucleus prostheses, bone fixation devices, bone plates, spinal rods, rod connectors, knees, and hip prostheses, dental implants, implantable tubes, wires, and electrical leads.
- the alloy may be used in drug delivery devices, including stents.
- the alloy disclosed herein may also be formed into a product, such as a billet for further processing.
- the product may be an automotive component such as valves, conrods, and piston pins.
- the product may also comprise an armored vehicle component such as tank track center guides and undercarriage parts.
- an armored vehicle component such as tank track center guides and undercarriage parts.
- the product may comprise a tool or die material for metal casting.
- the product may also be an aircraft component such as a turbine rotor, and a leading edge of a helicopter rotor blade.
- the present invention is further illuminated by the following non-limiting example, which is intended to be purely exemplary of the invention.
- a powder metallurgy technique was used to produce a tungsten containing titanium alloy. Using this method, beta phase island dispersions were created in CP Ti and in Ti-6Al-4V with 10% by weight W.
- nanopowder 30 to 45 nanometers (0.003 to 0.004 ⁇ m) in size with a specific surface area of between 7 to 10 m 2 /g was blended with CP Ti powder and processed as described above. These W nanopowders were also blended with CP Ti and master alloy powders to form the Ti-6Al-4V composition shown in Table 1.
- the W nanopowder was taken into solution in the Ti matrix on sintering the compacted blend, forming an alpha/beta structure with a uniform beta phase island dispersion.
- FIG. 1 shows that the W nanopowder completely diffused to form a beta phase island dispersion in the alpha/beta matrix.
- the diffusion of the W nanopowder transformed the all alpha microstructure typical of CP Ti to alpha/beta containing a dispersion of beta phase islands. In this case there was no evidence of any undissolved W.
- Table 1 shows that 10% W nano-sized powder addition substantially improved the strength of CP Ti resulting in twice the strength of CP Ti, as well as a higher strength then Ti-6Al-4V with roughly equivalent ductility.
- the W nanopowder addition resulted in a 30% improvement in strength while maintaining satisfactory ductility.
Abstract
Disclosed herein are titanium-tungsten alloys and composites wherein the tungsten comprises 0.5% to 40% by weight of the alloy. Also disclosed is a method of making such alloys and composites using powders of tungsten less then 3 μm in size, such as 1 μm or less. Also disclosed is a method of making the titanium alloy by powder metallurgy, and products made from such alloys or billets that may be cast, forged, or extruded. These methods of production can be used to make titanium alloys comprising other slow-diffusing beta stabilizers, such as but not limited to V, Nb, Mo, and Ta.
Description
- This application claims the benefit of domestic priority to U.S. Provisional Patent Application Ser. No. 60/563,009, filed Apr. 19, 2004, which is herein incorporated by reference in its entirety.
- Disclosed herein are titanium-tungsten alloys and composites. Also disclosed is a method of making such alloys and composites using nanopowders of tungsten and optionally comprising slow-diffusing beta stabilizers, such as but not limited to V, Nb, Mo, and Ta.
- While Ti alloys strengthened by W are generally desirable because they are strong wear resistant alloys, such alloys are difficult, if not impossible, to prepare by typical techniques. For example, in a casting process, W generally completely dissolves in the molten Ti during the melting step. As the resulting ingot solidifies beta-rich large, elongated islands form between the dendrites of the solidified casting. These resulting defects lead to poor mechanical properties in the final product.
- Until the present disclosure, the preparation of Ti—W by powder metallurgy (P/M), was not commercially viable because of the high melting point and slow diffusivity associated with W that causes it to remain segregated as discrete or undissolved particles. Ti—W alloys are mentioned in the literature for use as sputtering targets and in thin film applications; however, these alloys are tungsten (W) based with typically 10% or less Ti.
- Literature that does describe Ti based alloys comprising W describes W being added to form a particulate dispersion. For example, M. Frary, S. M. Abkowitz, and D. C. Dunand, “Microstructure and Mechanical Properties of Ti/W and Ti-6Al-4V/W Composites Fabricated by Powder-Metallurgy,” Materials Science and Engineering A344 (2003) 103-112, which is herein incorporated by reference, shows that partially diffused W dispersions in Ti powder (Commercially Pure “CP” Ti) and Ti-based alloys (Ti-6Al-4V) increases strength with an acceptable loss in ductility. The alloys described in Frary et al. comprise 3 μm to 10 μm tungsten powders that are too large to completely diffuse.
- The present disclosure avoids the aforementioned problems by using tungsten nanopowder. As used herein, nanopowder is defined as powders less than 1 micron, such as powders ranging from about 8 angstroms (the detection limit of electron microscopy) to less than 1 micron. The Inventors have discovered that the use of W nanopowder in the preparation of Ti—W alloys allows the W to completely diffuse into the Ti matrix during a typical P/M sintering cycle.
