JP2000256769A - HIGH STRENGTH BETA Ti ALLOY EXCELLENT IN COLD WORKABILITY - Google Patents
HIGH STRENGTH BETA Ti ALLOY EXCELLENT IN COLD WORKABILITYInfo
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- JP2000256769A JP2000256769A JP11065258A JP6525899A JP2000256769A JP 2000256769 A JP2000256769 A JP 2000256769A JP 11065258 A JP11065258 A JP 11065258A JP 6525899 A JP6525899 A JP 6525899A JP 2000256769 A JP2000256769 A JP 2000256769A
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、優れた冷間加工性
を有すると共に、時効処理後の強度−延性バランスに優
れた新規な高強度β型チタン合金に関するものである。The present invention relates to a novel high-strength β-type titanium alloy having excellent cold workability and an excellent balance between strength and ductility after aging treatment.
【０００２】[0002]
【従来の技術】現在実用化されている代表的なβ型Ｔｉ
合金は、Ｔｉ−１５Ｖ−３Ｃｒ−３Ｓｎ−３Ａｌであ
り、この合金はコイル製造によって比較的安価に薄板状
に加工することができることから、例えばチタンゴルフ
クラブのヘッド材料等して広く実用化されている。しか
しながら、該汎用チタン合金の時効処理後の強度特性
（強度と延性のバランス）は必ずしも満足し得るものと
は言えず、冷間加工の可能な最低限の延性（伸び率で５
％程度）を確保することの必要上、強度は１２０ｋｇｆ
／ｍｍ2程度に止まっており、高強度チタン合金として
の実用性を更に高め、或いは新規応用分野を開拓してい
くには、現状の延性を留保しつつ一層の高強度化を実現
することが望まれる。2. Description of the Related Art A typical β-type Ti currently in practical use.
The alloy is Ti-15V-3Cr-3Sn-3Al, and since this alloy can be processed into a thin plate at a relatively low cost by coil production, it has been widely used as a head material for a titanium golf club, for example. I have. However, the strength characteristics (balance between strength and ductility) of the general-purpose titanium alloy after aging treatment cannot always be said to be satisfactory, and the minimum ductility (elongation rate of 5%) at which cold working is possible is not possible.
%), The strength is 120kgf
/ Mm 2, and in order to further improve the practicality as a high-strength titanium alloy or to open up new application fields, it is necessary to realize higher strength while retaining the current ductility. desired.
【０００３】[0003]
【発明が解決しようとする課題】本発明は上記の様な事
情に着目してなされたものであって、その目的は、冷間
加工の可能な延性を有しつつ、強度の一段と高められた
新規なβ型チタン合金を提供することにある。DISCLOSURE OF THE INVENTION The present invention has been made in view of the above-mentioned circumstances, and its object is to provide a ductile material capable of cold working and to further increase the strength. It is to provide a novel β-type titanium alloy.
【０００４】[0004]
【課題を解決するための手段】上記課題を解決すること
のできた本発明に係る高強度β型Ｔｉ合金とは、質量％
で、Ｖ：１１〜１６％、Ｃｒ：２．０〜４．５％、Ｓ
ｎ：２．０〜４．０％、Ａｌ：２．５〜４．５％、Ｍ
ｏ：０．５〜２％を含有するところに特徴を有してお
り、このチタン合金は、その優れた加工性と高い強度特
性を活かし、例えばゴルフクラブのヘッド材料などとし
て有効に活用できる。The high-strength β-type Ti alloy according to the present invention, which has solved the above-mentioned problems, has a mass percentage of
V: 11 to 16%, Cr: 2.0 to 4.5%, S
n: 2.0 to 4.0%, Al: 2.5 to 4.5%, M
o: It is characterized by containing 0.5 to 2%, and this titanium alloy can be effectively utilized as, for example, a golf club head material by utilizing its excellent workability and high strength characteristics.
