WO2005090623A1 - 冷間加工性に優れる耐熱チタン合金板およびその製造方法 - Google Patents
冷間加工性に優れる耐熱チタン合金板およびその製造方法 Download PDFInfo
- Publication number
- WO2005090623A1 WO2005090623A1 PCT/JP2005/005292 JP2005005292W WO2005090623A1 WO 2005090623 A1 WO2005090623 A1 WO 2005090623A1 JP 2005005292 W JP2005005292 W JP 2005005292W WO 2005090623 A1 WO2005090623 A1 WO 2005090623A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- annealing
- present
- titanium alloy
- cold
- temperature
- Prior art date
Links
Classifications
-
- 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
-
- 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
-
- 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
- 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
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
- F01N—GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
- F01N2530/00—Selection of materials for tubes, chambers or housings
Definitions
- the present invention relates to a heat-resistant titanium alloy sheet excellent in cold workability and its production
- exhaust system components such as motorcycles and automobiles
- Parts such as the manifold, exhaust pipe, silencer (muffler), etc.
- Pure titanium which has excellent design properties such as color and texture, is used in some automobile exhaust systems.
- the muffler is the last part of the exhaust system, where the exhaust gas
- pure titanium which does not have high strength at high temperatures, can be used for muffler applications.
- pure stainless steel parts such pure titanium parts are mainly formed by bending, press forming, drawing, expanding holes, or bending plates, and then welding them. It is used as a welded pipe or after being formed into a desired shape by various cold working.
- such a pure titanium sheet is generally manufactured by the following steps. That is, ingots are formed by melting processes such as VAR (vacuum arc melting) and EBR (electron beam melting), which are converted into slabs by hot forging or slab rolling, and then into slabs. Hot-rolled strip, and then, after descaling, cold-rolled to form a cold-rolled strip. Alternatively, by cutting this, a cut plate product is manufactured.
- VAR vacuum arc melting
- EBR electron beam melting
- annealing is performed as necessary, and the final cold strip is also subjected to annealing. It is common to use
- a heat-resistant titanium alloy that has excellent high-temperature strength properties compared to JIS Class 2 pure titanium, and has cold workability and high temperature oxidation resistance equivalent to or better than JIS Class 2 pure titanium, and excellent cold workability It is an object of the present invention to provide a board and a method for producing the board.
- the present invention is based on the following means.
- the titanium alloy plate further comprises Sn, Zr, Mo, Nb,
- the heat-resistant titanium having excellent cold workability according to the above (1), characterized by containing at least one or two or more types of Cr in a total of 0.3% by mass to 1.5% by mass. Alloy plate.
- the component adjustment in the melting may be adjusted according to the above (1) or ( 2)
- the component adjustment in the melting may be adjusted according to the above (1) or ( 2)
- the hot-rolled sheet annealing or the intermediate annealing is performed in a temperature range of 650 to 8300C, and further, the final annealing is performed.
- a method for producing a heat-resistant titanium alloy sheet having excellent cold workability which is carried out at a temperature of 600 to 600.
- the inventors of the present invention have studied in detail the effects of component elements on high-temperature strength, oxidation resistance, and cold workability of titanium in order to solve the above-mentioned problems.As a result, when a certain amount of Cu is added to titanium, However, high-temperature strength can be significantly improved in the temperature range of about 500 to about 700 ° C, where automotive exhaust system members are used, without impairing cold workability and oxidation resistance. I found something. The present invention has been made based on this technological knowledge.
- the mass is 0 /. 0.3-: L. 8% Cu, 0.18% or less oxygen, 0.30% or less Fe, balance Ti and less than 0.3% impurity elements. I decided to.
- the upper limit of the added amount of Cu is set to 1.8%. If the added amount of Cu exceeds this, a large amount of Ti 2 Cu phase is generated and the cold workability is impaired. That's why. Further, the lower limit of the added amount of Cu is set to 0.3% because it is necessary to add 0.3% or more of 11 in order to sufficiently improve the high-temperature strength.
- Fe the content of Fe needs to be 0.30% or less.
- F e is an i3 phase stabilizing element, and develops a] 3 phase from room temperature to a high temperature range. If the Fe content is less than 0.30%, the amount of / 3 phase generated is negligible. However, if it is added beyond this, the amount of] 3 phase increases and Cu, which is an element that tends to be concentrated, concentrates intensively there, and the amount of solid solution in the ⁇ phase necessary for improving high-temperature strength decreases. Therefore, excessive ⁇ In order to suppress the appearance of the W phase, Fe must be set to 0.30% or less.