- In one embodiment, completely diffused W nanopowder forms an alpha/beta or all beta microstructure, or as alpha/beta or all beta microstructure containing a dispersion described as “beta phase islands.” Beta phase islands are a microscopic beta rich structure dispersed throughout an alpha, alpha/beta or all-beta microstructure. These dispersions result in Ti/W alloys with properties that are superior to a dispersion of partially diffused W particulates produced using Ti powder 3 μm or larger. In fact, the commercially pure (CP) Ti with 10% W containing dispersions of beta phase islands can have properties superior to Ti-6Al4V. In addition, the Ti-6Al-4V with 10% W can have annealed properties equivalent to the highly alloyed all-beta alloys that require solution treatment and aging to fully develop their properties (e.g. Ti-13V-11 Cr-3Al).
- In accordance with the present disclosure, W nanopowder can be blended with CP (commercially pure) Ti powder and, in the case of an alloy, blended with Ti powder, other elemental powders or with master alloy powders, which is defined as the mixture of starting metal powders used to form the resulting alloy by powder metallurgy processing. The powder blend is compacted, sintered and may or may not be hot isostatic pressed. The product may be subjected to additional processing, such as, forging, casting, or extrusion.
- A casting billet may also be prepared in the manner described above and then cast to shape. Ti—W master alloy additions can also be prepared by the methods disclosed in this invention. These master alloy additions can be used in casting of Ti—W or may be made into master alloy powder by attrition for use in P/M processing.
- The total diffusion of W, as disclosed herein, results in an alpha/beta phase microstructure in CP titanium typical of commercial alpha/beta alloys. In alpha/beta alloys the total diffusion of W results in a near beta or all beta microstructure. The Ti—W alloys also have properties that are superior to conventional Ti-6Al-4V. Further the Ti—W alpha/beta and all-beta alloys can be solution treated and aged in much the same way as conventional heat treatable Ti alloys.
- Disclosed herein is a method of making an alloy having a uniform dispersion of beta phase islands within a Ti matrix. According to this aspect, this uniform dispersion of beta phase islands can be controlled within the Ti matrix by adjusting the P/M sintering time and/or by manipulating the W powder size to a range from 8 angstroms to less then 3 μm, such as less than 1 μm. The beta phase island dispersion results in improved room and elevated temperature properties.
- In another aspect of the disclosure, the above-described method based on tungsten (W) can be used with other beta stabilizers, such as but not limited to V, Nb, Mo, and Ta. In this embodiment, the powder size of the particular beta stabilizer is related to the beta stabilizer's diffusivity at the sintering temperature of Ti.
- The creation of a uniform dispersion of beta phase is dependent on, among other things, the size of the beta stabilizer powder. In one embodiment, the beta stabilizer powder is less then 3 μm, such as less than 1 μm. The powder size used according to the present disclosure is also related to the beta stabilizer's diffusivity at the sintering temperature. In addition, the powder size range can depend on the desired matrix microstructure (i.e. alpha/beta or all beta), the size and number of beta phase islands and the desired amount of partially diffused beta stabilizer (residual undiffused particulate) with the beta phase islands, such as at the center of the beta phase islands.
- Partially dissolved particles of the beta-stabilizing addition, such as partially dissolved particles of W, V, Nb, Mo, or Ta, may be present within, such as at the center of, the beta phase islands and may contribute to the strengthening mechanism.
- The properties of Ti metal matrix composites containing particulate reinforcement of titanium carbide (TiC), titanium boride (TiB) or titanium diboride (TiB2) can also be enhanced by W nanopowder additions or the addition of sub-sieve sized powder of other beta stabilizers.
- The accompanying micrograph that is incorporated in and constitutes a part of this specification, illustrates one embodiment of the invention and together with the description, serve to explain the principles of the disclosure.
-
FIG. 1 is a scanning electron micrograph of a titanium-tungsten alloy according to the present invention. - One aspect of the present disclosure is directed to a composition of a titanium based alloy comprising a titanium material and tungsten in an amount ranging from 0.5% to 40% by weight. In one embodiment, the W powder addition used to make the alloy has an average diameter of less then 3 μm in size, such as less than 1 μm, and ranging from 8 angstroms to less then 1 μm as measured by the Fisher sub-screen size method, electron microscopy and/or photon correlation spectroscopy.
- The titanium in the Ti/W alloy described herein may comprise CP Ti powder or a Ti alloy, such as Ti-6Al-4V.
- The composition may comprise an alternative or additional slow diffusing beta stabilizer chosen from but not limited to V, Nb, Mo, and Ta. Such stabilizers will lead to an alloy containing dispersions of beta phase islands or an all beta structure with dispersions of partially dissolved beta stabilizer. In one embodiment, the beta phase islands contain undiffused particulate beta stabilizer at the core of the islands.