【０００５】[0005]
【発明の実施の形態】上記の様に本発明では、冷間加工
の可能な延性を確保しつつその強度が一段と高められた
β型チタン合金を提供するもので、具体的にはＴｉ中に
含有させる合金元素の種類と各含有率を規定したところ
に特徴を有しており、含有元素の種類と含有率範囲を定
めた理由は下記の通りである。BEST MODE FOR CARRYING OUT THE INVENTION As described above, the present invention provides a β-type titanium alloy whose strength is further enhanced while ensuring ductility that can be worked in a cold working. It has a feature in that the types of alloying elements to be contained and the respective contents are defined, and the reasons for determining the types of the contained elements and the ranges of the contents are as follows.
【０００６】Ｖ：１１〜１６％ Ｖは全率固溶型のβ相安定化元素として冷間加工性を高
めるのに欠くことのできない元素であり、１１％未満で
は冷間加工によりマルテンサイト変態を起こす不安定な
β相となり、冷間加工時に割れを起こす原因になる。一
方、Ｖ量が多くなり過ぎると時効硬化性能が低下し、満
足のいく強度が得られなくなるので、１６％以下に抑え
なければならない。冷間加工性と時効硬化特性の兼ね合
いを考慮してより好ましいＶ含有量の下限は１２％、よ
り好ましい上限は１４％である。V: 11 to 16% V is an element which is indispensable for enhancing the cold workability as a β-phase stabilizing element of a solid solution type, and when it is less than 11%, it becomes a martensitic transformation by cold working. And an unstable β phase causing cracking during cold working. On the other hand, if the V content is too large, the age hardening performance is reduced, and a satisfactory strength cannot be obtained. Therefore, the V content must be suppressed to 16% or less. Considering the balance between cold workability and age hardening characteristics, a more preferred lower limit of the V content is 12%, and a more preferred upper limit is 14%.
【０００７】Ｃｒ：２．０〜４．５％ Ｃｒは共析反応型の元素であり、β相を安定化し冷間加
工性を確保するうえで欠くことのできない元素であり、
２．０％未満ではそれらの作用が有効に発揮されなくな
る。しかし、多過ぎるとβ相が安定になり過ぎて時効硬
化性能が低下し強度不足になるので４．５％以下に抑え
なければならない。冷間加工性と時効硬化性能を加味し
てより好ましいＣｒ含有率の下限は２．５％、より好ま
しい上限は４．０％である。Cr: 2.0-4.5% Cr is an element of the eutectoid reaction type, and is an indispensable element for stabilizing the β phase and ensuring cold workability.
If it is less than 2.0%, those effects cannot be exhibited effectively. However, if the amount is too large, the β phase becomes too stable, the age hardening performance decreases, and the strength becomes insufficient. Therefore, the β phase must be suppressed to 4.5% or less. Considering the cold workability and the age hardening performance, the more preferable lower limit of the Cr content is 2.5%, and the more preferable upper limit is 4.0%.
【０００８】Ｓｎ：２．０〜４．０％ Ｓｎは、β相を安定化すると共に、時効処理後の強度を
高めるのに重要な元素であり、２．０％未満ではそれら
の効果が不足気味となって強度不足となる。しかし多過
ぎると、拡散速度が遅くなりかえって時効硬化能を低下
させるので４．０％以下に抑えなければならない。Ｓｎ
含有量のより好ましい下限は２．５％、より好ましい上
限は３．５％である。[0008] Sn: 2.0 to 4.0% Sn is an important element for stabilizing the β phase and increasing the strength after aging treatment. If the content is less than 2.0%, the effect is insufficient. It feels weak and lacks strength. However, if the amount is too large, the diffusion rate becomes slower and the age hardening ability is reduced, so that it must be suppressed to 4.0% or less. Sn
A more preferred lower limit of the content is 2.5%, and a more preferred upper limit is 3.5%.