- the sum of these impurities, such as nitrogen, carbon, Ni, Cr, Al, Sn, Si, hydrogen, and other elements contained in ordinary titanium materials, and other elements are also If it is less than 0.3% that does not impair workability, it may be contained.
- the high-temperature oxidation resistance which is an important characteristic that the heat-resistant material should have like the high-temperature strength, is not impaired at all even when Cu is added.
- the oxygen content is preferably 0.10% or less from the viewpoint of workability. This is because, with an oxygen content in this range, twinning is further promoted and workability is further improved. Since oxygen has little effect on high-temperature strength, limiting oxygen to 0.10% or less does not impair high-temperature characteristics at all.
- Such effects can be further exerted by limiting the oxygen content to 0.06% or less. That is, in the alloy of the present invention (1), if the oxygen content is 0.06% or less, the effect of the present invention is most exerted.
- the present invention (2) at least one or more of Sn, Zr, Mo, Nb, and Cr are added to the alloy of the present invention (1) in a total amount of 0.1%. It is determined that the content is 3% by mass or more and 1.5% by mass or less.
- All of Sn, Zr, Mo, Nb, and Cr form a solid solution to the ⁇ phase to some extent, and increase the high-temperature strength by overlapping with Cu.
- the high-temperature oxidation resistance is improved.
- the added amount must be at least 0.3% in total. If it is not added more than this, improvement of high temperature strength and high temperature This is because improvement in oxidation resistance cannot be obtained.
- the total amount of addition must be 1.5% or less. This is because these elements have the effect of accelerating the precipitation of Ti 2 Cu, and when added in large amounts, the amount of Ti 2 Cu produced increases and the workability is impaired. However, if the total is less than 1.5%, the effect is small.
- the present invention described in claim 3 or 4 (hereinafter, the present inventions (3) and (4)) relates to a method of manufacturing a thin plate used frequently in an exhaust system of an automobile. That is, the present invention (3) provides a method for producing a thin plate having a titanium alloy component according to the present invention (1) or (2), which is produced through steps of melting, hot rolling and cold rolling. A method for producing a titanium alloy sheet according to the present invention (1) or (2), characterized in that the method is carried out in a temperature range of 65 to 83 ° C.
- the annealing before the final cold rolling is performed in the temperature range of 65 ° C to 80 ° C
- the final annealing after the cold rolling is 65 ° C. Even when the temperature is lower than 0 ° C, it is possible to maintain a large amount of Cu dissolved in the ⁇ phase.
- This manufacturing method is applied to the present invention described in claim 4. However, if the temperature is lower than 600 ° C, distortion is difficult to remove and hard to soften, so sufficient cold workability cannot be obtained, so it should be avoided.
- Titanium having the composition shown in Table 1 was melted by VAR (vacuum arc melting), turned into a slab by hot forging, heated to 860 ° C, and then sheeted by a hot continuous rolling mill. A 3.5 mm thick hot rolled strip was used.
- This hot-rolled strip was subjected to continuous air-cooled annealing (hot-rolled sheet annealing) at 720 ° C for 2 minutes, and the oxide scale was removed by shot blasting and pickling. Thus, a 1 mm thick cold-rolled strip was used. After that, vacuum annealing (final annealing) of furnace cooling was performed at 680 ° C for 4 hours, and a tensile test specimen was sampled in parallel with the rolling direction. A tensile test was performed at 0 ° C. Strength properties were evaluated by 0.2% resistance to heat, and additivity was evaluated by elongation at room temperature. Further, using a 30 mm ⁇ 30 mm rectangular test piece, a heat treatment at 700 ° C. for 200 hours was performed in the air, and the oxidation increase was measured. These evaluation results are also shown in Table 1. ⁇ table 1 ⁇
- Test No. 1 is an example of JIS Class 2 industrial pure titanium, and Test Nos. 2 and 3 are examples of alloys to which A 1 is added by about 1 to 2%. Test No. 1 has an elongation of 39.5% at room temperature and has sufficient cold workability.On the other hand, 0.2% heat resistance at high temperature is 60 MP at 550 ° C. a, 21MPa at 625 ° C and 8MPa at 700 ° C, with insufficient high-temperature strength.
- Test Nos. 2 and 3 to which A1 was added exhibited 0.2% resistance at 550 ° C, 625 ° C, and 700 ° C. High temperature strength has been achieved, but room temperature elongation is 30% or less, and cold workability is insufficient.
- Test Nos. 5, 6, 7, 9, 10, 10, 12, 13, and 15, which are examples of the present invention (1) produced by the method described in the present invention (3).