- As described in the prior art, “beta flecks”, are generally a form of beta phase islands that are well-known as a defect. See, for example, “Powder Metallurgy of Titanium Alloys,” by Froes and Smugeresky, The Metallurgical Society of AIME, Warrendale, Pa. 1980; ASM Online Handbook, “Wrought Titanium and Titanium Alloys—Wrought Titanium Processing,”; “Processing of Titanium and Titanium Alloys—Secondary Fabrication,” Y. G. Zhou, J. L. Tang, H. Q. Yu, and W. D. Zeng, “Effects of Beta Fleck on the Properties of Ti-10V-2Fe-3Al Alloy,” Titanium 1992 Science and Technology, The Minerals, Metals and Materials Society, Warrendale, Pa. 1992, Vol 1, pp 513-521; and http://mse-p012.eng.ohio-state.edu/fraser/mse663/AlphaBeta JCW.pdf, “Properties and Applications of α+β Ti Alloys, which are all incorporated herein by reference.
- The occurrence of beta fleck defects is generally unpredictable, and usually results in poor properties, and thus may lead to the premature failure of a component. Contrary to the teachings of the prior art, the present disclosure provides for the creation of uniform dispersions of beta phase islands that can improve the mechanical properties of Ti and its alloys. The beta fleck defect occurs in alpha-beta and near beta alloys where segregation of alloying elements results in localized regions depleted in alpha stabilizers (e.g. aluminum) or with an excess of beta stabilizers (e.g. molybdenum). These regions then transform to the beta phase resulting in beta flecks. Contamination of powder or castings by tramp particles of a beta stabilizer, such as W, can also result in beta flecks.
- The present disclosure teaches that controlled dispersions of the so-called “beta fleck”, herein termed “beta phase islands”, can be beneficial and improve the properties of titanium and its alloys.
- In another embodiment, the alloy has a microstructure that comprises all-alpha phase, alpha/beta phases and all beta phase, or all-alpha phase and alpha/beta phases comprising a dispersion of beta phase islands. The beta phase islands optionally include partially diffused beta stabilizer within the beta phase islands, such as at the center of the beta phase islands.
- Also described herein is a powder metallurgical method of making the above-described composition. This method comprises:
-
- blending a titanium material powder with a tungsten powder to form a blended powder that comprises from 0.5% to 40% by weight of tungsten powder having an average diameter less then 3 μm in size, such as ranging from 8 angstroms to less than 1 μm, such as ranging from 10 nm to 500 nm;
- compacting the blended powder; and
- sintering the compacted and blended powder, wherein
- the sintered compact can then be hot isostatically pressed if necessary.
- After powder metallurgical processing as described above the part may be further processed by techniques including, but not limited to casting, forging, and extrusion.
- In one embodiment, the alloy described herein may be used in implantable medical devices, such as orthopedic implants, including spinal implants, disc prostheses, nucleus prostheses, bone fixation devices, bone plates, spinal rods, rod connectors, knees, and hip prostheses, dental implants, implantable tubes, wires, and electrical leads. In other embodiments, the alloy may be used in drug delivery devices, including stents.
- The alloy disclosed herein may also be formed into a product, such as a billet for further processing. In other embodiment, the product may be an automotive component such as valves, conrods, and piston pins.
- The product may also comprise an armored vehicle component such as tank track center guides and undercarriage parts.
- In another embodiment, the product may comprise a tool or die material for metal casting.
- The product may also be an aircraft component such as a turbine rotor, and a leading edge of a helicopter rotor blade.
- All amounts, percentages, and ranges expressed herein are approximate.
- The present invention is further illuminated by the following non-limiting example, which is intended to be purely exemplary of the invention.
- A powder metallurgy technique was used to produce a tungsten containing titanium alloy. Using this method, beta phase island dispersions were created in CP Ti and in Ti-6Al-4V with 10% by weight W. In this example, nanopowder 30 to 45 nanometers (0.003 to 0.004 μm) in size with a specific surface area of between 7 to 10 m2/g was blended with CP Ti powder and processed as described above. These W nanopowders were also blended with CP Ti and master alloy powders to form the Ti-6Al-4V composition shown in Table 1.
- The W nanopowder was taken into solution in the Ti matrix on sintering the compacted blend, forming an alpha/beta structure with a uniform beta phase island dispersion.
-
FIG. 1 shows that the W nanopowder completely diffused to form a beta phase island dispersion in the alpha/beta matrix. The diffusion of the W nanopowder transformed the all alpha microstructure typical of CP Ti to alpha/beta containing a dispersion of beta phase islands. In this case there was no evidence of any undissolved W. - Table 1 shows that 10% W nano-sized powder addition substantially improved the strength of CP Ti resulting in twice the strength of CP Ti, as well as a higher strength then Ti-6Al-4V with roughly equivalent ductility. In the Ti-6Al-4V containing composition, the W nanopowder addition resulted in a 30% improvement in strength while maintaining satisfactory ductility.
TABLE 1 The Effect of 10% W Nano-sized Powder Addition on the Mechanical Properties of CP Ti and Ti-6Al-4V Ultimate Tensile Yield Reduction Material Strength Strength in Area Composition (psi) (psi) Elongation (%) (%) Ti 75,110 59,595 24 46 Ti + 10% W 147,320 131,515 15 37 Ti-6Al-4V 137,605 124,700 14 28 Ti-6Al-4V + 10% W 178,350 171,100 9 20 - Unless otherwise indicated, all numbers expressing quantities of ingredients, reaction conditions, and so forth used in the specification and claims are to be understood as being modified in all instances by the term “about.” Accordingly, unless indicated to the contrary, the numerical parameters set forth in the following specification and attached claims are approximations that may vary depending upon the desired properties sought to be obtained by the present invention.