【０００９】Ａｌ：２．５〜４．５％ Ａｌは固溶強化元素であって、高強度化に欠くことので
きない元素であり、本発明で意図するレベルの強度を確
保するには２．５％以上含有させなければならない。し
かし多過ぎるとβ相の延性が低下し、冷間加工性が損な
われるので、４．５％以下に抑えなければならない。強
度と冷間加工性の兼ね合いを考慮してより好ましいＡｌ
含有量の下限は３．０％、より好ましい上限は４．０％
である。Al: 2.5-4.5% Al is a solid solution strengthening element, and is an element indispensable for increasing the strength. To ensure the level of strength intended in the present invention, 2. It must be contained at least 5%. However, if the content is too large, the ductility of the β phase is reduced and the cold workability is impaired, so that the content must be suppressed to 4.5% or less. More preferable Al considering the balance between strength and cold workability
The lower limit of the content is 3.0%, and the more preferable upper limit is 4.0%.
It is.
【００１０】Ｍｏ：０．５〜２％ Ｍｏは、適量添加することにより強度−延性バランスを
高める作用を有しており、その効果を有効に発揮させる
には０．５％以上、より好ましくは０．７５％以上含有
させなければならない。しかし、Ｍｏ量が多くなり過ぎ
ると時効硬化性能が低下し高強度化の目的が達成できな
くなるので、２％以下、より好ましくは１．５％以下に
抑えるべきである。Mo: 0.5 to 2% Mo has an effect of increasing the strength-ductility balance by adding an appropriate amount, and 0.5% or more, more preferably, Mo is effective in exerting the effect. It must be contained at least 0.75%. However, if the Mo content is too large, the age hardening performance is reduced and the purpose of increasing the strength cannot be achieved, so the content should be suppressed to 2% or less, more preferably 1.5% or less.
【００１１】本発明にかかるチタン合金における必須の
合金元素は上記の５種であり、残部は実質的にＴｉであ
るが、他のβ安定化元素であるＦｅ等を少量含有させる
ことも有効である。本発明のチタン合金に許容される不
可避不純物元素としては、たとえばＯ，Ｎ，Ｈ等があ
り、これらの不可避不純物は、上記本発明チタン合金の
特性を阻害しない限り微量含まれていても構わない。The essential alloy elements in the titanium alloy according to the present invention are the above five kinds, and the balance is substantially Ti. However, it is also effective to contain a small amount of other β-stabilizing element such as Fe. is there. The unavoidable impurity elements allowed in the titanium alloy of the present invention include, for example, O, N, H, and the like, and these unavoidable impurities may be contained in trace amounts as long as the characteristics of the titanium alloy of the present invention are not impaired. .
【００１２】既存のβ型チタン合金の中で代表的なの
は、前述の如くＴｉ−１５Ｖ−３Ｃｒ−３Ｓｎ−３Ａｌ
合金であるが、該β型チタン合金の強度は、時効熱処理
後の抗張力で高いものでも１２００ＭＰａまでであり、
コイル製造の可能な５％レベル以上の伸び率を維持しつ
つ１２００ＭＰａを超える高レベルの抗張力を有するも
のは知られていない。A typical example of the existing β-type titanium alloy is Ti-15V-3Cr-3Sn-3Al, as described above.
It is an alloy, but the strength of the β-type titanium alloy is up to 1200 MPa even with a high tensile strength after aging heat treatment.
Nothing has been known that has a high level of tensile strength exceeding 1200 MPa while maintaining an elongation of 5% or more, which is possible for coil production.
【００１３】ところが上記本発明の規定要件を満たすβ
型チタン合金は、後記実施例でも明らかにする如く５％
以上の伸び率を有しつつ、時効処理後の抗張力で１２０
０ＭＰａ以上の高い値を示し、こうした優れた強度・延
性バランスによって優れた加工性の下で高強度のチタン
合金製品を得ることが可能となる。However, β which satisfies the above-mentioned requirements of the present invention
The type titanium alloy is 5% as clarified in the examples described later.
While having the above elongation, the tensile strength after aging treatment is 120
It shows a high value of 0 MPa or more, and it is possible to obtain a high-strength titanium alloy product under excellent workability by such excellent strength-ductility balance.
【００１４】即ち本発明のβ型チタン合金は、高延性で
冷間加工性に優れたものであり、冷間での圧延加工、鍛
造加工、プレス加工等によって容易に加工することがで
きる。That is, the β-type titanium alloy of the present invention has high ductility and excellent cold workability, and can be easily worked by cold rolling, forging, pressing or the like.