- 16, 17 and 18 all have a high room temperature elongation of 35% or more and a 0.2% resistance to heat at 550 ° C, 625 ° C and 700 ° C.
- Forces are high values of 10 OMPa or more, 80 MPa or more, and 30 MPa or more at each temperature, and both excellent cold workability and high high-temperature strength are achieved. The effects of the invention are fully exhibited. In particular, in Test Nos.
- Test No. 4 Although a high room temperature elongation of 40.6% was obtained, the 0.2% heat resistance at 550 ° C, 625 ° C, and 700 ° C was respectively It is 100 MPa, 80 MPa, and 30 MPa or less, and the high temperature strength has not been sufficiently improved.
- Test No. 11 also showed a high room temperature elongation of 37.2%, but the 0.2% proof stresses at 65 ° C and 700 ° C were 80 MPa and 30 MPa, respectively. It was below MPa, and the improvement in high-temperature strength was insufficient.
- Test No. 4 the added amount of Cu did not reach the lower limit of 0.3% of the present invention, 0.3%, and the amount of dissolved Cu required for improving the high-temperature strength was insufficient.
- Test No. 11 the content of the three-phase stabilizing element Fe was added in excess of the upper limit of the present invention of 0.30%. This is because Cu concentrates intensively there, and the amount of solid solution in the ⁇ phase necessary for improving the high-temperature strength has decreased.
- Test Nos. 8 and 14 the high-temperature strength was sufficiently high, but the room temperature elongation was 35% or less in both cases, which was considerably lower than JIS Class 2 pure titanium. This is because in Test No. 8, Cu was added in excess of 1.8% of the upper limit of the present invention, so that a large amount of Ti 2 Cu phase was formed and the ductility during cold was impaired. In Test No. 14, the oxygen content was added in excess of 0.18%, which is the upper limit of the present invention, so that twinning deformation was suppressed and the deformability during cold was reduced.
- the titanium alloy plate made of the element specified in the present invention has excellent cold workability and high-temperature strength, and also has high temperature oxidation resistance equivalent to that of pure titanium. Deviates from the alloy element amount specified in the present invention. Once removed, the balance between cold workability and high temperature strength cannot be achieved.
- Titanium having the composition shown in Table 2 was melted by VAR (vacuum arc melting), turned into a slab by hot forging, heated to 860 ° C, and then stripped by a hot continuous rolling mill. A 3.5 mm thick hot rolled strip was used.
- This hot-rolled strip was subjected to continuous air-cooled annealing (hot-rolled sheet annealing) at 720 ° C for 2 minutes, and the oxide scale was removed by shot blasting and pickling. A 1 mm thick cold-rolled strip was used. Thereafter, furnace-cooled vacuum annealing (final annealing) was performed at 680 ° C for 4 hours, and a tensile test specimen was taken in parallel with the rolling direction, and a tensile test was performed at room temperature and at 700 ° C.
- the strength characteristics were evaluated by 0.2% resistance to resistance, and the workability was evaluated by the elongation value at room temperature. Further, a rectangular test piece of 30 mm ⁇ 30 mm was subjected to a heat treatment at 700 ° C. for 200 hours in the air, and the amount of increase in oxidation was measured. These evaluation results are also shown in Table 2.
- test numbers 19, 21, 23, 25, 27, 29, 30 of the examples of the present invention (2) produced by the method described in the present invention (3) are shown.
- 31, 32, 33, 34, and 35 all have a high room temperature elongation of over 35%, and the same amount of Cu, Fe, and oxygen 0.2% resistance at 700 ° C is more than 7MPa higher than that of Test No. 6 and the effect of adding Sn, Zr, Mo, Nb, and Cr alone or in combination Has been demonstrated.
- test numbers 20, 22, 24, 26, 28, 36, and 37 have a 0.2% resistance at 700 ° C higher than that of the test number 6.
- the amount of increase in oxidation during heat treatment at 700 ° C for 200 hours in air was also smaller than that in Test No. 6, and the high-temperature strength and high-temperature oxidation resistance were improved, but the room temperature elongation was 35%. Below, the workability has been impaired.
- Test Nos. 38 to 42 are Examples of the present invention (2) in which Sn, Zr, Mo, Nb, and Cr were added to the alloy of Test No. 12, and Because of the amount of addition, a high room temperature elongation of 35% or more, a 0.2% resistance to heat at 700 ° C for test numbers 12 and over, and an atmospheric heat treatment at 700 ° C for 200 hours High temperature oxidation resistance is achieved.
