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WO2009151031A1 - ALLIAGE DE TITANE DE TYPE α－β - Google Patents

ALLIAGE DE TITANE DE TYPE α－β Download PDF

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Publication number
WO2009151031A1
WO2009151031A1 PCT/JP2009/060475 JP2009060475W WO2009151031A1 WO 2009151031 A1 WO2009151031 A1 WO 2009151031A1 JP 2009060475 W JP2009060475 W JP 2009060475W WO 2009151031 A1 WO2009151031 A1 WO 2009151031A1
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WIPO (PCT)
Prior art keywords
mass
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titanium alloy
type titanium
tic
Prior art date
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Ceased
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PCT/JP2009/060475
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English (en)
Japanese (ja)
Inventor
昌吾 村上
浩一 赤澤
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Kobe Steel Ltd
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Kobe Steel Ltd
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Publication date
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Publication of WO2009151031A1 publication Critical patent/WO2009151031A1/fr
Anticipated expiration legal-status Critical
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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
    • 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

Definitions

  • the present invention relates to a high-strength ⁇ - ⁇ type titanium alloy having excellent intermittent cutting performance by end milling or milling.
  • High strength ⁇ - ⁇ type titanium alloys typified by Ti-6Al-4V are light weight, high strength, high corrosion resistance, and can easily change the strength level by heat treatment. Has been used extensively. In order to make further use of these characteristics, in recent years, automobile parts such as automobile and motorcycle engine members, sports equipment such as golf equipment, civil engineering and building materials, various tools, eyeglass frames and other consumer goods fields, The application of ⁇ - ⁇ type titanium alloys has been expanded to energy development applications.
  • the titanium alloy for connecting rods described in Patent Document 1 contains rare earth elements (REM) and Ca, S, Se, Te, Pb, Bi as appropriate, and forms granular compounds to suppress deterioration in toughness and ductility. In addition, the machinability (cutability) is improved.
  • REM rare earth elements
  • Ca, S, Se, Te, Pb, Bi as appropriate
  • the free-cutting titanium alloy described in Patent Document 2 improves machinability (cutability) by containing rare earth elements (REM) and improves hot workability by containing B. .
  • the free-cutting titanium alloy described in Patent Document 3 has ductility of the matrix by adding P and S, P and Ni, or P and S and Ni as free-cutting components, and REM in addition to these elements.
  • the reduction and the refinement of inclusions are performed to improve the free-cutting property and suppress the reduction of hot workability and fatigue strength.
  • ⁇ - ⁇ type titanium alloy described in Patent Document 4 C is positively added, and the strength in the practical temperature range from room temperature to 500 ° C. does not decrease. Furthermore, this ⁇ - ⁇ type titanium alloy improves the hot workability as compared with the Ti-6Al-4V alloy, which is a general-purpose alloy, by reducing the strength in the higher forging temperature range, and in the titanium alloy substrate. The fatigue rate is improved by suppressing the area ratio of TiC to be 3% or less.
  • the ⁇ - ⁇ type titanium alloy described in Patent Document 5 positively adds C and controls the ratio [Cr] / [Fe] between the Cr content and the Fe content to control the Fe content relative to the Cr content.
  • the solid solubility limit of C is increased, the amount of TiC precipitation is suppressed, and machinability (cutability) and hot workability are improved.
  • the ⁇ - ⁇ type titanium alloy described in Patent Document 6 ensures hot workability including forgeability by positive addition of C. Furthermore, this ⁇ - ⁇ type titanium alloy has both excellent machinability (cutability) and hot workability by reducing and refining the amount of TiC precipitates and limiting the upper limit of Cr concentration.
  • the present invention has been made in order to solve the above-described conventional problems, and the object thereof is high strength ⁇ - ⁇ type titanium which is excellent in hot workability and excellent in intermittent cutting by end milling or milling. It is to provide an alloy.
  • the present invention contains C: 0.06 to 0.13 mass%, Al: 3.0 to 8.5 mass%, V: 5.0 mass% or less, Cr: 3.0 mass% or less, Fe: Less than 2.5% by mass, Mo: 6.0% by mass or less, Ni: 5.0% by mass or less, Nb: 5.0% by mass or less, Ta: 5.0% by mass or less Total