- Other embodiments of the invention will be apparent to those skilled in the art from consideration of the specification and practice of the invention disclosed herein. It is intended that the specification and examples be considered as exemplary only, with a true scope and spirit of the invention being indicated by the following claims.
Claims (32)
1. A composition comprising a titanium alloy, said alloy comprising tungsten in an amount ranging from 0.5% to 40% by weight of said alloy, wherein the tungsten has an average diameter less then 3 μm in size.
2. The composition of claim 1 , wherein the tungsten powder has an average diameter ranging from 8 angstroms to 1 μm or less.
3. The composition of claim 2 , wherein the tungsten powder has an average diameter ranging from 10 nm to 500 nm.
4. The composition of claim 1 , comprising at least one beta stabilizer chosen from V, Nb, Mo, and Ta.
5. The composition of claim 1 , wherein said alloy comprises dispersions of beta phase islands.
6. The composition of claim 5 , wherein said beta phase islands comprise undiffused particulate beta stabilizer at the core of said islands.
7. The composition of claim 1 , wherein said titanium material comprises a material chosen from Ti powder and Ti alloy.
8. The composition of claim 1 , wherein said alloy has a microstructure that comprises alpha/beta phases, all beta phases, or alpha/beta phases comprising a dispersion of beta phase islands.
9. The composition of claim 8 , wherein said beta phase islands include partially diffused beta stabilizer within the beta phase islands.
10. The composition of claim 1 , further comprising at least one particulate material chosen from titanium carbide (TiC), titanium boride (TiB), titanium diboride (TiB2) or combinations thereof.
11. A powder metallurgy method of producing a tungsten comprising titanium alloy, said method comprising:
blending a titanium containing powder with a tungsten containing powder to form a blended powder, said blended powder comprising tungsten powder in an amount ranging from 0.5% to 40% by weight of said alloy, wherein said tungsten powder has an average diameter less then 3 μm in size;
compacting the blended powder;
sintering the compacted and blended powder to form a tungsten containing titanium alloy; and
optionally subjecting the sintered tungsten containing titanium alloy to hot isostatic pressing.
12. The method of claim 11 , further comprising subjecting the sintered tungsten containing titanium alloy to a process chosen from casting, forging, and extrusion.
13. The method of claim 11 , wherein the tungsten containing powder has an average diameter ranging from 8 angstroms to 1 μm or less.
14. The method of claim 13 , wherein the tungsten containing powder has an average diameter ranging from 10 to 500 nm.
15. The method of claim 11 , wherein the blended powder further comprises at least one beta stabilizer chosen from V, Nb, Mo, and Ta.
16. The method of claim 11 , wherein the blended powder further comprises at least one particulate material chosen from titanium carbide (TiC), titanium boride (TiB), titanium diboride (TiB2) or combinations thereof.
17. The method of claim 11 , wherein said tungsten containing titanium alloy contains dispersions of beta phase islands.
18. The method of claim 17 , wherein said beta phase islands contain residual beta stabilizer at the core.
19. The method of claim 11 , wherein said titanium containing powder comprises a Ti powder or a Ti alloy.
20. The method of claim 19 , wherein said Ti alloy comprises Ti-6Al-4V.
21. The method of claim 11 , wherein the tungsten containing titanium alloy has a microstructure that comprises all-alpha phase, alpha/beta phases, or all-beta phase, or all-alpha phase or alpha/beta phases comprising a dispersion of beta phase islands.
22. The method of claim 21 , wherein said beta phase islands include partially diffused beta stabilizer within the beta phase islands.
23. A product comprising the composition of claim 1 .
24. The product of claim 23 , wherein said product is an orthopedic device chosen from knee, hip, spinal, and dental implants.
25. The product of claim 23 , wherein said product is an automotive component chosen from valves, connecting rods, piston pins and spring retainers.
26. The product of claim 23 , wherein said product is an military vehicle component chosen from tank track, suspension, and undercarriage parts.
27. The product of claim 23 , wherein said product is a tool or die material for metal forming chosen from shot sleeves, plungers and dies.
28. The product of claim 23 , wherein said product is an aircraft component chosen from a turbine rotor, and a leading edge of a helicopter rotor blade, tubing, valves and fittings.
29. The product of claim 23 , wherein said product is a billet for subsequent casting, forging or extrusion.
30. A powder metallurgy method of producing a titanium containing product, said method comprising:
blending a titanium containing powder with a tungsten containing powder to form a blended powder, said blended powder comprising tungsten powder in an amount ranging from 0.5% to 40% by weight of said alloy, wherein said tungsten powder has an average diameter less then 3 μm in size;
compacting the blended powder; and
sintering the compacted and blended powder,
said method optionally comprising a post-sintering process chosen from hot isostatically pressing, casting, forging and extrusion.