- Test Nos. 43 to 52 are examples in which Sn, Zr, Mo, Nb, and Cr were added to the alloy of Test No. 16, and the appropriate test described in the present invention (2) was performed.
- Test numbers 38 to 47 to which the additive amount was added showed a high room temperature elongation of 35% or more and a high high-temperature strength that exceeded test number 16 by 5 MPa or more (0.2% resistance at 700 ° C).
- F high high-temperature oxidation resistance (high-temperature oxidation resistance during atmospheric heat treatment at 700 ° C for 200 hours).
- the addition amounts of Sn, Zr, Mo, Nb, and Cr were less than 0.3% specified in the present invention (2), and test numbers 48, 49, 50, For 51 and 52, the improvement in high-temperature strength was at most 3 MPa, and the improvement in high-temperature oxidation resistance was only slight.
- Hot-rolled sheet annealing condition cold-rolled sheet annealing conditions 0.2% ⁇ Ka elongation 0.2% ⁇ Ka oxidized amount Remarks number (Pa) (%) (MPa ) (mg / cm 2)
- Table 3 shows the test results for materials with the same composition as Test No. 6. Regardless of the conditions of hot-rolled sheet annealing, cold-rolled sheet annealing, which was the final annealing, was performed in the temperature range of 65 to 83 ° C. Test numbers 55, 56, 57, 60, 6 1, 62, 65, 66, and 67 all have high room temperature elongation of 40% or more and 34? A 0.2% proof stress at a high value of > 700 is obtained, and the oxidation resistance is comparable to that of pure titanium.
- the final cold-rolling annealing temperature was 63 ° C., which was out of the condition range specified in the present invention (3). Elongation, a high resistance of 0.2 MPa at 700 ° C. or higher of 34 MPa or more, and oxidation resistance comparable to that of pure titanium were obtained. This is because the effect of the present invention (4) was exhibited because the hot-rolled sheet annealing, which is the annealing before the cold rolling, was performed in a temperature range of 65 to 8300C.
- Test numbers 53, 58, 59, 63, 64, and 68 were tested at room temperature elongation of 40% or more, and at 700 ° C of 30 MPa or more. Although the proof stress of 0.2% was obtained, the high-temperature strength was slightly lower than that of Examples of the above test numbers. The reasons are as follows.
- the hot-rolled sheet annealing which is the annealing before cold rolling, was performed in the temperature range of 65 to 80 ° C. specified in the present invention (4). Since the annealing of a cold-rolled sheet was less than 600 ° C. as specified in the present invention (4), the margin for improvement in high-temperature strength was slightly reduced. In Test No. 58, since the cold-rolled sheet annealing as the final annealing was outside the temperature range specified in the present invention (3) or (4), the improvement in the high-temperature strength was limited. It has become a little smaller.
- Test Nos. 59, 63, 64, and 68 were performed under the temperature range of 65-83 ° C specified in the present invention (4) when hot-rolled sheet annealing, which is annealing before cold rolling, was performed. In addition, since the cold-rolled sheet annealing, which is the final annealing, was out of the temperature range specified in the present invention (3), the improvement in the high-temperature strength was slightly reduced.
- Table 4 shows the test results for materials with the same composition as Test No. 29.
- Each of the cold-rolled annealed sheets (test numbers 69 to 72) produced by the method of (3) or (4) of the present invention has a high room temperature elongation of 35% or more, and a high room temperature elongation of 441 ⁇ & Level 0.2% resistance to 700 ° C, and excellent high-temperature oxidation resistance.
- test number 73 in which the cold-rolled sheet annealing, which is the final annealing, was out of the temperature range specified in the present invention (3) or (4), the 0.2% proof stress at 700 ° C was not sufficient. The results were slightly lower than those in Examples of Test Nos. 69 to 72.
- Table 5 shows the test results for materials having the same composition as Test No. 34.
- the hot-rolled sheet annealing which is the annealing before the cold rolling, is outside the temperature range of 65 ° to 83 ° C. specified in the present invention (4), and the final rolling is the cold-rolled sheet.
- test numbers 74 and 78 in which the sheet annealing was out of the temperature range specified in the present invention (3), the 0.2% proof stress at 700 ° C was slightly higher than that of test numbers 75 to 77. It was lower than the example.
- Table 6 shows the test results for materials with the same composition as test number 44.
- Test No. 80 produced by the method according to the present invention (3)
- Test No. 81 produced by the method described in the invention (4) also has a high room temperature elongation equivalent to that of Test No. 44, a high 0.2% resistance at 700 ° C., and excellent high temperature oxidation resistance Is obtained.