  • An ⁇ - ⁇ -type titanium alloy having a value of 0.5% or less and an average equivalent circle diameter of the TiC precipitates of 1 ⁇ m or less.
  • the ⁇ - ⁇ type titanium alloy of the present invention preferably contains Si: 1.0% by mass or less.
  • the ⁇ - ⁇ type titanium alloy of the present invention preferably contains one or more of Zr: 5.0 mass% or less and Sn: 5.0 mass% or less in total of 7.0 mass% or less.
  • the ⁇ - ⁇ type titanium alloy of the present invention has high strength and excellent hot workability, as well as excellent continuous machinability, as well as intermittent cutability by end milling or milling.
  • the present inventors have investigated the cause of the decrease in tool life when cutting ⁇ - ⁇ type titanium alloys to which C is added. As a result, it was found that even when the amount of TiC precipitates generated is small, the tool life is reduced when coarse TiC precipitates are present. In particular, it has been found that the effect of tool life reduction due to TiC precipitates is more pronounced during intermittent cutting by end milling or milling than by continuous cutting by a drill.
  • the present inventors improved hot workability such as forgeability by positive addition of C, and then reduced the amount of TiC precipitate and refined, We succeeded in obtaining a high-strength ⁇ - ⁇ type titanium alloy with excellent intermittent cutting performance.
  • the ⁇ - ⁇ type titanium alloy of the present invention contains C: 0.06 to 0.13 mass%, Al: 3.0 to 8.5 mass%, V: 5.0 mass% or less, Cr: 3.0 mass% or less, Fe: less than 2.5 mass%, Mo: 6.0 mass% or less, Ni: 5.0 mass% or less, Nb: 5.0 mass% or less, Ta: 5.0 mass%
  • One or more of the following is contained in a total of 2.0 to 10.0% by mass, and the balance is Ti and inevitable impurities.
  • the ⁇ - ⁇ type titanium alloy of the present invention has an average area ratio of TiC precipitates of 0.5% or less in an arbitrary cross section of 0.25 mm 2 or more in the titanium alloy substrate, and the circle of the TiC precipitates. The average equivalent diameter is 1 ⁇ m or less.
  • the ⁇ - ⁇ type titanium alloy has an ⁇ phase which is a close hexagonal crystal (hexagonalHclose-packed lattice (HCP)) and a ⁇ phase which is a body-centered cubic crystal (Body-Centered Cubic lattice (BCC)) in the structure. It is a mixed titanium alloy.
  • HCP hexagonalHclose-packed lattice
  • BCC Body-Centered Cubic lattice
  • C 0.06 to 0.13 mass%
  • C has the effect of improving strength.
  • C is finely precipitated as TiC in the ⁇ temperature range
  • the ⁇ phase crystal grains are refined and the hot workability is improved by the refinement. If the C content is less than 0.06% by mass, the action is insufficient. On the other hand, if the C content exceeds 0.13% by mass, coarse TiC having an average equivalent circle diameter of more than 1 ⁇ m and not dissolved in the ⁇ phase at room temperature remains, and the mechanical properties deteriorate. As a result, the intermittent cutting performance is adversely affected.
  • the lower limit of the C content is 0.06% by mass, preferably 0.07% by mass, more preferably 0.08% by mass
  • the upper limit of the C content is 0.13% by mass, preferably 0%. .12% by mass, more preferably 0.11% by mass.
  • Al 3.0 to 8.5% by mass
  • Al is an ⁇ -stabilizing element and is an element added to generate an ⁇ -phase. If the Al content is less than 3.0% by mass, ⁇ -phase generation is insufficient, sufficient strength is not exhibited, and a tensile strength (TS) of 900 MPa or more cannot be obtained. On the other hand, if the Al content exceeds 8.5% by mass, the ductility deteriorates and the elongation (EL) decreases to less than 10%. Therefore, the lower limit of the Al content is 3.0% by mass, preferably 3.2% by mass, and the upper limit of the Al content is 8.5% by mass, preferably 8.0% by mass.
  • V 5.0 mass% or less, Cr: 3.0 mass% or less, Fe: less than 2.5 mass%, Mo: 6.0 mass% or less, Ni: 5.0 mass% or less, Nb: 5. 1% or more of 0% by mass or less and Ta: 5.0% by mass or less in total 2.0 to 10.0% by mass
  • These elements are all ⁇ -stabilizing elements and are elements added to generate a ⁇ -phase. If the total content of these elements is less than 2.0% by mass, the amount of ⁇ -phase produced is too small. Therefore, the total content of these elements is 2.0% by mass or more, preferably 3.0% by mass or more. These elements also have the effect of improving the strength.
  • the elongation (EL) deteriorates. To do. In particular, when the Fe content is excessive, the decrease in elongation (EL) becomes significant. Moreover, when there is too much content of Cr, machinability will fall. Therefore, the upper limit of the content of these elements is defined as described above, and the upper limit of the total content of these elements is 10.0% by mass.
  • the ⁇ - ⁇ type titanium alloy of the present invention is composed of Ti and unavoidable impurities in addition to the above elements, but may contain the following elements alone or in combination.
