US20120118433A1 - Method of modifying thermal and electrical properties of multi-component titanium alloys - Google Patents
Method of modifying thermal and electrical properties of multi-component titanium alloys Download PDFInfo
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- US20120118433A1 US20120118433A1 US12/923,056 US92305610A US2012118433A1 US 20120118433 A1 US20120118433 A1 US 20120118433A1 US 92305610 A US92305610 A US 92305610A US 2012118433 A1 US2012118433 A1 US 2012118433A1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
- B22D21/06—Casting non-ferrous metals with a high melting point, e.g. metallic carbides
-
- 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
- B22F3/10—Sintering only
- B22F3/1039—Sintering only by reaction
-
- 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
-
- 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
-
- 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
- C22C32/001—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 only oxides
- C22C32/0015—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 only oxides with only single oxides as main non-metallic constituents
- C22C32/0031—Matrix based on refractory metals, W, Mo, Nb, Hf, Ta, Zr, Ti, V or alloys thereof
-
- 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
- C22C32/0073—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 only borides
Definitions
- the present invention relates to a method of improving physical properties of titanium alloys and, more specifically, a method of increasing thermal conductivity and reducing electrical resistivity of articles made of titanium-based compositions.
- Titanium alloys offer attractive physical and mechanical property combinations that provide significant weight savings in various industries such as aerospace and space. Thermal conductivity of titanium alloys, however, is low compared to other structural metals such as steel and aluminum. Low thermal conductivity of titanium alloys affects heating rates and obtainable cooling rates after processing and heat treatments. Another drawback of titanium alloys is their high electrical resistivity compared to steel and aluminum. High electrical resistivity limits the use of titanium alloys as electrical conductors. There is a need, therefore, for a new and improved method of increasing thermal conductivity and reducing electrical resistivity of conventional titanium alloys such as Ti-6Al-4V without debits in mechanical properties, specifically tensile elongation and fatigue. The method of the present invention meets this need.
- titanium boride (TiB) precipitates are incorporated into a titanium alloy and the alloy is then subjected to controlled deformation to orient the TiB precipitates in the direction of interest to achieve improvements in thermal and electrical properties.
- the controlled deformation of the alloy to orient the TiB precipitates is accomplished by hot metalworking.
- the boron is introduced into the titanium alloy composition to produce TiB precipitates by any suitable method, such as casting, cast-and-wrought processing, powder metallurgy techniques such as gas atomization and blended elemental approach. Hot metalworking operations such as forging, rolling and extrusion can be used to accomplish alignment of the TiB precipitates along the direction of metal flow.
- the method of the present invention may be used to increase thermal conductivity and reduce electrical resistivity of multi-component titanium alloys such as Ti-6Al-4V (Ti-64) and Ti-6Al-2Sn-4Zr-2Mo(Ti-6242).
- multi-component titanium alloys such as Ti-6Al-4V (Ti-64) and Ti-6Al-2Sn-4Zr-2Mo(Ti-6242).
- FIG. 1 is a pre-alloyed powder metallurgy process flowchart for fabrication of TiB incorporated titanium alloy articles
- FIG. 2 a is a microstructure of Ti-6Al-4V-1B showing a cross-section of as-atomized pre-alloyed powder particle
- FIG. 2 b is a microstructure of Ti-6Al-4V-1B after powder consolidation via hot isostatic pressing;
- FIG. 3 shows microstructures of Ti-6Al-4V-1B forging article at different locations
- FIG. 4 a is a microstructure of an extrusion article made out of pre-alloyed powder of Ti-6Al-4V-1B revealing TiB precipitates (dark phase) aligned along the extrusion axis.
- FIG. 4 b is a transverse micrograph of FIG. 4 a showing hexagonal cross-sections of TiB precipitates
- FIG. 5 is a graph comparing the thermal conductivity of Ti-6Al-4V-1B (labeled as nano Ti-64) forging and extrusion articles with that of a Ti-6Al-4V article;
- FIG. 6 is a graph comparing the thermal conductivity of Ti-6Al-2Sn-4Zr-2Mo-1B forging article with that of the baseline Ti-6Al-2Sn-4Zr-2Mo article;
- FIG. 7 is a graph comparing the electrical resistivity of Ti-6Al-4V-1B (labeled as nano Ti-64) forging article with that of a Ti-6Al-4V article;
- FIG. 8 is a graph comparing the electrical resistivity of Ti-6Al-2Sn-4Zr-2Mo-1B forging article with that of the baseline Ti-6Al-2Sn-4Zr-2Mo article.