- the titanium alloy sheet of the present invention is used in a combustion exhaust gas discharge path, such as an exhaust manifold, an exhaust pipe, a muffler (muffler), which is an exhaust system component of two-wheeled and four-wheeled vehicles. It can be used especially for such purposes.
- a combustion exhaust gas discharge path such as an exhaust manifold, an exhaust pipe, a muffler (muffler), which is an exhaust system component of two-wheeled and four-wheeled vehicles. It can be used especially for such purposes.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
Claims
Priority Applications (6)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
SI200531998T SI1726670T1 (sl) | 2004-03-19 | 2005-03-16 | Uporaba pločevine iz toplotno odporne titanove zlitine z izvrstnimi lastnostmi obdelave v hladnem v izpušnem sistemu vozila |
US10/592,892 US20070187008A1 (en) | 2004-03-19 | 2005-03-16 | Heat resistant titanium alloy sheet excellent in cold workability and a method of production of the same |
EP05721342.3A EP1726670B1 (en) | 2004-03-19 | 2005-03-16 | Use of a heat resistant titanium alloy sheet excellent in cold workability in an exhaust system of a vehicle |
US12/931,573 US20110132500A1 (en) | 2004-03-19 | 2011-02-04 | Heat resistant titanium alloy sheet excellent in cold workability and a method of production of the same |
US13/327,306 US20120148437A1 (en) | 2004-03-19 | 2011-12-15 | Heat Resistant Titanium Alloy Sheet Excellent in Cold Workability and A Method of Production of the Same |
US14/455,013 US9797029B2 (en) | 2004-03-19 | 2014-08-08 | Heat resistant titanium alloy sheet excellent in cold workability and a method of production of the same |
Applications Claiming Priority (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2004080280 | 2004-03-19 | ||
JP2004-080280 | 2004-03-19 | ||
JP2005067175A JP4486530B2 (ja) | 2004-03-19 | 2005-03-10 | 冷間加工性に優れる耐熱チタン合金板およびその製造方法 |
JP2005-067175 | 2005-03-10 |
Related Child Applications (4)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US10/592,892 A-371-Of-International US20070187008A1 (en) | 2004-03-19 | 2005-03-16 | Heat resistant titanium alloy sheet excellent in cold workability and a method of production of the same |
US12/931,573 Continuation US20110132500A1 (en) | 2004-03-19 | 2011-02-04 | Heat resistant titanium alloy sheet excellent in cold workability and a method of production of the same |
US13/327,306 Continuation US20120148437A1 (en) | 2004-03-19 | 2011-12-15 | Heat Resistant Titanium Alloy Sheet Excellent in Cold Workability and A Method of Production of the Same |
US14/455,013 Continuation-In-Part US9797029B2 (en) | 2004-03-19 | 2014-08-08 | Heat resistant titanium alloy sheet excellent in cold workability and a method of production of the same |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2005090623A1 true WO2005090623A1 (ja) | 2005-09-29 |
Family
ID=34993724
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2005/005292 WO2005090623A1 (ja) | 2004-03-19 | 2005-03-16 | 冷間加工性に優れる耐熱チタン合金板およびその製造方法 |
Country Status (5)
Country | Link |
---|---|
US (4) | US20070187008A1 (ja) |
EP (2) | EP1726670B1 (ja) |
JP (1) | JP4486530B2 (ja) |
SI (2) | SI1726670T1 (ja) |