31. The method of claim 30 , wherein said product is an orthopedic or dental implant.
32. The method of claim 30 , wherein said product is a billet that is subjected to at least one post-sintering process chosen from casting, forging, and extrusion.
Priority Applications (2)
Application Number | Priority Date | Filing Date | Title |
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US11/108,865 US20050268746A1 (en) | 2004-04-19 | 2005-04-19 | Titanium tungsten alloys produced by additions of tungsten nanopowder |
US13/850,488 US20140079583A1 (en) | 2004-04-19 | 2013-03-26 | Titanium tungsten alloys produced by additions of tungsten nanopowder |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
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US56300904P | 2004-04-19 | 2004-04-19 | |
US11/108,865 US20050268746A1 (en) | 2004-04-19 | 2005-04-19 | Titanium tungsten alloys produced by additions of tungsten nanopowder |
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US13/850,488 Continuation US20140079583A1 (en) | 2004-04-19 | 2013-03-26 | Titanium tungsten alloys produced by additions of tungsten nanopowder |
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US20050268746A1 true US20050268746A1 (en) | 2005-12-08 |
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US13/850,488 Abandoned US20140079583A1 (en) | 2004-04-19 | 2013-03-26 | Titanium tungsten alloys produced by additions of tungsten nanopowder |
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US13/850,488 Abandoned US20140079583A1 (en) | 2004-04-19 | 2013-03-26 | Titanium tungsten alloys produced by additions of tungsten nanopowder |
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US7846551B2 (en) | 2007-03-16 | 2010-12-07 | Tdy Industries, Inc. | Composite articles |
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US7954569B2 (en) | 2004-04-28 | 2011-06-07 | Tdy Industries, Inc. | Earth-boring bits |
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US8104550B2 (en) | 2006-08-30 | 2012-01-31 | Baker Hughes Incorporated | Methods for applying wear-resistant material to exterior surfaces of earth-boring tools and resulting structures |
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US8322465B2 (en) | 2008-08-22 | 2012-12-04 | TDY Industries, LLC | Earth-boring bit parts including hybrid cemented carbides and methods of making the same |
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US11400613B2 (en) | 2019-03-01 | 2022-08-02 | California Institute Of Technology | Self-hammering cutting tool |
US11591906B2 (en) | 2019-03-07 | 2023-02-28 | California Institute Of Technology | Cutting tool with porous regions |
CN116987920B (en) * | 2023-09-26 | 2023-12-08 | 海朴精密材料(苏州)有限责任公司 | Ti-based all-metal energetic structural material, preparation method and application thereof |
Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4894090A (en) * | 1985-09-12 | 1990-01-16 | Santrade Limited | Powder particles for fine-grained hard material alloys |
US5498302A (en) * | 1992-02-07 | 1996-03-12 | Smith & Nephew Richards, Inc. | Surface hardened biocompatible metallic medical implants |
US5545248A (en) * | 1992-06-08 | 1996-08-13 | Nippon Tungsten Co., Ltd. | Titanium-base hard sintered alloy |
US6009728A (en) * | 1993-07-28 | 2000-01-04 | Matsushita Electric Industrial Co., Ltd. | Die for press-molding optical elements |
US6279443B1 (en) * | 1997-12-26 | 2001-08-28 | Nippon Tungsten Co., Ltd. | Die cut roll |
Family Cites Families (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH03229837A (en) * | 1990-02-01 | 1991-10-11 | Sumitomo Metal Ind Ltd | Ti-base alloy for hot working tool and its manufacture |
JP2606946B2 (en) * | 1990-03-13 | 1997-05-07 | 日立金属株式会社 | Ti-W target material and method of manufacturing the same |
WO1999005332A1 (en) * | 1997-07-25 | 1999-02-04 | Dynamet Technology, Inc. | Titanium materials containing tungsten |
-
2005
- 2005-04-19 US US11/108,865 patent/US20050268746A1/en not_active Abandoned
- 2005-04-19 WO PCT/US2005/013291 patent/WO2006073428A2/en active Application Filing
-
2013
- 2013-03-26 US US13/850,488 patent/US20140079583A1/en not_active Abandoned
Patent Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4894090A (en) * | 1985-09-12 | 1990-01-16 | Santrade Limited | Powder particles for fine-grained hard material alloys |
US5498302A (en) * | 1992-02-07 | 1996-03-12 | Smith & Nephew Richards, Inc. | Surface hardened biocompatible metallic medical implants |
US5545248A (en) * | 1992-06-08 | 1996-08-13 | Nippon Tungsten Co., Ltd. | Titanium-base hard sintered alloy |