- Ti-6Al-4V Ti-64
- Ti-6Al-2Sn-4Zr-2Mo Ti-6242
- boron into the titanium alloy composition to produce TiB precipitates can be accomplished by several different methods, such as casting, cast-and-wrought processing, powder metallurgy techniques such as gas atomization and blended elemental approach.
- the boron may be added to the titanium alloy in the liquid state, wherein the boron is completely dissolved in the liquid titanium alloy.
- the boron may be added to the titanium alloy through intermixing of solid powders, as by powder metallurgy. Regardless of the process used to add the boron to the titanium alloy, the boron may be added as elemental boron, TiB2 or as any appropriate master alloy containing boron.
- the boron may be added in amounts in the range from 0.01% to 18.4%, by weight. More preferably, the boron is added to the titanium alloy in amounts ranging from 0.01% to 2%, by weight, depending on titanium alloy composition.
- Hot metalworking operations such as forging, rolling, and extrusion can be used to accomplish alignment of TiB precipitates along the direction of metal flow.
- the present method can be practiced by the gas atomization powder metallurgy process flowchart shown in FIG. 1 .
- the boron is added to the molten titanium alloy and the liquid melt is inert gas atomized to obtain titanium alloy powder.
- Each powder particle contains needle-shaped TiB precipitates distributed uniformly and in random orientations.
- An example microstructure of Ti-6Al-4V-1B powder particle cross-section which contains 6 vol. % of TiB (dark phase) is shown in FIG. 2 a .
- Titanium alloy powder is consolidated using a conventional technique such as hot isostatic pressing (HIP) to obtain a fully dense powder compact. In as-compacted condition, the TiB precipitates are still in random orientations distributed uniformly in the titanium alloy matrix.
- An example microstructure of Ti-6Al-4V-1B powder after HIP is shown in FIG. 2 b.
- Hot working parameters commonly practiced for producing titanium alloy articles were found to produce the desired alignment of TiB precipitates along the direction of metal flow.
- the hot working parameters are as follows:
- FIG. 3 Micrographs at different locations of a Ti-6Al-4V-1B article made via forging of a powder compact of 16′′ height ⁇ 3.5′′ diameter into a disk of 3′′ height ⁇ 8′′ diameter in the temperature range 1750-2200° F. and a ram speed of 40 inch/min are shown in FIG. 3 . Alignment of TiB needle-shaped precipitates (dark phase) along the radial orientation after forging is evident in FIG. 3 .
- FIG. 4 Another example microstructure of a Ti-6Al-4V-1B article that was produced by extrusion processing of a 3′′ diameter powder compact into a bar of 0.75′′ diameter at 2000° F. and a ram speed of 100 inch/min is shown in FIG. 4 , which reveals alignment of TiB precipitates (dark phase) along the extrusion axis.
- Thermal conductivity of Ti-64-1B (labeled as nano Ti-64) forging and extrusion articles is compared with that of Ti-64 article in FIG. 5 .
- Higher thermal conductivity of nano Ti-64 forging in the radial orientation and nano Ti-64 extrusion in the axial orientation is evident compared to the baseline Ti-64 in the temperature range 70-1250° F.
- Thermal conductivity data of Ti-6242-1B forging article is compared with that of the baseline Ti-6242 article in FIG. 6 . Increased thermal conductivity compared to the baseline is evident in this material system also. Increase in thermal conductivity by up to 35% was recorded in articles with the TiB precipitates aligned along the test direction.
- Ti-64-1B (labeled as nano Ti-64) forging article is compared with that of Ti-64 article in FIG. 7 .
- Reduced electrical resistivity of nano Ti-64 forging in the radial orientation compared to the baseline Ti-64 in the temperature range 70-1500° F. is evident.
- Electrical resistivity data of Ti-6242-1B forging article is compared with that of the baseline Ti-6242 article in FIG. 8 .
- Reduced electrical resistivity compared to the baseline is evident in this material system also. Reduction in thermal conductivity by up to 20% was recorded in articles with the TiB precipitates aligned along the test direction.
- TiB incorporated titanium alloys offer several benefits in mechanical properties without debits in ductility and fatigue.
- room temperature tensile properties of boron-modified titanium alloy articles (referred to as nano version) are compared with those of baseline titanium alloys in Table 2.
- the tensile yield strength and ultimate strength were higher by 25%, modulus of elasticity is higher by 20%, while maintaining tensile elongations equivalent to their baseline titanium alloys.
