WO2001092589A1 - Alliage de titane presentant une excellente ductilite, resistance a la fatigue et rigidite et son procede de production - Google Patents

Alliage de titane presentant une excellente ductilite, resistance a la fatigue et rigidite et son procede de production Download PDF

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Publication number
WO2001092589A1
WO2001092589A1 PCT/JP2000/003461 JP0003461W WO0192589A1 WO 2001092589 A1 WO2001092589 A1 WO 2001092589A1 JP 0003461 W JP0003461 W JP 0003461W WO 0192589 A1 WO0192589 A1 WO 0192589A1
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WO
WIPO (PCT)
Prior art keywords
titanium alloy
fatigue strength
ductility
rigidity
producing
Prior art date
Application number
PCT/JP2000/003461
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English (en)
Japanese (ja)
Inventor
Nozomu Ariyasu
Satoshi Matsumoto
Original Assignee
Sumitomo Metal Industries, Ltd.
Honda Giken Kogyo Kabushiki Kaisha
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Sumitomo Metal Industries, Ltd., Honda Giken Kogyo Kabushiki Kaisha filed Critical Sumitomo Metal Industries, Ltd.
Priority to PCT/JP2000/003461 priority Critical patent/WO2001092589A1/fr
Priority to EP00929912A priority patent/EP1295955A4/fr
Publication of WO2001092589A1 publication Critical patent/WO2001092589A1/fr
Priority to US10/303,731 priority patent/US20030084970A1/en

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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
    • 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