US6009728A (en) * | 1993-07-28 | 2000-01-04 | Matsushita Electric Industrial Co., Ltd. | Die for press-molding optical elements |
US6279443B1 (en) * | 1997-12-26 | 2001-08-28 | Nippon Tungsten Co., Ltd. | Die cut roll |
Non-Patent Citations (1)
Title |
---|
"elemental." Dictionary.com Unabridged. Random House, Inc. 06 Mar. 2012. . * |
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US8007714B2 (en) | 2004-04-28 | 2011-08-30 | Tdy Industries, Inc. | Earth-boring bits |
US8172914B2 (en) | 2004-04-28 | 2012-05-08 | Baker Hughes Incorporated | Infiltration of hard particles with molten liquid binders including melting point reducing constituents, and methods of casting bodies of earth-boring tools |
US7954569B2 (en) | 2004-04-28 | 2011-06-07 | Tdy Industries, Inc. | Earth-boring bits |
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US8403080B2 (en) | 2004-04-28 | 2013-03-26 | Baker Hughes Incorporated | Earth-boring tools and components thereof including material having hard phase in a metallic binder, and metallic binder compositions for use in forming such tools and components |
US8808591B2 (en) | 2005-06-27 | 2014-08-19 | Kennametal Inc. | Coextrusion fabrication method |
US8318063B2 (en) | 2005-06-27 | 2012-11-27 | TDY Industries, LLC | Injection molding fabrication method |
US8637127B2 (en) | 2005-06-27 | 2014-01-28 | Kennametal Inc. | Composite article with coolant channels and tool fabrication method |
US8647561B2 (en) | 2005-08-18 | 2014-02-11 | Kennametal Inc. | Composite cutting inserts and methods of making the same |
US7687156B2 (en) | 2005-08-18 | 2010-03-30 | Tdy Industries, Inc. | Composite cutting inserts and methods of making the same |
US7997359B2 (en) | 2005-09-09 | 2011-08-16 | Baker Hughes Incorporated | Abrasive wear-resistant hardfacing materials, drill bits and drilling tools including abrasive wear-resistant hardfacing materials |
US8002052B2 (en) | 2005-09-09 | 2011-08-23 | Baker Hughes Incorporated | Particle-matrix composite drill bits with hardfacing |
US8388723B2 (en) | 2005-09-09 | 2013-03-05 | Baker Hughes Incorporated | Abrasive wear-resistant materials, methods for applying such materials to earth-boring tools, and methods of securing a cutting element to an earth-boring tool using such materials |
US8758462B2 (en) | 2005-09-09 | 2014-06-24 | Baker Hughes Incorporated | Methods for applying abrasive wear-resistant materials to earth-boring tools and methods for securing cutting elements to earth-boring tools |
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US7703555B2 (en) | 2005-09-09 | 2010-04-27 | Baker Hughes Incorporated | Drilling tools having hardfacing with nickel-based matrix materials and hard particles |
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US7802495B2 (en) | 2005-11-10 | 2010-09-28 | Baker Hughes Incorporated | Methods of forming earth-boring rotary drill bits |
US9192989B2 (en) | 2005-11-10 | 2015-11-24 | Baker Hughes Incorporated | Methods of forming earth-boring tools including sinterbonded components |
US7784567B2 (en) | 2005-11-10 | 2010-08-31 | Baker Hughes Incorporated | Earth-boring rotary drill bits including bit bodies comprising reinforced titanium or titanium-based alloy matrix materials, and methods for forming such bits |
US7913779B2 (en) | 2005-11-10 | 2011-03-29 | Baker Hughes Incorporated | Earth-boring rotary drill bits including bit bodies having boron carbide particles in aluminum or aluminum-based alloy matrix materials, and methods for forming such bits |
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US20070102199A1 (en) * | 2005-11-10 | 2007-05-10 | Smith Redd H | Earth-boring rotary drill bits and methods of manufacturing earth-boring rotary drill bits having particle-matrix composite bit bodies |
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WO2008034042A3 (en) * | 2006-09-14 | 2008-05-22 | Iap Res Inc | Micron size powders having nano size reinforcement |
US20100124514A1 (en) * | 2006-09-14 | 2010-05-20 | The Timken Company | Method of producing uniform blends of nano and micron powders |
US8889065B2 (en) | 2006-09-14 | 2014-11-18 | Iap Research, Inc. | Micron size powders having nano size reinforcement |
WO2008034043A2 (en) * | 2006-09-14 | 2008-03-20 | Iap Research, Inc. | Method of producing uniform blends of nano and micron powders |
US20080069716A1 (en) * | 2006-09-14 | 2008-03-20 | The Timken Company | Micron size powders having nano size reinforcement |
US8841005B2 (en) | 2006-10-25 | 2014-09-23 | Kennametal Inc. | Articles having improved resistance to thermal cracking |