Abstract
Description
- 1. Field of the Invention
- The present invention relates to a method of improving physical properties of titanium alloys and, more specifically, a method of increasing thermal conductivity and reducing electrical resistivity of articles made of titanium-based compositions.
- 2. Description of the Background Art
- Titanium alloys offer attractive physical and mechanical property combinations that provide significant weight savings in various industries such as aerospace and space. Thermal conductivity of titanium alloys, however, is low compared to other structural metals such as steel and aluminum. Low thermal conductivity of titanium alloys affects heating rates and obtainable cooling rates after processing and heat treatments. Another drawback of titanium alloys is their high electrical resistivity compared to steel and aluminum. High electrical resistivity limits the use of titanium alloys as electrical conductors. There is a need, therefore, for a new and improved method of increasing thermal conductivity and reducing electrical resistivity of conventional titanium alloys such as Ti-6Al-4V without debits in mechanical properties, specifically tensile elongation and fatigue. The method of the present invention meets this need.
- In accordance with the new and improved method of the present invention, titanium boride (TiB) precipitates are incorporated into a titanium alloy and the alloy is then subjected to controlled deformation to orient the TiB precipitates in the direction of interest to achieve improvements in thermal and electrical properties. The controlled deformation of the alloy to orient the TiB precipitates is accomplished by hot metalworking.
- The boron is introduced into the titanium alloy composition to produce TiB precipitates by any suitable method, such as casting, cast-and-wrought processing, powder metallurgy techniques such as gas atomization and blended elemental approach. Hot metalworking operations such as forging, rolling and extrusion can be used to accomplish alignment of the TiB precipitates along the direction of metal flow.
- As an illustrative example, the method of the present invention may be used to increase thermal conductivity and reduce electrical resistivity of multi-component titanium alloys such as Ti-6Al-4V (Ti-64) and Ti-6Al-2Sn-4Zr-2Mo(Ti-6242).
-
FIG. 1 is a pre-alloyed powder metallurgy process flowchart for fabrication of TiB incorporated titanium alloy articles; -
FIG. 2 a is a microstructure of Ti-6Al-4V-1B showing a cross-section of as-atomized pre-alloyed powder particle; -
FIG. 2 b is a microstructure of Ti-6Al-4V-1B after powder consolidation via hot isostatic pressing; -
FIG. 3 shows microstructures of Ti-6Al-4V-1B forging article at different locations; -
FIG. 4 a is a microstructure of an extrusion article made out of pre-alloyed powder of Ti-6Al-4V-1B revealing TiB precipitates (dark phase) aligned along the extrusion axis. -
FIG. 4 b is a transverse micrograph ofFIG. 4 a showing hexagonal cross-sections of TiB precipitates; -
FIG. 5 is a graph comparing the thermal conductivity of Ti-6Al-4V-1B (labeled as nano Ti-64) forging and extrusion articles with that of a Ti-6Al-4V article; -
FIG. 6 is a graph comparing the thermal conductivity of Ti-6Al-2Sn-4Zr-2Mo-1B forging article with that of the baseline Ti-6Al-2Sn-4Zr-2Mo article; -
FIG. 7 is a graph comparing the electrical resistivity of Ti-6Al-4V-1B (labeled as nano Ti-64) forging article with that of a Ti-6Al-4V article; and -
FIG. 8 is a graph comparing the electrical resistivity of Ti-6Al-2Sn-4Zr-2Mo-1B forging article with that of the baseline Ti-6Al-2Sn-4Zr-2Mo article. - Methods of increasing thermal conductivity and reducing electrical resistivity of multi-component titanium alloys such as Ti-6Al-4V (Ti-64) and Ti-6Al-2Sn-4Zr-2Mo (Ti-6242) are described hereinafter. These methods encompass two important elements:
-
- 1) Incorporation of TiB precipitates into the titanium alloy matrix; and
- 2) Alignment of TiB precipitates in the direction of interest via hot metalworking.
- Introduction of boron into the titanium alloy composition to produce TiB precipitates can be accomplished by several different methods, such as casting, cast-and-wrought processing, powder metallurgy techniques such as gas atomization and blended elemental approach. The boron may be added to the titanium alloy in the liquid state, wherein the boron is completely dissolved in the liquid titanium alloy. The boron may be added to the titanium alloy through intermixing of solid powders, as by powder metallurgy. Regardless of the process used to add the boron to the titanium alloy, the boron may be added as elemental boron, TiB2 or as any appropriate master alloy containing boron. The boron may be added in amounts in the range from 0.01% to 18.4%, by weight. More preferably, the boron is added to the titanium alloy in amounts ranging from 0.01% to 2%, by weight, depending on titanium alloy composition.