  • Titanium alloy with excellent ductility, fatigue strength and rigidity and its manufacturing method
  • the present invention is useful for structural parts that require light weight and excellent mechanical properties, such as automobile engine conrods, valves, camshafts, crankshafts, pushrods, aircraft, and high-speed railway vehicles.
  • the present invention relates to a titanium alloy having high rigidity and excellent ductility and fatigue strength, and a method for producing the same. Background art
  • Titanium alloys are lightweight, have high strength, and are also excellent in corrosion resistance and heat resistance. Therefore, application to various mechanical parts for automobiles, aircraft, and high-speed railway vehicles is being studied.
  • titanium alloys have a Young's modulus that is about half that of steel materials, so when applied to mechanical structural materials, the occurrence of buckling and bending must be considered.
  • a design that increases the cross-sectional area of the part is required to secure a certain strength.
  • Such component design makes it impossible to take advantage of the excellent properties of titanium alloy such as light weight and high strength.
  • JP-A-5-5142 proposes a method for producing a titanium-based composite material in which a TiB solid solution is dispersed at a predetermined volume ratio in a matrix made of a titanium alloy. According to this manufacturing method, a composite material exhibiting excellent properties such as strength, rigidity, and abrasion resistance from room temperature to high temperature can be obtained.
  • melting, sintering, or powder metallurgy was premised because of poor plastic workability, and application to large structural materials was difficult.
  • knowledge on the matrix structure of the manufactured composite materials is not disclosed, and it is unclear whether ductility and fatigue strength required for structural materials can be secured.
  • Japanese Patent Application Laid-Open No. 10-1760 proposes a particle-reinforced titanium-based composite material containing TiB or TiC particles and using a 1-type titanium alloy as a matrix and controlling the structure to a needle-like phase structure.
  • a particle-reinforced titanium-based composite material containing TiB or TiC particles and using a 1-type titanium alloy as a matrix and controlling the structure to a needle-like phase structure.
  • TiB or TiC is used as the ceramic particles for reinforcement, so the powder metallurgy method is premised on its production, and it is difficult to apply it to large structural materials.
  • the matrix structure becomes a needle-like structure, the Young's modulus is high, but sufficient ductility cannot be obtained. Disclosure of the invention
  • titanium alloys have excellent specific strength, but have a problem that their Young's modulus is significantly lower than that of steel materials.
  • various types of composite materials have been studied, but problems remain in hot workability and ductility.
  • structural components are used in even more severe environments and are required to reduce manufacturing costs, and are required to have excellent hot workability and to have predetermined strength characteristics. Become so.
  • automotive condolution parts are required to have hot workability, high rigidity, excellent ductility and excellent fatigue strength. It has become.
  • titanium alloys having these characteristics have not been developed yet.
  • the present invention has been made in view of a request for development of a titanium alloy used for such a mechanical component, and is a titanium alloy which is hot workable and has excellent ductility, fatigue strength and rigidity, and a method for producing the same. Intended to provide ing.
  • a specific object of the present invention is to be able to perform hot forging or hot rolling, to have a high rigidity with a tensile strength of at least lOOMpa and a Young's modulus of at least 130 Gpa, and to have a predetermined ductility and fatigue strength. We are developing titanium alloys.
  • the present inventors conducted various studies on the components, finely dispersed particles, and matrix structure in order to develop the above-mentioned titanium alloy. As a result, the following findings (a) to (c) were obtained. I got it.
  • Applicable dispersed particles include titanium carbide or titanium boride generated by crystallization and / or precipitation reaction in the matrix, but their Young's modulus as particles is 1.3 times or more larger than titanium carbide It is effective to use titanium boride.
  • phase stabilizing elements When aging treatment is performed on titanium alloys containing Hf with Al, oxygen, or Sn or I, these components exhibit age hardening that promotes the formation of intermetallic compounds (Ti 3 Al). Fatigue strength can be greatly improved.
  • the ⁇ -phase stabilizing element has an effect of lowering the Young's modulus, but has an effect of improving hot workability.
  • the present invention has been completed on the basis of the above findings, and has a method for producing a titanium alloy of the following (1), (3) and (4), and a titanium alloy of the following (2), (3) and (4): The main point is.
  • ⁇ 0.5 to 3.0%
  • a titanium alloy in which metal boride is uniformly crystallized and / or precipitated in the matrix, and the matrix structure is equiaxed ⁇ structure Is a titanium alloy having excellent ductility, fatigue strength and stiffness characterized by having a content of at least 40 vol%.
  • This titanium alloy is of type or ⁇ + type.
  • This is a method for producing a titanium alloy with excellent ductility, fatigue strength and rigidity, characterized in that the heating temperature of the alloy is set to be 10 ° C or lower than that of Transus.