【００１５】尚、本発明に係るβ型チタン合金の鋳造・
鍛造・熱延条件、時効熱処理（焼鈍）条件、脱スケール
条件、冷間加工条件等は特に制限されず、公知のβ型チ
タン合金に適用される条件をそのまま、或いは要求特性
に応じて適当に変更して適用すればよい。Incidentally, the casting and casting of the β-type titanium alloy according to the present invention
Forging and hot rolling conditions, aging heat treatment (annealing) conditions, descaling conditions, cold working conditions, and the like are not particularly limited, and the conditions applied to known β-type titanium alloys can be used as they are or appropriately according to required characteristics. It can be changed and applied.
【００１６】上記の様に本発明のβ型チタン合金は、冷
間加工に必要な適度の延性を有しつつ高い強度を有して
いるので、チタン合金が本来備えている優れた比強度や
耐食性などを有効に活かしつつ、冷間加工によって様々
の製品に加工することができ、例えばチタンゴルフクラ
ブのヘッド材料を始め、板ばねや釣り具等の素材として
有効に活用できる。As described above, the β-type titanium alloy of the present invention has a high ductility while having an appropriate ductility required for cold working, and therefore has excellent specific strength and inherent strength inherent in the titanium alloy. It can be worked into various products by cold working while effectively utilizing corrosion resistance and the like, and can be effectively used as a material for, for example, a head material of a titanium golf club, a leaf spring, a fishing gear and the like.
【００１７】[0017]
【実施例】以下、実施例を挙げて本発明をより具体的に
説明するが、本発明はもとより下記実施例によって制限
を受ける訳ではなく、前・後記の趣旨に適合し得る範囲
で適当に変更して実施することも可能であり、それらは
いずれも本発明の技術的範囲に包含される。EXAMPLES Hereinafter, the present invention will be described more specifically with reference to examples. However, the present invention is not necessarily limited by the following examples, and may be appropriately performed within a range that can conform to the purpose described above and below. Modifications can be made and all of them are included in the technical scope of the present invention.
【００１８】実施例 表１に示す成分組成のチタン合金をインダクトスカル溶
解法によって溶製し、８０ｍｍt×１３０ｍｍw×２６０
ｍｍL（約１２ｋｇ）の鋳塊を得る。これを１０００℃
（β温度域）加熱で４０ｍｍtに鍛造した後、脱スケー
ルと疵取りを兼ねて周囲を約２ｍｍ切削することにより
熱間圧延素材とし、これを１０００℃に再加熱してから
熱間圧延し、厚さ４．４ｍｍの熱延板を得た。EXAMPLE A titanium alloy having the composition shown in Table 1 was melted by the induct skull melting method to obtain 80 mm t × 130 mm w × 260.
An ingot of mm L (about 12 kg) is obtained. 1000 ℃
(Β temperature range) After forging to 40 mm t by heating, the surroundings are cut by about 2 mm for both descaling and flaw removal to obtain a hot-rolled material, which is reheated to 1000 ° C and hot-rolled. A hot rolled sheet having a thickness of 4.4 mm was obtained.
【００１９】得られた各熱延板を８００℃で３０分間焼
鈍した後、ショットブラスト・酸洗処理を施して厚さ４
ｍｍにまで脱スケールし、長手方向冷延（４ｍｍ→２．
８ｍｍ）および８００℃×５分間の焼鈍を行なって、厚
さ８ｍｍの冷延焼鈍板を得た。Each of the obtained hot-rolled sheets was annealed at 800 ° C. for 30 minutes, and then subjected to a shot blast and pickling treatment to obtain a thickness of 4 mm.
mm, and then cold-rolled in the longitudinal direction (4 mm → 2.
8 mm) and 800 ° C. × 5 minutes to obtain a cold-rolled annealed sheet having a thickness of 8 mm.
【００２０】得られた各冷延焼鈍板について、４８０℃
および５１０℃で８時間の時効熱処理を施してから引張
試験を行なった。結果は表１に示す通りであり、この表
より次の様に考察できる。Each of the obtained cold-rolled annealed sheets was 480 ° C.