- Hot metalworking operations such as forging, rolling, and extrusion can be used to accomplish alignment of TiB precipitates along the direction of metal flow.
- The present method can be practiced by the gas atomization powder metallurgy process flowchart shown in
FIG. 1 . The boron is added to the molten titanium alloy and the liquid melt is inert gas atomized to obtain titanium alloy powder. Each powder particle contains needle-shaped TiB precipitates distributed uniformly and in random orientations. An example microstructure of Ti-6Al-4V-1B powder particle cross-section which contains 6 vol. % of TiB (dark phase) is shown inFIG. 2 a. Titanium alloy powder is consolidated using a conventional technique such as hot isostatic pressing (HIP) to obtain a fully dense powder compact. In as-compacted condition, the TiB precipitates are still in random orientations distributed uniformly in the titanium alloy matrix. An example microstructure of Ti-6Al-4V-1B powder after HIP is shown inFIG. 2 b. - The powder compact is then subjected to a metalworking operation such as forging, rolling, or extrusion. Hot working parameters commonly practiced for producing titanium alloy articles were found to produce the desired alignment of TiB precipitates along the direction of metal flow. As an illustrative example, the hot working parameters are as follows:
- Micrographs at different locations of a Ti-6Al-4V-1B article made via forging of a powder compact of 16″ height×3.5″ diameter into a disk of 3″ height×8″ diameter in the temperature range 1750-2200° F. and a ram speed of 40 inch/min are shown in
FIG. 3 . Alignment of TiB needle-shaped precipitates (dark phase) along the radial orientation after forging is evident inFIG. 3 . Another example microstructure of a Ti-6Al-4V-1B article that was produced by extrusion processing of a 3″ diameter powder compact into a bar of 0.75″ diameter at 2000° F. and a ram speed of 100 inch/min is shown inFIG. 4 , which reveals alignment of TiB precipitates (dark phase) along the extrusion axis. - Thermal and electrical properties of several TiB incorporated titanium alloy articles (chemical compositions given in Table 1) were evaluated. Identical testing was performed on titanium alloys without TiB precipitates for comparison. Thermal conductivity testing was performed in accordance with the standard test method ASTM E1461 and electrical resistivity was determined per the standard method ASTM B84.
-
TABLE 1 Chemical compositions (in weight percent) of titanium alloy articles tested. Composition in Weight Percent S. No. Alloy Form Al B C Fe H N O Mo Ni Si Sn V Zr Ti 1 Ti-64 Bar 6.05 <0.005 0.004 0.153 0.0033 0.0031 0.115 4.18 balance 2 Nano Ti-64 Forging 6.04 0.91 0.051 0.05 0.011 0.009 0.139 3.8 balance 3 Nano Ti-64 Extrusion 6.1 1.06 0.046 0.051 0.0042 0.016 0.122 4.2 balance 4 Ti-6242 Bar 6.1 <0.005 0.019 0.048 0.0051 0.027 0.132 2.08 0.037 0.066 1.76 4.16 balance 5 Nano Ti-6242 Forging 6.11 1.03 0.109 0.046 0.0049 0.0068 0.108 2.11 0.045 0.1 1.88 4.43 balance - Thermal conductivity of Ti-64-1B (labeled as nano Ti-64) forging and extrusion articles is compared with that of Ti-64 article in
FIG. 5 . Higher thermal conductivity of nano Ti-64 forging in the radial orientation and nano Ti-64 extrusion in the axial orientation is evident compared to the baseline Ti-64 in the temperature range 70-1250° F. - Thermal conductivity data of Ti-6242-1B forging article is compared with that of the baseline Ti-6242 article in
FIG. 6 . Increased thermal conductivity compared to the baseline is evident in this material system also. Increase in thermal conductivity by up to 35% was recorded in articles with the TiB precipitates aligned along the test direction. - Electrical resistivity of Ti-64-1B (labeled as nano Ti-64) forging article is compared with that of Ti-64 article in
FIG. 7 . Reduced electrical resistivity of nano Ti-64 forging in the radial orientation compared to the baseline Ti-64 in the temperature range 70-1500° F. is evident. Electrical resistivity data of Ti-6242-1B forging article is compared with that of the baseline Ti-6242 article inFIG. 8 . Reduced electrical resistivity compared to the baseline is evident in this material system also. Reduction in thermal conductivity by up to 20% was recorded in articles with the TiB precipitates aligned along the test direction. - In addition to the improvements in thermal and electrical properties, TiB incorporated titanium alloys offer several benefits in mechanical properties without debits in ductility and fatigue. For example, room temperature tensile properties of boron-modified titanium alloy articles (referred to as nano version) are compared with those of baseline titanium alloys in Table 2. In nano titanium alloys, the tensile yield strength and ultimate strength were higher by 25%, modulus of elasticity is higher by 20%, while maintaining tensile elongations equivalent to their baseline titanium alloys.