WO (1) | WO2005090623A1 (ja) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN114774725A (zh) * | 2022-04-26 | 2022-07-22 | 西北有色金属研究院 | 一种3C电子产品用Gr4带材的制备方法 |
Families Citing this family (26)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP4486530B2 (ja) * | 2004-03-19 | 2010-06-23 | 新日本製鐵株式会社 | 冷間加工性に優れる耐熱チタン合金板およびその製造方法 |
JP4987609B2 (ja) * | 2007-07-30 | 2012-07-25 | 新日本製鐵株式会社 | 冷間加工性に優れる排気装置部材用耐熱チタン合金およびその製造方法ならびに該合金を用いた排気装置部材 |
JP4987640B2 (ja) * | 2007-09-10 | 2012-07-25 | 新日本製鐵株式会社 | 冷間加工部品の製造に適した機械部品用または装飾部品用チタン合金棒線およびその製造方法 |
JP5176445B2 (ja) * | 2007-09-10 | 2013-04-03 | 新日鐵住金株式会社 | 耐酸化性および成形性に優れた排気系部品用チタン合金材および、その製造方法ならびに、その合金材を用いた排気装置 |
WO2010054236A1 (en) * | 2008-11-06 | 2010-05-14 | Titanium Metals Corporation | Methods for the manufacture of a titanium alloy for use in combustion engine exhaust systems |
JP4666271B2 (ja) * | 2009-02-13 | 2011-04-06 | 住友金属工業株式会社 | チタン板 |
JP5365266B2 (ja) * | 2009-03-05 | 2013-12-11 | 新日鐵住金株式会社 | プレス成形性に優れたチタン合金薄板およびその製造方法 |
US10358698B2 (en) | 2009-12-28 | 2019-07-23 | Nippon Steel Corporation | Heat resistant titanium alloy material for exhaust system part use excellent in oxidation resistance, method of production of heat resistant titanium alloy material for exhaust system part use excellent in oxidation resistance, and exhaust system |
KR101454458B1 (ko) * | 2009-12-28 | 2014-10-27 | 신닛테츠스미킨 카부시키카이샤 | 내산화성이 우수한 배기계 부품용 내열 티타늄 합금재, 내산화성이 우수한 배기계 부품용 내열 티타늄 합금판의 제조 방법 및 배기 장치 |
JP2012052178A (ja) * | 2010-08-31 | 2012-03-15 | Kobe Steel Ltd | 室温での強度及び延性に優れたチタン合金 |
WO2012115243A1 (ja) | 2011-02-24 | 2012-08-30 | 新日本製鐵株式会社 | 冷間でのコイル取扱性に優れた高強度α+β型チタン合金熱延板及びその製造方法 |
JP2013001973A (ja) * | 2011-06-17 | 2013-01-07 | Nippon Steel & Sumitomo Metal Corp | 耐水素吸収性ならびに造管性に優れるチタン合金溶接管および溶接管用フープ製品とそれらの製造方法 |
US9587770B2 (en) | 2011-12-20 | 2017-03-07 | Nippon Steel & Sumitomo Metal Corporation | α + β type titanium alloy sheet for welded pipe, manufacturing method thereof, and α + β type titanium alloy welded pipe product |
EP3112483A4 (en) | 2014-04-10 | 2017-10-25 | Nippon Steel & Sumitomo Metal Corporation | Welded pipe of + titanium alloy with excellent strength and rigidity in pipe-length direction, and process for producing same |
CN104028574B (zh) * | 2014-06-13 | 2016-07-06 | 无锡华生精密材料股份有限公司 | 一种生产汽车排气管软管用钛合金钢带的方法 |
EP3266887A4 (en) * | 2015-03-02 | 2018-07-18 | Nippon Steel & Sumitomo Metal Corporation | Thin titanium sheet and manufacturing method therefor |
CN104745872B (zh) * | 2015-04-22 | 2016-08-17 | 哈尔滨工业大学 | 一种适用于650℃温度下使用的高温钛合金 |
US10920300B2 (en) | 2015-07-29 | 2021-02-16 | Nippon Steel Corporation | Titanium composite material and titanium material for hot rolling |
TWI627285B (zh) * | 2015-07-29 | 2018-06-21 | Nippon Steel & Sumitomo Metal Corp | Titanium composite and titanium for hot rolling |
KR102334071B1 (ko) | 2017-08-31 | 2021-12-03 | 닛폰세이테츠 가부시키가이샤 | 티타늄판 |
CN111655880B (zh) | 2018-02-07 | 2021-11-02 | 日本制铁株式会社 | 钛合金材料 |
CN109082560A (zh) * | 2018-08-29 | 2018-12-25 | 江苏沃钛有色金属有限公司 | 一种抗拉伸的钛合金板及其制备方法 |
JP7397278B2 (ja) * | 2019-08-09 | 2023-12-13 | 日本製鉄株式会社 | チタン合金板及び自動車用排気系部品 |
CN111020342B (zh) * | 2019-12-27 | 2021-09-14 | 昆明理工大学 | 一种形变强化制备抗菌钛合金的方法 |
