WO2006022951A2 - Method for manufacturing titanium alloy wire with enhanced properties - Google Patents
Method for manufacturing titanium alloy wire with enhanced properties Download PDFInfo
- Publication number
- WO2006022951A2 WO2006022951A2 PCT/US2005/018492 US2005018492W WO2006022951A2 WO 2006022951 A2 WO2006022951 A2 WO 2006022951A2 US 2005018492 W US2005018492 W US 2005018492W WO 2006022951 A2 WO2006022951 A2 WO 2006022951A2
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- titanium alloy
- wire
- approximately
- reduction
- hot
- Prior art date
Links
Classifications
-
- 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
- B22F3/17—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by forging
-
- 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
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
- C22C1/1042—Alloys containing non-metals starting from a melt by atomising
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
-
- 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
-
- 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
- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
- B22F5/12—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product of wires
-
- 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
-
- 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
- the present invention relates to a method of manufacturing titanium alloy wire and, more particularly, to such a method wherein precipitated discontinuous particulates of a reinforcement material such as TiB and/or TiC are added to the alloy and it is processed in accordance with a new and improved method wherein the reinforcement thereof by the particulates is enhanced.
- a reinforcement material such as TiB and/or TiC
- the new and improved method of the present invention is not subject to these disadvantages and possesses advantages not possible with the use of previously used or known methods.
- the method of the present invention is directed to the manufacturing of titanium alloy wire suitable for application to wire/fiber composites, generally comprising the steps of forming the desired alloy via casting a billet or gas atomization; hot forging to create a uniform chemistry and microstructure; conforming to rod or coil, e.g., of about 0:2 inches in diameter; and cold drawing to wire, e.g., of about .005 inches in diameter.
- a preferred method comprises the formation of titanium alloy powder by gas atomization from a boron rich melt; consolidating the powder metal to bar form using hot isostatic pressing (HIP) with a pressure of about 5,000 to 45,000 psi, e.g., 15,000 psi, and a temperature of about 1,65O 0 F to 1,75O 0 F until full consolidation, yet remaining below the beta transis to avoid grain growth and grain boundary segregation; hot reduction at approximately 1500 0 F to 2100 0 F, e.g., 1,750 0 F, to reduce the bar to rod or coil form and perform the initial break-up of the larger TiB grains; and cold drawing and annealing at approximately a 10 to 20 percent reduction per pass to avoid cracking.
- HIP hot isostatic pressing
- an increased frequency of annealing steps under very low oxygen conditions serves to relieve work hardening and also recrystallizes the TiB grains to a refined size with alignment with the wire axis.
- This new and improved method enables the fabrication of fine titanium alloy wire with simultaneous achievement of high TiB reinforcement content and small reinforcement grain size.
- Other reinforcement materials may be used such as TiC, alone or in combination with TiB.
- U.S. Patent No. 5,763,079 consists of four principal operations, namely, formation of the desired alloy via casting a billet, hot forging to create a uniform chemistry and microstructure, hot forming to rod (or coil) of about 0.2 inches in diameter, and cold drawing to wire of about .005 inches in diameter. Intermediate annealing operations are necessary during the cold drawing to relieve residual stresses and restore ductility for further drawing.
- This basic wire forming process is designed to achieve area reduction through hot forming, hot extrusion and finally cold drawing in the fewest operations and the fewest breaks that would affect continuous lengths.
- the wire drawing process can be designed or modified to control microstructural evolution in addition to the base purpose of area reduction.
- the wire drawing method of the present invention can achieve improved microstructures in difficult alloys that cannot be achieved by any other known method, and was developed for the purpose of producing a discontinuously reinforced T1-6A1- 4V alloy with the simultaneous achievement of high TiB content and small reinforcement grain size.
- the present wire forming method can start with a casting of Ti-6A1-4V alloy from a Boron rich melt.
- the TiB will precipitate during cooling, but the cooling rate will allow for larger TiB grain growth which is undesirable.
- a powder metal formed by gas atomization from a Boron rich melt preferably is used rather than a casting.