-
TABLE 2 Typical room temperature tensile properties of boron-modified titanium alloy articles referred to as nano alloys. S. No. Alloy Article Orientation TYS, ksi UTS, ksi TE, % TM, Msi 1 Ti-64 Bar Axial 120 130 13 16.9 2 Nano Ti-64 Forging Radial 140 154 13 18.6 3 Nano Ti-64 Extrusion Axial 152 163 10 19.9 4 Ti-6242 Bar Axial 131 141 13 16.5 5 Nano Ti-6242 Forging Radial 161 170 9 19.1 TYS: Tensile Yield Strength, UTS: Ultimate Tensile Strength, TE: Tensile Elongation, and TM: Tensile Modulus (modulus of elasticity in tension). - While the invention has been described in connection with what is presently considered to be the most practical and preferred embodiments, it is to be understood that the invention is not to be limited to the disclosed embodiments, but on the contrary, is intended to cover various modifications and equivalent arrangements included within the spirit and scope of the appended claims.
Claims (10)
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US12/923,056 US20120118433A1 (en) | 2010-11-12 | 2010-11-12 | Method of modifying thermal and electrical properties of multi-component titanium alloys |
EP11172128A EP2453029A1 (en) | 2010-11-12 | 2011-06-30 | Method of modifying thermal and electrical properties of multi-component titanium alloys |
CN2011102296938A CN102465217A (en) | 2010-11-12 | 2011-08-11 | Method of modifying thermal and electrical properties of multi-component titanium alloys |
KR1020110084208A KR20120051572A (en) | 2010-11-12 | 2011-08-23 | Method of modifying thermal and electrical properties of multi-component titanium alloys |
JP2011189256A JP2012102394A (en) | 2010-11-12 | 2011-08-31 | Method of modifying thermal and electrical properties of multi-component titanium alloy |
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CN109722564A (en) * | 2019-01-10 | 2019-05-07 | 青海聚能钛金属材料技术研究有限公司 | Ti-6242 titanium alloy and preparation method thereof |
CN109722565A (en) * | 2019-01-10 | 2019-05-07 | 青海聚能钛金属材料技术研究有限公司 | High temperature resistant titanium alloy and its preparation method and application |
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WO2005060631A2 (en) * | 2003-12-11 | 2005-07-07 | Ohio University | Titanium alloy microstructural refinement method and high temperature, high strain rate superplastic forming of titanium alloys |
US20060016521A1 (en) * | 2004-07-22 | 2006-01-26 | Hanusiak William M | Method for manufacturing titanium alloy wire with enhanced properties |
US20070286761A1 (en) * | 2006-06-07 | 2007-12-13 | Miracle Daniel B | Method of producing high strength, high stiffness and high ductility titanium alloys |
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EP0484931B1 (en) * | 1990-11-09 | 1998-01-14 | Kabushiki Kaisha Toyota Chuo Kenkyusho | Sintered powdered titanium alloy and method for producing the same |
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- 2011-06-30 EP EP11172128A patent/EP2453029A1/en not_active Withdrawn
- 2011-08-11 CN CN2011102296938A patent/CN102465217A/en active Pending
- 2011-08-23 KR KR1020110084208A patent/KR20120051572A/en not_active Application Discontinuation
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WO2005060631A2 (en) * | 2003-12-11 | 2005-07-07 | Ohio University | Titanium alloy microstructural refinement method and high temperature, high strain rate superplastic forming of titanium alloys |
US20060016521A1 (en) * | 2004-07-22 | 2006-01-26 | Hanusiak William M | Method for manufacturing titanium alloy wire with enhanced properties |
US20070286761A1 (en) * | 2006-06-07 | 2007-12-13 | Miracle Daniel B | Method of producing high strength, high stiffness and high ductility titanium alloys |
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KR20120051572A (en) | 2012-05-22 |
CN102465217A (en) | 2012-05-23 |
EP2453029A1 (en) | 2012-05-16 |
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