  • the solution treatment is performed in a temperature range of (? Transus-350 ° C) to (? Transzas-10 ° C), and if necessary, an aging treatment is performed.
  • FIG. 1 is a diagram showing various properties of a titanium alloy tested in Example 1 after solution treatment.
  • FIG. 2 is a view showing various properties of the titanium alloy tested in Example 1 after solution treatment or after aging treatment.
  • the metal boride is finely crystallized and / or precipitated and uniformly dispersed in the matrix, and if necessary, an appropriate amount of a phase stabilizing element such as Al or oxygen is contained.
  • the matrix structure is controlled to have an equiaxial structure ratio (hereinafter also referred to as “equiaxial ratio”) of at least 40% in terms of area ratio (same as volume ratio), thereby improving ductility and It is characterized by ensuring fatigue strength.
  • Sn, Zr, and Hf which are neutral elements, may be contained as necessary to improve high-temperature strength, improve creep resistance, or use a ⁇ phase stabilizing element as a ⁇ phase monolayer.
  • the amount of addition is limited by the V equivalent to such an extent that it does not become too small, so that ⁇ transduction is reduced and hot workability is improved.
  • Titanium alloys are classified into three types according to their microstructure at room temperature: type 5, +5 and '/ ?, and the present invention is directed to ⁇ and type + titanium alloys. .
  • equiaxed tissue is superior to acicular tissue.
  • a mixture with a needle-like structure generated by transformation from the ⁇ phase may be used.
  • the ratio of the equiaxed structure that is, the equiaxed ratio must be 40% or more in area ratio.
  • the equiaxed ratio is 50% or more.
  • the microstructure can be observed with an optical microscope after a sample is taken from the alloy matrix and polished and corroded.
  • the area ratio of the equiaxed ⁇ -structure specified in the present invention is obtained by performing image processing on the matrix of a microscopically observed tissue photograph, classifying the matrix into equiaxed tissue and needle-shaped tissue, and determining the ratio. Measure.
  • the reason why the equiaxial ratio is defined in the present invention is that the properties of the ductility and the fatigue strength of the titanium alloy largely depend on the area ratio of the equiaxial braided structure. 2.
  • the metal boride (Ti B) in the matrix of the titanium alloy B is contained and crystallized and / or precipitated during solidification and cooling.
  • the Young's modulus of the titanium alloy is very high relative to the titanium alloy, and the Young's modulus of the titanium alloy can be improved in accordance with the composite rule.
  • the content is set to 0.5 to 3.0%.
  • ⁇ -phase stabilizing element Al and oxygen are phase stabilizing elements, have a large solid solution hardening effect, and significantly improve the Young's modulus. However, if 1 is less than 5.5% and oxygen is less than 0.07%, the effect is not sufficiently exhibited, while if A1 exceeds 10% and oxygen exceeds 0.25%, workability and ductility decrease. I do. Therefore, the content of both should be A1: 5.5 to 10% and 0: 0.07 to 0.25%. Desirably, A1: 7 to 9% and oxygen: 0.07 to 0.15%.
  • phase stabilizing elements include C, H and N, all of which reduce the room-temperature ductility, so the upper limits are C: 0.1%, H: 0.05% and N: 0.1%. .
  • a neutral element or a Z and? Phase stabilizing element can be blended.
  • any of the added elements dissolve in the matrix.
  • most of the neutral elements Zr and Hf form solid solutions in the matrix, but crystallize and / or precipitate zirconium boride and hafnium borohydride as metal borides in trace amounts. Since these are very small, improvement in Young's modulus cannot be expected.
  • Sn, Zr, and Hf which are neutral elements, can be contained.
  • Sn, Zr, and Hf exert the effect of solid solution strengthening and have little effect on improving Young's modulus, but can increase high-temperature strength.
  • the upper limit is set to 20% in total. Desirably, the total is 5% or less.
  • Phase stabilizing elements include V, Mo, Cr, Fe, Nb, Ni and W.
  • the contained / phase stabilizing element has the effect of lowering the transus and improving the hot workability.
  • these elements form a solid solution in the titanium alloy matrix and suppress intermetallic compounds (Ti 3 Al) generated more than necessary. This has the effect of increasing the content of A1.
  • an excessive content greatly reduces the Young's modulus, so one or more types can be added in a range of 10% or less in V equivalent shown by the following formula (a). Desirably, the V equivalent is 5% or less.
  • Titanium alloy ingots are produced by adding titanium sponge, which is a titanium raw material, to pure Al, electrolytic Sn, Zr sponge, pure Hf, A1-V master alloy, Al-Mo master alloy, and Mo, Cr, V, etc.
  • a single substance is appropriately selected and blended in a predetermined amount to prepare a compacted molten raw material.
  • A1 boride and Fe boride are used as the B source in the raw material to crystallize, precipitate and disperse Ti B in the titanium alloy.
  • the oxygen content of Ingo' metropolitan can be adjusted to some extent by the type of titanium sponge, if you need to adjust in large amounts, the Ti_ ⁇ 2 is used as the adjustment member.
  • the adjusted raw material is arc-melted by melting a consumable electrode by a vacuum melting furnace or by non-consumable electrode melting by plasma arc melting to produce an alloy ingot.
  • the produced titanium alloy ingot is subjected to hot working by forging or rolling to obtain a predetermined microstructure, and is appropriately subjected to heat treatment to adjust mechanical properties.