JP7541255B2 (ja) | 2021-01-20 | 2024-08-28 | 日本製鉄株式会社 | チタン合金板及び自動車用排気系部品 |
CN115537599B (zh) * | 2022-10-13 | 2023-06-06 | 东莞理工学院 | 一种高弹性模量及近零线膨胀系数的钛铌合金及其制备方法 |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS63270449A (ja) * | 1987-04-28 | 1988-11-08 | Nippon Steel Corp | 異方性の小さい良延性チタン板の製造方法 |
JPH05279773A (ja) * | 1991-03-25 | 1993-10-26 | Nippon Steel Corp | 均一微細組織の高強度チタン合金 |
JP2003326389A (ja) * | 2001-07-12 | 2003-11-18 | Daido Steel Co Ltd | 溶融金属形成用Ti系線材 |
JP2004002953A (ja) | 2002-04-10 | 2004-01-08 | Nippon Steel Corp | 電解Cu箔製造ドラム用チタン板およびその製造方法 |
Family Cites Families (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS4915122B1 (ja) * | 1969-09-12 | 1974-04-12 | ||
JPH0646269B2 (ja) * | 1985-10-14 | 1994-06-15 | 住友金属工業株式会社 | Ti合金製めがねフレ−ム |
US4744878A (en) * | 1986-11-18 | 1988-05-17 | Kerr-Mcgee Chemical Corporation | Anode material for electrolytic manganese dioxide cell |
US5188677A (en) * | 1989-06-16 | 1993-02-23 | Nkk Corporation | Method of manufacturing a magnetic disk substrate |
DE4000270C2 (de) * | 1990-01-08 | 1999-02-04 | Stahlwerk Ergste Gmbh & Co Kg | Verfahren zum Kaltverformen von unlegiertem Titan |
JP2616491B2 (ja) * | 1995-06-09 | 1997-06-04 | 住友金属工業株式会社 | チタン合金 |
EP0812924A1 (de) * | 1996-06-11 | 1997-12-17 | Institut Straumann Ag | Titanwerkstoff, Verfahren zu seiner Herstellung und Verwendung |
JPH1180867A (ja) | 1997-09-08 | 1999-03-26 | Sumitomo Metal Ind Ltd | 抗菌性および耐生物付着性に優れるTi合金およびその製造方法 |
JP2000096165A (ja) * | 1998-09-25 | 2000-04-04 | Sumitomo Metal Ind Ltd | 抗菌性および耐生物付着性に優れたTi合金およびその製造方法 |
JP3967515B2 (ja) | 2000-02-16 | 2007-08-29 | 株式会社神戸製鋼所 | マフラー用チタン合金材およびマフラー |
JP4064143B2 (ja) * | 2002-04-11 | 2008-03-19 | 新日本製鐵株式会社 | チタン製自動車部品 |
JP4486530B2 (ja) * | 2004-03-19 | 2010-06-23 | 新日本製鐵株式会社 | 冷間加工性に優れる耐熱チタン合金板およびその製造方法 |
-
2005
- 2005-03-10 JP JP2005067175A patent/JP4486530B2/ja active Active
- 2005-03-16 US US10/592,892 patent/US20070187008A1/en not_active Abandoned
- 2005-03-16 EP EP05721342.3A patent/EP1726670B1/en active Active
- 2005-03-16 WO PCT/JP2005/005292 patent/WO2005090623A1/ja not_active Application Discontinuation
- 2005-03-16 SI SI200531998T patent/SI1726670T1/sl unknown
- 2005-03-16 SI SI200531996T patent/SI2333130T1/sl unknown
- 2005-03-16 EP EP11155253.5A patent/EP2333130B1/en active Active
-
2011
- 2011-02-04 US US12/931,573 patent/US20110132500A1/en not_active Abandoned
- 2011-12-15 US US13/327,306 patent/US20120148437A1/en not_active Abandoned
-
2014
- 2014-08-08 US US14/455,013 patent/US9797029B2/en active Active
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS63270449A (ja) * | 1987-04-28 | 1988-11-08 | Nippon Steel Corp | 異方性の小さい良延性チタン板の製造方法 |
JPH05279773A (ja) * | 1991-03-25 | 1993-10-26 | Nippon Steel Corp | 均一微細組織の高強度チタン合金 |
JP2003326389A (ja) * | 2001-07-12 | 2003-11-18 | Daido Steel Co Ltd | 溶融金属形成用Ti系線材 |
JP2004002953A (ja) | 2002-04-10 | 2004-01-08 | Nippon Steel Corp | 電解Cu箔製造ドラム用チタン板およびその製造方法 |
Non-Patent Citations (2)
Title |
---|
See also references of EP1726670A4 * |
THE JAPAN INSTITUTE OF METALS: "Kinzoku Binran", 5 October 1996, REVISED EDITION, 5TH PRINT, MARUZEN CO., LTD, pages: 639, XP008110654 * |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN114774725A (zh) * | 2022-04-26 | 2022-07-22 | 西北有色金属研究院 | 一种3C电子产品用Gr4带材的制备方法 |