  • Si 1.0% by mass or less
  • the ratio of Cr content to Fe content [Cr] / [Fe] is preferably 3.0 or less.
  • both Cr and Fe are ⁇ -stabilizing elements, but Fe has an effect of expanding the solid solubility limit of C as compared with Cr. If the ratio [Cr] / [Fe] of the Cr content to the Fe content exceeds 3.0, the effect of expanding the C solid solubility limit by Fe is lost, and the effect of suppressing the precipitation of TiC cannot be exhibited. Therefore, when Fe is contained, the upper limit of the Cr content to Fe content ratio [Cr] / [Fe] is 3.0, preferably 2.5.
  • the titanium alloy of the present invention is an ⁇ - ⁇ type titanium alloy whose structure is composed of an ⁇ phase and a ⁇ phase at room temperature.
  • TiC precipitates in the structure of the ⁇ - ⁇ type titanium alloy, that is, in the titanium alloy substrate, but the average value of the area ratio of TiC precipitates in an arbitrary cross section of 0.25 mm 2 or more in the titanium alloy substrate. Is 0.5% or less.
  • the average equivalent circle diameter of the TiC precipitates is 1 ⁇ m or less.
  • the upper limit of the average value of the area ratio of TiC precipitates in an arbitrary cross section of 0.25 mm 2 or more in the titanium alloy substrate is 0.5%, preferably 0.25%.
  • the upper limit of the average circle equivalent diameter of the TiC precipitates is 1 ⁇ m, preferably 0.8 ⁇ m.
  • the thickness of 0.25 mm 2 or more in the titanium alloy substrate is increased.
  • the average value of the area ratio of the TiC precipitates in an arbitrary cross section can be 0.5% or less, and the average value of the equivalent circle diameter of the TiC precipitates can be 1 ⁇ m or less.
  • ingots of titanium alloys having the component compositions shown in Table 1 were cast by the CCIM method (Cold Crucible Induction Melting). These ingots have a cylindrical shape with a diameter of 150 mm and a height of 150 mm.
  • Hot forging was performed under the following production conditions. Hot forging was performed by heating the ingot at 1200 ° C., forging at a forging ratio of about 1.5, cooling to water, heating to 900 ° C., and forging at a forging ratio of about 3.2 or more. By this hot forging, a titanium alloy plate having a long plate shape with a cross section of 20 mm in thickness and 190 mm in width was obtained. Next, after air-cooling to room temperature, the final titanium alloy plate used for a test was obtained by annealing at 800 degreeC for 2 hours. From this titanium alloy plate, a structure observation test piece, an end mill cutting test piece, and a tensile test piece were sampled and subjected to the following tests.
  • the tissue observation test piece is collected from a portion excluding the thickness of 2 mm from the front and back surfaces of the titanium alloy plate and the thickness of 50 mm from the side surface.
  • This test piece was embedded in a synthetic resin holder, polished so that the test piece was exposed, and further buffed.
  • the surface of the polished specimen is photographed at a magnification of 400 times. This photography is performed with four fields of view, and the total observation area is 0.25 mm 2 . From the image data thus obtained, image analysis software (Nano Hunter NS2K-Lt, manufactured by Nanosystem Co., Ltd.) was used to determine the area ratio of TiC precipitates and the equivalent circle diameter of each photograph.
  • ⁇ Room temperature tensile test> A tensile test piece was collected from the titanium alloy plate described above. The tensile test was performed in accordance with ASTM standard E8. The shape and dimensions of the tensile test piece are shown in FIG. The test temperature is room temperature (25 ° C.), and the strain rate is 100 / sec. From the test results, those having a tensile strength (TS) of 900 MPa or more and an elongation (EL) of 10% or more were accepted and judged to be a high-strength titanium alloy. Table 2 shows the tensile strength (TS) and elongation (EL) of each sample obtained in this test.
  • TS tensile strength
  • EL elongation
  • Sample No. in Table 2 Is the sample No. described in Table 1. Is consistent with Sample No. 4 and no. Examples 6 to 11 are invention examples, and the component composition shown in Table 1, the average area ratio of TiC precipitates and the average equivalent circle diameter shown in Table 2 both satisfy the conditions of the present invention. All others are comparative examples.
  • sample no. 4 and no. 6 to 11 can be judged to be high-strength titanium alloys having excellent intermittent machinability.
  • the amount of tool wear determined by the intermittent cutting test could not be satisfied with at least one of the tensile strength (TS) and elongation (EL) determined in the room temperature tensile test. That is, sample no. 1-3, no. 5 and no. 12 to 19 cannot be judged to be high-strength titanium alloys having excellent intermittent machinability.