US8007922B2 (en) | 2006-10-25 | 2011-08-30 | Tdy Industries, Inc | Articles having improved resistance to thermal cracking |
US8697258B2 (en) | 2006-10-25 | 2014-04-15 | Kennametal Inc. | Articles having improved resistance to thermal cracking |
US7775287B2 (en) | 2006-12-12 | 2010-08-17 | Baker Hughes Incorporated | Methods of attaching a shank to a body of an earth-boring drilling tool, and tools formed by such methods |
US20080135304A1 (en) * | 2006-12-12 | 2008-06-12 | Baker Hughes Incorporated | Methods of attaching a shank to a body of an earth-boring drilling tool, and tools formed by such methods |
US7841259B2 (en) | 2006-12-27 | 2010-11-30 | Baker Hughes Incorporated | Methods of forming bit bodies |
US8176812B2 (en) | 2006-12-27 | 2012-05-15 | Baker Hughes Incorporated | Methods of forming bodies of earth-boring tools |
US7846551B2 (en) | 2007-03-16 | 2010-12-07 | Tdy Industries, Inc. | Composite articles |
US8137816B2 (en) | 2007-03-16 | 2012-03-20 | Tdy Industries, Inc. | Composite articles |
US8790439B2 (en) | 2008-06-02 | 2014-07-29 | Kennametal Inc. | Composite sintered powder metal articles |
US8221517B2 (en) | 2008-06-02 | 2012-07-17 | TDY Industries, LLC | Cemented carbide—metallic alloy composites |
US9163461B2 (en) | 2008-06-04 | 2015-10-20 | Baker Hughes Incorporated | Methods of attaching a shank to a body of an earth-boring tool including a load-bearing joint and tools formed by such methods |
US7703556B2 (en) | 2008-06-04 | 2010-04-27 | Baker Hughes Incorporated | Methods of attaching a shank to a body of an earth-boring tool including a load-bearing joint and tools formed by such methods |
US8746373B2 (en) | 2008-06-04 | 2014-06-10 | Baker Hughes Incorporated | Methods of attaching a shank to a body of an earth-boring tool including a load-bearing joint and tools formed by such methods |
US8770324B2 (en) | 2008-06-10 | 2014-07-08 | Baker Hughes Incorporated | Earth-boring tools including sinterbonded components and partially formed tools configured to be sinterbonded |
US10144113B2 (en) | 2008-06-10 | 2018-12-04 | Baker Hughes Incorporated | Methods of forming earth-boring tools including sinterbonded components |
US8261632B2 (en) | 2008-07-09 | 2012-09-11 | Baker Hughes Incorporated | Methods of forming earth-boring drill bits |
US8459380B2 (en) | 2008-08-22 | 2013-06-11 | TDY Industries, LLC | Earth-boring bits and other parts including cemented carbide |
US8322465B2 (en) | 2008-08-22 | 2012-12-04 | TDY Industries, LLC | Earth-boring bit parts including hybrid cemented carbides and methods of making the same |
US8025112B2 (en) | 2008-08-22 | 2011-09-27 | Tdy Industries, Inc. | Earth-boring bits and other parts including cemented carbide |
US8858870B2 (en) | 2008-08-22 | 2014-10-14 | Kennametal Inc. | Earth-boring bits and other parts including cemented carbide |
US8225886B2 (en) | 2008-08-22 | 2012-07-24 | TDY Industries, LLC | Earth-boring bits and other parts including cemented carbide |
US9435010B2 (en) | 2009-05-12 | 2016-09-06 | Kennametal Inc. | Composite cemented carbide rotary cutting tools and rotary cutting tool blanks |
US8272816B2 (en) | 2009-05-12 | 2012-09-25 | TDY Industries, LLC | Composite cemented carbide rotary cutting tools and rotary cutting tool blanks |
US8869920B2 (en) | 2009-06-05 | 2014-10-28 | Baker Hughes Incorporated | Downhole tools and parts and methods of formation |
US8201610B2 (en) | 2009-06-05 | 2012-06-19 | Baker Hughes Incorporated | Methods for manufacturing downhole tools and downhole tool parts |
US8464814B2 (en) | 2009-06-05 | 2013-06-18 | Baker Hughes Incorporated | Systems for manufacturing downhole tools and downhole tool parts |
US8317893B2 (en) | 2009-06-05 | 2012-11-27 | Baker Hughes Incorporated | Downhole tool parts and compositions thereof |
US9266171B2 (en) | 2009-07-14 | 2016-02-23 | Kennametal Inc. | Grinding roll including wear resistant working surface |
US8308096B2 (en) | 2009-07-14 | 2012-11-13 | TDY Industries, LLC | Reinforced roll and method of making same |
US9643236B2 (en) | 2009-11-11 | 2017-05-09 | Landis Solutions Llc | Thread rolling die and method of making same |
US10669797B2 (en) | 2009-12-08 | 2020-06-02 | Baker Hughes, A Ge Company, Llc | Tool configured to dissolve in a selected subsurface environment |
US10240419B2 (en) | 2009-12-08 | 2019-03-26 | Baker Hughes, A Ge Company, Llc | Downhole flow inhibition tool and method of unplugging a seat |
US9682425B2 (en) | 2009-12-08 | 2017-06-20 | Baker Hughes Incorporated | Coated metallic powder and method of making the same |