  • heat treatment to adjust mechanical properties.
  • the structure in the matrix varies greatly depending on the heating conditions in the vicinity of the transus.
  • hot working is performed at a temperature higher than the transus, needle-like ⁇ -structures are likely to appear, and the heat at a temperature lower than the transus In the case of cold working, equiaxed tissue is likely to appear.
  • the heating temperature at the time of finishing hot working is lower than the temperature of Transus.
  • the phase and the / phase are mixed.
  • the acicular structure and the equiaxed structure mix.
  • the heating temperature during finishing hot working must be at least 10 ° C lower than Transus.
  • the lower limit of the heating temperature is not particularly limited, but may be any temperature higher than the lower limit of the hot working.
  • the heating temperature at the time of finishing hot working is specified, and the heating temperature at the time of rough working before finish working may be a temperature exceeding ⁇ transus.
  • hot working of a titanium alloy ingot is necessary not only to work to approximate the part shape, but also to make the matrix a predetermined microstructure.
  • the equiaxed structure in order for the equiaxed structure to appear in the matrix, it is necessary to apply a heat treatment after applying the processing strain. For example, once the microstructure becomes a needle-like structure, it cannot be made into an equiaxed structure no matter how much heat treatment is applied thereafter.
  • To change the matrix from acicular to equiaxed it is necessary to heat it again to a temperature lower than?
  • the hot-worked titanium alloy is subjected to a solution treatment or an aging heat treatment to adjust its mechanical properties.
  • a solution treatment or an aging heat treatment By making the temperature of the solution treatment 10 ° C or more lower than that of Transus, it is possible to secure the equiaxed tissue formed by hot working as it is.
  • the treatment temperature is too low, the effect of the solution treatment is lost, so that the temperature is set to (? Transus-350 ° C) or more. Therefore, in the present invention, the solution treatment is performed at (? Transus-350 ° C) to ⁇ Transus-10 ° C), and more preferably
  • the temperature range is from ⁇ Transus-200 ° C) to (? Transus-100 ° C). Furthermore, the aging treatment promotes the formation of intermetallic compounds (Ti 3 Al), thereby further improving the fatigue strength of the titanium alloy.
  • the conditions of the aging treatment vary depending on the alloy composition, but it is desirable that the treatment temperature is 500 to 600 ° C and the treatment time is 5 hours or more.
  • a titanium alloy having the composition shown in Table 1 was arc-melted using a vacuum melting furnace to produce an ingot with a diameter of 140.
  • the T / A trans of the titanium alloy tested is 1070 ° C.
  • the obtained alloy ingot was subjected to hot forging and solution treatment twice under the following conditions to obtain a test material.
  • Rough forging Forging dimension Outer diameter 80mm (working ratio 68%, forging ratio 3)
  • Heating temperature 1170 ° C ( ⁇ Transus + 100.C)
  • Heating temperature 1040 ° C to 1170 ° C (The individual heating temperature is shown in Fig. 1.)
  • Heating temperature 700 ° C ⁇ : 1100 ° C (The individual heating temperature is shown in Fig. 1.)
  • Fig. 1 From the results in Fig. 1, it can be seen that the tensile strength of all the test materials is l lOO Mpa or higher, the Young's modulus is 130 Gpa or higher, and high rigidity is ensured. 3-6 have an equiaxed ratio of 40 vol% or more, and have excellent fatigue strength and ductility in addition to rigidity.
  • Example 1 Using the alloy ingot obtained in Example 1, the conditions of hot forging were changed, and the effect of the aging treatment after the solution treatment was confirmed.
  • the tested titanium alloys were subjected to the following processes A to D.
  • Forging dimension 25mm outside diameter (working rate 97%, forging ratio 30) Heating temperature: 1170 ° C (? Transas + 100 ° C)
  • Forging and elongation dimensions 25 mm outside diameter (working ratio 97%, forging ratio 30) Heating temperature: 1170 ° C ( ⁇ Transus + 100 ° C)
  • Forging / extension size Outer diameter 80 dragon (working ratio 68%, forging ratio 3) Heating temperature: 1170 ° C ( ⁇ Transus + 100 ° C)
  • Forging / stretching dimensions Outer diameter 25mm (Processing ratio 90%, Forging ratio 10) Heating temperature: 1040 ° C ⁇ Transus — 30 ° C) 4-3 Solution treatment
  • Processes A and B which are comparative examples, have a tensile strength of llOOMpa or higher, a Young's modulus of 130 Gpa or higher, and high rigidity.However, the heating temperature of finish forging is inappropriate. The ductility and fatigue strength are not secured.
  • processes C and D which are examples of the invention, exhibit excellent ductility and fatigue strength in addition to high rigidity. Further, in the process D, by performing the aging treatment, it becomes possible to increase the heat resistance and the tensile strength and further improve the fatigue strength.
  • the titanium alloy of this invention since it has the characteristic which is high rigidity required as a structural material, and is excellent in ductility and fatigue strength, it provides a mechanical part which satisfies excellent mechanical properties with a light weight. it can. Therefore, the titanium alloy of the present invention can be widely used for automobile engine conrods, camshafts, crankshafts and pushrods, aircraft structural members, high-speed railway vehicle parts, and the like.