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  • 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)
  • Powder Metallurgy (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

La présente invention concerne un alliage de titane de type a-ß à haute résistance présentant d'excellentes propriétés de travail à chaud et d'excellentes propriétés de découpe lors d'opérations de fraisage et de fraisage en bout. L'alliage de titane contient de 0,06 à 0,13 % en masse de C, de 3,0 à 8,5 % en masse de Al et de 2,0 à 10,0 % en masse au total d'une ou plusieurs des quantités suivantes : pas plus de 5,0 % en masse de V, pas plus de 3,0 % en masse de Cr, moins de 2,5 % en masse de Fe, pas plus de 6,0 % en masse de Mo, pas plus de 5,0 % en masse de Ni, pas plus de 5,0 % en masse de Nb et pas plus de 5,0 % en masse de Ta, le reste contenant du Ti et des impuretés inévitables. La valeur moyenne du rapport de section du précipité de TiC dans le matériau de base de l'alliage de titane est inférieure ou égale à 0,5 % et la valeur moyenne du diamètre en phase arrondie du précipité de TiC est inférieure ou égale à 1 µm.
PCT/JP2009/060475 2008-06-11 2009-06-08 ALLIAGE DE TITANE DE TYPE α－β Ceased WO2009151031A1 (fr)

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Application Number Priority Date Filing Date Title
JP2008-153217 2008-06-11
JP2008153217A JP2009299110A (ja) 2008-06-11 2008-06-11 断続切削性に優れた高強度α−β型チタン合金

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Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102154576A (zh) * 2011-04-21 2011-08-17 辽宁峰阁钛业集团有限公司 一种高强度高塑性钛合金
US20130164168A1 (en) * 2010-01-20 2013-06-27 Vsmpo-Avisma Corporation Secondary Titanium Alloy And The Art Of Its Manufacture
CN103627928A (zh) * 2013-12-12 2014-03-12 西北有色金属研究院 一种低温高强两相钛合金
CN104762525A (zh) * 2015-03-27 2015-07-08 常熟市双羽铜业有限公司 一种热交换器用钛合金管
US20180044763A1 (en) * 2015-03-26 2018-02-15 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Alpha-ß TITANIUM ALLOY
CN106521236B (zh) * 2016-10-25 2018-08-24 南京工业大学 一种含Fe的低成本近β型高强钛合金及其制备方法
JPWO2020179912A1 (fr) * 2019-03-06 2020-09-10
US20230064898A1 (en) * 2021-08-19 2023-03-02 Fusheng Precision Co., Ltd. Golf club head alloy, golf club head, heat treatment method for the golf club head alloy, and method for producing golf club head