US10603765B2 (en) | 2010-05-20 | 2020-03-31 | Baker Hughes, a GE company, LLC. | Articles comprising metal, hard material, and an inoculant, and related methods |
US8978734B2 (en) | 2010-05-20 | 2015-03-17 | Baker Hughes Incorporated | Methods of forming at least a portion of earth-boring tools, and articles formed by such methods |
US9687963B2 (en) | 2010-05-20 | 2017-06-27 | Baker Hughes Incorporated | Articles comprising metal, hard material, and an inoculant |
US8905117B2 (en) | 2010-05-20 | 2014-12-09 | Baker Hughes Incoporated | Methods of forming at least a portion of earth-boring tools, and articles formed by such methods |
US9790745B2 (en) | 2010-05-20 | 2017-10-17 | Baker Hughes Incorporated | Earth-boring tools comprising eutectic or near-eutectic compositions |
US8490674B2 (en) | 2010-05-20 | 2013-07-23 | Baker Hughes Incorporated | Methods of forming at least a portion of earth-boring tools |
US10335858B2 (en) | 2011-04-28 | 2019-07-02 | Baker Hughes, A Ge Company, Llc | Method of making and using a functionally gradient composite tool |
US9631138B2 (en) | 2011-04-28 | 2017-04-25 | Baker Hughes Incorporated | Functionally gradient composite article |
US9926763B2 (en) | 2011-06-17 | 2018-03-27 | Baker Hughes, A Ge Company, Llc | Corrodible downhole article and method of removing the article from downhole environment |
US10697266B2 (en) | 2011-07-22 | 2020-06-30 | Baker Hughes, A Ge Company, Llc | Intermetallic metallic composite, method of manufacture thereof and articles comprising the same |
US9707739B2 (en) | 2011-07-22 | 2017-07-18 | Baker Hughes Incorporated | Intermetallic metallic composite, method of manufacture thereof and articles comprising the same |
US9833838B2 (en) | 2011-07-29 | 2017-12-05 | Baker Hughes, A Ge Company, Llc | Method of controlling the corrosion rate of alloy particles, alloy particle with controlled corrosion rate, and articles comprising the particle |
US10092953B2 (en) | 2011-07-29 | 2018-10-09 | Baker Hughes, A Ge Company, Llc | Method of controlling the corrosion rate of alloy particles, alloy particle with controlled corrosion rate, and articles comprising the particle |
US10301909B2 (en) | 2011-08-17 | 2019-05-28 | Baker Hughes, A Ge Company, Llc | Selectively degradable passage restriction |
US9925589B2 (en) | 2011-08-30 | 2018-03-27 | Baker Hughes, A Ge Company, Llc | Aluminum alloy powder metal compact |
US9856547B2 (en) | 2011-08-30 | 2018-01-02 | Bakers Hughes, A Ge Company, Llc | Nanostructured powder metal compact |
US10737321B2 (en) | 2011-08-30 | 2020-08-11 | Baker Hughes, A Ge Company, Llc | Magnesium alloy powder metal compact |
US9802250B2 (en) | 2011-08-30 | 2017-10-31 | Baker Hughes | Magnesium alloy powder metal compact |
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US8800848B2 (en) | 2011-08-31 | 2014-08-12 | Kennametal Inc. | Methods of forming wear resistant layers on metallic surfaces |
US9643144B2 (en) | 2011-09-02 | 2017-05-09 | Baker Hughes Incorporated | Method to generate and disperse nanostructures in a composite material |
US9016406B2 (en) | 2011-09-22 | 2015-04-28 | Kennametal Inc. | Cutting inserts for earth-boring bits |
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US9926766B2 (en) | 2012-01-25 | 2018-03-27 | Baker Hughes, A Ge Company, Llc | Seat for a tubular treating system |
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US9910026B2 (en) | 2015-01-21 | 2018-03-06 | Baker Hughes, A Ge Company, Llc | High temperature tracers for downhole detection of produced water |
US10378303B2 (en) | 2015-03-05 | 2019-08-13 | Baker Hughes, A Ge Company, Llc | Downhole tool and method of forming the same |
US10221637B2 (en) | 2015-08-11 | 2019-03-05 | Baker Hughes, A Ge Company, Llc | Methods of manufacturing dissolvable tools via liquid-solid state molding |
US10016810B2 (en) | 2015-12-14 | 2018-07-10 | Baker Hughes, A Ge Company, Llc | Methods of manufacturing degradable tools using a galvanic carrier and tools manufactured thereof |
US11649526B2 (en) | 2017-07-27 | 2023-05-16 | Terves, Llc | Degradable metal matrix composite |
US11898223B2 (en) | 2017-07-27 | 2024-02-13 | Terves, Llc | Degradable metal matrix composite |
US20210198771A1 (en) * | 2018-05-28 | 2021-07-01 | Life Vascular Devices Biotech, S.L. | A beta-phase titanium and tungsten alloy |
CN113088733A (en) * | 2021-03-31 | 2021-07-09 | 中南大学 | Ti-W heterogeneous metal-metal composite material and preparation method thereof |
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WO2006073428A3 (en) | 2006-10-05 |
US20140079583A1 (en) | 2014-03-20 |
WO2006073428A2 (en) | 2006-07-13 |
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