- the powder forming process employs more rapid cooling than casting and is less likely to produce large TiB grains.
- a compositionally uniform billet is prepared using powder metallurgy techniques to avoid the grain growth and potential for chemical segregation inherent in the casting process.
- the metal alloy powder produced from Boron rich Ti-6A1-4V alloy is first hot formed into a bar compatible in size with the available industrial wire forming equipment. The bar is hot rolled into rod or coil with a diameter of about 0.2 inches, and the rod or coil is then transferred to the cold drawing operations.
- the cold drawing process of the present invention serves to break up the large TiB grains without deleterious microcracking or void formation. It has been discovered that the addition of frequent annealing steps to relieve work hardening will also recrystallize the TiB grains to a refined size with alignment with the wire axis. Annealing steps have been utilized in the known wire drawing process, but less frequently and for shorter periods of time. The increased frequency of anneals in accordance with the present invention increases the requirement for annealing under very low oxygen conditions to avoid excessive surface material loss due to oxygen contamination and oxygen interstitial pick up by the wire metallurgy that may interfere with the TiB refinement process. Accordingly, the present method enables the fabrication of fine titanium alloy wire with simultaneous achievement of high reinforcement content and small reinforcement grain size.
- an acceptable alloy powder is gas atomized spherical powder with a composition of Ti-6A1-4V- 1.7B in a size range of minus 35 mesh to plus 270 mesh.
- An acceptable interstitial content was found to be oxygen less than 1500 ppm.
- This quality powder has been used to fabricate composite panels and is known to yield uniform chemistry and microstructure. Consolidation of the powder metal to bar form is based on methods found successful for composite panels. For example, it has been determined that non-contaminating consolidation tooling is needed, such as vacuum degassed mild steel or conventional titanium alloys.
- Consolidation to a bar is achieved using hot isostatic pressing (HDP) with a pressure of approximately 5000 psi to 45,000 psi, e.g., 15,000 psi, and a temperature of about 1650 0 F to 175O 0 F.
- HDP hot isostatic pressing
- the hot reduction operation at about 1500 0 F to 2100 0 F, e.g., 175O 0 F, serves to reduce the bar to coil or rod form and performs the initial breakup to the larger TiB grains. It has been determined that about 50:1 hot reduction in section area is effective to breakup of the primary large TiB grains.
- the subsequent cold drawing must impart sufficient cold work through the thickness of the rod or coil, and the Docket No.: 4314.2 5 annealing must relieve the work hardening without grain growth. It has been determined that about a 10 percent reduction per pass is necessary to assure sufficient uniformity of cold working and avoid microcracking and void formation during the initial cold drawing steps from the nominal 0.2 inch diameter condition. Reductions in area can increase to about 15 percent per pass by the mid-point in the sectional area reduction process, and about 20 percent area reductions are possible by the end of the area reduction process.
- Annealing at about 1200 0 F to 2000 0 F, e.g., 1750 0 F for about 1 hour in inert gas with forced inert gas cooling is sufficient to remove work hardening, recrystallize the TiB and avoid grain growth.
- Annealing is performed at intervals corresponding to an accumulated reduction in section area of about 50 percent.
- the above-described method of the present invention produces ⁇ -6A1-4V alloy with fine grained TiB reinforcement in concentrations ranging from 1 to 50 percent by volume with reinforcement alignment along the wire axis. It has been found that this process is effective with a wide variety of titanium alloys, such as Ti-6Al-2Sn-4Zr-2Mo alloy, Ti-6Al-4Sn-4Zr- lNb-lMo-0.2Si alloy, T ⁇ -3A1-2.5V alloy, Ti-10V-2Fe-3Al alloy, 1 ⁇ -5A1-2.5 Sn alloy and Ti- 8Al-IMo-IV alloy. Also, it is effective with other precipitated discontinuous reinforcements such as TiC, or mixtures of TiB and TiC.