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US20040221929A1 (en) 2003-05-09 2004-11-11 Hebda John J. Processing of titanium-aluminum-vanadium alloys and products made thereby
US7837812B2 (en) 2004-05-21 2010-11-23 Ati Properties, Inc. Metastable beta-titanium alloys and methods of processing the same by direct aging
US10053758B2 (en) 2010-01-22 2018-08-21 Ati Properties Llc Production of high strength titanium
US9255316B2 (en) 2010-07-19 2016-02-09 Ati Properties, Inc. Processing of α+β titanium alloys
US9206497B2 (en) 2010-09-15 2015-12-08 Ati Properties, Inc. Methods for processing titanium alloys
US8613818B2 (en) 2010-09-15 2013-12-24 Ati Properties, Inc. Processing routes for titanium and titanium alloys
US10513755B2 (en) 2010-09-23 2019-12-24 Ati Properties Llc High strength alpha/beta titanium alloy fasteners and fastener stock
US20120076686A1 (en) * 2010-09-23 2012-03-29 Ati Properties, Inc. High strength alpha/beta titanium alloy
US8652400B2 (en) 2011-06-01 2014-02-18 Ati Properties, Inc. Thermo-mechanical processing of nickel-base alloys
US9050647B2 (en) 2013-03-15 2015-06-09 Ati Properties, Inc. Split-pass open-die forging for hard-to-forge, strain-path sensitive titanium-base and nickel-base alloys
US9869003B2 (en) 2013-02-26 2018-01-16 Ati Properties Llc Methods for processing alloys
US9192981B2 (en) 2013-03-11 2015-11-24 Ati Properties, Inc. Thermomechanical processing of high strength non-magnetic corrosion resistant material
US9777361B2 (en) 2013-03-15 2017-10-03 Ati Properties Llc Thermomechanical processing of alpha-beta titanium alloys
US11111552B2 (en) 2013-11-12 2021-09-07 Ati Properties Llc Methods for processing metal alloys
US10094003B2 (en) 2015-01-12 2018-10-09 Ati Properties Llc Titanium alloy
WO2016152663A1 (fr) * 2015-03-26 2016-09-29 株式会社神戸製鋼所 Alliage de titane alpha-bêta
US10502252B2 (en) 2015-11-23 2019-12-10 Ati Properties Llc Processing of alpha-beta titanium alloys
CN111225989B (zh) * 2017-10-06 2022-03-15 莫纳什大学 改进的可热处理钛合金
CN112522539B (zh) * 2020-11-19 2022-04-08 西部超导材料科技股份有限公司 一种高动态性能钛合金及其制备方法
US12344918B2 (en) 2023-07-12 2025-07-01 Ati Properties Llc Titanium alloys

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JP2000204425A (ja) * 1998-11-12 2000-07-25 Kobe Steel Ltd 高強度・高延性α＋β型チタン合金
JP2005105335A (ja) * 2003-09-30 2005-04-21 Kobe Steel Ltd 高温強度に優れた耐熱Ｔｉ合金
JP2006219734A (ja) * 2005-02-14 2006-08-24 Kobe Steel Ltd 良好な延性を有する超高強度α−β型チタン合金

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JP2000204425A (ja) * 1998-11-12 2000-07-25 Kobe Steel Ltd 高強度・高延性α＋β型チタン合金
JP2005105335A (ja) * 2003-09-30 2005-04-21 Kobe Steel Ltd 高温強度に優れた耐熱Ｔｉ合金
JP2006219734A (ja) * 2005-02-14 2006-08-24 Kobe Steel Ltd 良好な延性を有する超高強度α−β型チタン合金

Cited By (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20130164168A1 (en) * 2010-01-20 2013-06-27 Vsmpo-Avisma Corporation Secondary Titanium Alloy And The Art Of Its Manufacture
US9458527B2 (en) * 2010-01-20 2016-10-04 Vsmpo-Avisma Corporation Secondary titanium alloy and the art of its manufacture
CN102154576A (zh) * 2011-04-21 2011-08-17 辽宁峰阁钛业集团有限公司 一种高强度高塑性钛合金
CN103627928A (zh) * 2013-12-12 2014-03-12 西北有色金属研究院 一种低温高强两相钛合金
CN103627928B (zh) * 2013-12-12 2015-11-11 西北有色金属研究院 一种低温高强两相钛合金
US20180044763A1 (en) * 2015-03-26 2018-02-15 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Alpha-ß TITANIUM ALLOY
CN104762525A (zh) * 2015-03-27 2015-07-08 常熟市双羽铜业有限公司 一种热交换器用钛合金管
CN106521236B (zh) * 2016-10-25 2018-08-24 南京工业大学 一种含Fe的低成本近β型高强钛合金及其制备方法
JPWO2020179912A1 (fr) * 2019-03-06 2020-09-10
WO2020179912A1 (fr) * 2019-03-06 2020-09-10 日本製鉄株式会社 Matériau de barre
JP7120437B2 (ja) 2019-03-06 2022-08-17 日本製鉄株式会社 棒材
US20230064898A1 (en) * 2021-08-19 2023-03-02 Fusheng Precision Co., Ltd. Golf club head alloy, golf club head, heat treatment method for the golf club head alloy, and method for producing golf club head

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