Also Published As
Publication number | Publication date |
---|---|
US20110132500A1 (en) | 2011-06-09 |
JP2005298970A (ja) | 2005-10-27 |
US20070187008A1 (en) | 2007-08-16 |
EP2333130A1 (en) | 2011-06-15 |
US20140348697A1 (en) | 2014-11-27 |
SI2333130T1 (sl) | 2016-01-29 |
EP1726670A1 (en) | 2006-11-29 |
US20120148437A1 (en) | 2012-06-14 |
EP1726670A4 (en) | 2010-12-01 |
SI1726670T1 (sl) | 2016-04-29 |
EP2333130B1 (en) | 2015-08-26 |
US9797029B2 (en) | 2017-10-24 |
EP1726670B1 (en) | 2015-09-02 |
JP4486530B2 (ja) | 2010-06-23 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
WO2005090623A1 (ja) | 冷間加工性に優れる耐熱チタン合金板およびその製造方法 | |
JP5700175B2 (ja) | フェライト系ステンレス鋼 | |
JP5609571B2 (ja) | 耐酸化性に優れたフェライト系ステンレス鋼 | |
JP6075349B2 (ja) | フェライト系ステンレス鋼 | |
US7806993B2 (en) | Heat-resistant ferritic stainless steel and method for production thereof | |
WO2011024568A1 (ja) | 耐熱性に優れるフェライト系ステンレス鋼 | |
JP4987609B2 (ja) | 冷間加工性に優れる排気装置部材用耐熱チタン合金およびその製造方法ならびに該合金を用いた排気装置部材 | |
WO2011081077A1 (ja) | 耐酸化性に優れた排気系部品用耐熱チタン合金材、耐酸化性に優れた排気系部品用耐熱チタン合金板の製造方法、及び排気装置 | |
CN108026623B (zh) | 铁素体系不锈钢 | |
JP5125600B2 (ja) | 高温強度、耐水蒸気酸化性および加工性に優れるフェライト系ステンレス鋼 | |
CN104364404B (zh) | 铁素体系不锈钢 | |
JP2008115419A (ja) | 加工性に優れた排気系部品用α型チタン合金材およびその製造方法ならびに該合金を用いた排気装置部材 | |
WO2020080104A1 (ja) | フェライト系ステンレス鋼 | |
JP5862314B2 (ja) | 耐酸化性に優れた排気系部品用チタン合金材および、その製造方法ならびに、その合金材を用いた排気装置 | |
JP6624345B1 (ja) | フェライト系ステンレス鋼 | |
JP2896077B2 (ja) | 耐高温酸化性およびスケール密着性に優れたフエライト系ステンレス鋼 | |
JP2942073B2 (ja) | 高温強度に優れたエキゾースト・マニホールド用フェライト系ステンレス鋼 | |
WO2019151125A1 (ja) | フェライト系ステンレス鋼 | |
WO2018116792A1 (ja) | フェライト系ステンレス鋼 | |
JP2023037686A (ja) | フェライト系ステンレス鋼 | |
JP2024030778A (ja) | フェライト系ステンレス冷延焼鈍鋼板、その素材となる冷延鋼板および前記冷延焼鈍鋼板の製造方法 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
AK | Designated states |
Kind code of ref document: A1 Designated state(s): AE AG AL AM AT AU AZ BA BB BG BR BW BY BZ CA CH CN CO CR CU CZ DE DK DM DZ EC EE EG ES FI GB GD GE GH GM HR HU ID IL IN IS KE KG KP KR KZ LC LK LR LS LT LU LV MA MD MG MK MN MW MX MZ NA NI NO NZ OM PG PH PL PT RO RU SC SD SE SG SK SL SM SY TJ TM TN TR TT TZ UA UG US UZ VC VN YU ZA ZM ZW |
|
AL | Designated countries for regional patents |
Kind code of ref document: A1 Designated state(s): BW GH GM KE LS MW MZ NA SD SL SZ TZ UG ZM ZW AM AZ BY KG KZ MD RU TJ TM AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IS IT LT LU MC NL PL PT RO SE SI SK TR BF BJ CF CG CI CM GA GN GQ GW ML MR NE SN TD TG |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application | ||
WWE | Wipo information: entry into national phase |
Ref document number: 10592892 Country of ref document: US Ref document number: 2007187008 Country of ref document: US |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2005721342 Country of ref document: EP |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
WWW | Wipo information: withdrawn in national office |
Ref document number: DE |
|
WWP | Wipo information: published in national office |
Ref document number: 2005721342 Country of ref document: EP |
|
WWP | Wipo information: published in national office |
Ref document number: 10592892 Country of ref document: US |