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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)
  • Forging (AREA)

Abstract

La présente invention concerne un alliage de titane, dans la matrice duquel un borure métallique est cristallisé et/ou déposé de manière homogène. Cet alliage est caractérisé en ce que la matrice présente une structure α équiaxiale, dans une quantité supérieure ou égale à 40 % en vol. Cet alliage de titane peut être produit par soumission à un usinage de finition à chaud, à une température de 10 °C ou inférieure à sa température β transus. Ledit alliage de titane présente une grande rigidité, une excellente ductilité et une très bonne résistance à la fatigue, qui sont des propriétés requises par un élément de structure, et peut être largement utilisé pour des parties de moteurs d'automobiles, des éléments de structure d'avions, des parties d'autorails de transport à grande vitesse et des parties similaires.
PCT/JP2000/003461 2000-05-29 2000-05-29 Alliage de titane presentant une excellente ductilite, resistance a la fatigue et rigidite et son procede de production WO2001092589A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
PCT/JP2000/003461 WO2001092589A1 (fr) 2000-05-29 2000-05-29 Alliage de titane presentant une excellente ductilite, resistance a la fatigue et rigidite et son procede de production
EP00929912A EP1295955A4 (fr) 2000-05-29 2000-05-29 Alliage de titane presentant une excellente ductilite, resistance a la fatigue et rigidite et son procede de production
US10/303,731 US20030084970A1 (en) 2000-05-29 2002-11-26 Titanium alloy having high ductility, fatigue strength and rigidity and method of manufacturing same

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PCT/JP2000/003461 WO2001092589A1 (fr) 2000-05-29 2000-05-29 Alliage de titane presentant une excellente ductilite, resistance a la fatigue et rigidite et son procede de production

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Cited By (2)

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JP2009174709A (ja) * 2007-12-25 2009-08-06 Yamaha Motor Co Ltd 破断分割型コンロッド、内燃機関、輸送機器および破断分割型コンロッドの製造方法
JP2019512046A (ja) * 2015-12-22 2019-05-09 ストック カンパニー“チェペトスキー メカニカル プラント” チタン合金から棒材を製造する方法

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US7531021B2 (en) * 2004-11-12 2009-05-12 General Electric Company Article having a dispersion of ultrafine titanium boride particles in a titanium-base matrix
US7559853B2 (en) * 2005-06-20 2009-07-14 Sri Sports Limited Golf club head and method for manufacturing the same
US20080035250A1 (en) * 2006-08-09 2008-02-14 United Technologies Corporation Grain refinement of titanium alloys
FR2940319B1 (fr) * 2008-12-24 2011-11-25 Aubert & Duval Sa Procede de traitement thermique d'un alliage de titane, et piece ainsi obtenue
WO2013124001A1 (fr) 2012-02-25 2013-08-29 Adamco Ag Composé auto-stabilisant de matrice de métal d'aluminium et d'halloysite
US9957836B2 (en) 2012-07-19 2018-05-01 Rti International Metals, Inc. Titanium alloy having good oxidation resistance and high strength at elevated temperatures
CN107377842B (zh) * 2017-09-19 2018-08-03 陕西华镁特材科技有限公司 一种Ti6Al7Nb钛合金大规格板坯的制备方法
RU2710407C1 (ru) * 2019-07-26 2019-12-26 Федеральное государственное унитарное предприятие "Центральный научно-исследовательский институт конструкционных материалов "Прометей" имени И.В. Горынина Национального исследовательского центра "Курчатовский институт" (НИЦ "Курчатовский институт" - ЦНИИ КМ "Прометей") Сплав на основе титана

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2009174709A (ja) * 2007-12-25 2009-08-06 Yamaha Motor Co Ltd 破断分割型コンロッド、内燃機関、輸送機器および破断分割型コンロッドの製造方法
JP2019512046A (ja) * 2015-12-22 2019-05-09 ストック カンパニー“チェペトスキー メカニカル プラント” チタン合金から棒材を製造する方法

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EP1295955A1 (fr) 2003-03-26
EP1295955A4 (fr) 2004-05-12

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