- titanium alloys such as Ti-6Al-2Sn-4Zr-2Mo alloy, Ti-6Al-4Sn-4Zr- lNb-lMo-0.2Si alloy, T ⁇ -3A1-2.5V alloy, Ti-10V-2Fe-3Al alloy, 1 ⁇ -5A1-2
- the method may utilize a billet cast from a Boron rich melt, but the inherent risks of microcracking and void formation would be greater owing to the larger TiB grain growth that results from a slow cooled casting.
- the extremely high area reductions inherent in the wire forming process combined with properly controlled reduction and annealing conditions in the present method produces high performance titanium alloy wire that cannot be produced by any other known metallurgical process.
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Chemical & Material Sciences (AREA)
- Manufacturing & Machinery (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
- Metal Extraction Processes (AREA)
- Forging (AREA)
Abstract
Description
Claims
Priority Applications (5)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2007522498A JP5037340B2 (en) | 2004-07-22 | 2005-05-25 | Method for producing titanium alloy wire with enhanced properties |
ES05755493T ES2385086T3 (en) | 2004-07-22 | 2005-05-25 | Procedure for manufacturing titanium alloy wire with improved properties |
EP05755493A EP1784269B1 (en) | 2004-07-22 | 2005-05-25 | Method for manufacturing titanium alloy wire with enhanced properties |
CN2005800243125A CN101068945B (en) | 2004-07-22 | 2005-05-25 | Method for manufacturing titanium alloy wire with enhanced properties |
KR1020077001471A KR101184464B1 (en) | 2004-07-22 | 2005-05-25 | Method for manufacturing titanium alloy wire with enhanced properties |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US10/895,885 US20060016521A1 (en) | 2004-07-22 | 2004-07-22 | Method for manufacturing titanium alloy wire with enhanced properties |
US10/895,885 | 2004-07-22 |
Publications (2)
Publication Number | Publication Date |
---|---|
WO2006022951A2 true WO2006022951A2 (en) | 2006-03-02 |
WO2006022951A3 WO2006022951A3 (en) | 2007-08-02 |
Family
ID=35655874
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/US2005/018492 WO2006022951A2 (en) | 2004-07-22 | 2005-05-25 | Method for manufacturing titanium alloy wire with enhanced properties |
Country Status (7)
Country | Link |
---|---|
US (1) | US20060016521A1 (en) |
EP (1) | EP1784269B1 (en) |
JP (1) | JP5037340B2 (en) |
KR (1) | KR101184464B1 (en) |
CN (1) | CN101068945B (en) |
ES (1) | ES2385086T3 (en) |
WO (1) | WO2006022951A2 (en) |
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-
2004
- 2004-07-22 US US10/895,885 patent/US20060016521A1/en not_active Abandoned
-
2005
- 2005-05-25 ES ES05755493T patent/ES2385086T3/en active Active
- 2005-05-25 WO PCT/US2005/018492 patent/WO2006022951A2/en active Application Filing
- 2005-05-25 EP EP05755493A patent/EP1784269B1/en not_active Not-in-force
- 2005-05-25 CN CN2005800243125A patent/CN101068945B/en not_active Expired - Fee Related
- 2005-05-25 KR KR1020077001471A patent/KR101184464B1/en not_active IP Right Cessation
- 2005-05-25 JP JP2007522498A patent/JP5037340B2/en not_active Expired - Fee Related
Non-Patent Citations (1)
Title |
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See references of EP1784269A4 * |
Also Published As
Publication number | Publication date |
---|---|
CN101068945A (en) | 2007-11-07 |
EP1784269A2 (en) | 2007-05-16 |
KR101184464B1 (en) | 2012-09-21 |
EP1784269A4 (en) | 2008-03-05 |
WO2006022951A3 (en) | 2007-08-02 |
CN101068945B (en) | 2010-07-14 |
JP2008507624A (en) | 2008-03-13 |
JP5037340B2 (en) | 2012-09-26 |
EP1784269B1 (en) | 2011-12-14 |
ES2385086T3 (en) | 2012-07-18 |
KR20070035042A (en) | 2007-03-29 |
US20060016521A1 (en) | 2006-01-26 |
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