After aging heat treatment at 510 ° C. for 8 hours, a tensile test was performed. The results are as shown in Table 1 and can be considered as follows from this table.
【００２１】Ｎｏ．１〜４は本発明の規定要件を全て満
たす実施例であり、５％レベル以上の伸び率を有しつつ
抗張力は１２００ＭＰａレベル以上の高い値を有してお
り、強度・延びバランスの非常に優れたものであること
が分かる。No. Examples 1 to 4 satisfy all the requirements of the present invention. The tensile strength has a high value of 1200 MPa or more while having an elongation of 5% or more, and the strength-elongation balance is extremely excellent. It turns out that it is a thing.
【００２２】これらに対しＮｏ．５，６は従来材、Ｎ
ｏ．７〜１６は本発明で定めるいずれかの要件を欠く比
較例であり、下記の様に延性不足であるか或いは抗張力
が低くて強度・延びバランスが不十分であり、本発明の
目的にそぐわない。On the other hand, no. 5 and 6 are conventional materials, N
o. Comparative Examples 7 to 16 lack any of the requirements defined in the present invention, and are inadequate in ductility or low in tensile strength and insufficient in strength-elongation balance as described below, and do not meet the purpose of the present invention.
【００２３】Ｎｏ．７，８，９，１０：ＶまたはＣｒの
含有量が規定範囲を外れる比較例であり、これらの元素
量が不足するものは冷延性が悪く、また多すぎる場合は
時効処理後の強度が低い。Ｎｏ．１１はＳｎの含有率が
不足する比較例で、時効処理後の延性が悪く、Ｎｏ．１
２は逆にＳｎ量が多過ぎる比較例で、冷延性は良好であ
るものの時効処理後の強度が低く、本発明の要求レベル
に達していない。No. 7, 8, 9, 10: Comparative examples in which the content of V or Cr is out of the specified range. Those in which the amounts of these elements are insufficient have poor cold-rolling properties, and in the case where they are too large, the strength after aging treatment is low. . No. No. 11 is a comparative example in which the Sn content is insufficient, and the ductility after aging treatment is poor. 1
Conversely, No. 2 is a comparative example in which the amount of Sn is too large. Although the cold-rolling property is good, the strength after aging treatment is low, and the required level of the present invention is not reached.
【００２４】Ｎｏ．１３，１４はＡｌ含有量が規定範囲
を外れる比較例であり、Ａｌ不足のＮｏ．１３では、冷
延性は良好であるものの時効処理後の強度が低く、Ａｌ
過剰のＮｏ．１４では冷延性が劣悪である。更にＮｏ．
１５はＭｏ量が不足する比較例で、強度・延性は従来材
（Ｎｏ．５，６）と殆ど変わらない。またＮｏ．１６は
Ｍｏ量が多過ぎる比較例であり、時効処理後の強度が不
足している。No. Nos. 13 and 14 are comparative examples in which the Al content is out of the specified range. In No. 13, although the cold rolling property was good, the strength after aging treatment was low,
Excess No. In No. 14, the cold rolling property is poor. No.
15 is a comparative example in which the Mo content is insufficient, and the strength and ductility are almost the same as those of the conventional materials (Nos. 5 and 6). No. 16 is a comparative example in which the Mo amount is too large, and the strength after the aging treatment is insufficient.
【００２５】[0025]
【表１】 [Table 1]
【００２６】[0026]
【発明の効果】本発明は以上の様に構成されており、β
型チタン合金中のＶ，Ｃｒ，Ｓｎ，Ａｌ，Ｍｏの各含有
量を規定することによって、冷間加工の可能な延性を有
すると共に、焼鈍後の強度で１２００ＭＰａレベル以上
の高い抗張力を有する強度・延びバランスの卓越したβ
型チタン合金を提供し得ることになった。そしてこのβ
型チタン合金は、その優れた延性と強度、更にはチタン
合金が本来有している高い比強度や耐食性を活かし、チ
タンゴルフクラブのヘッド材料等として有効に活用でき
る。The present invention is configured as described above,
By defining the respective contents of V, Cr, Sn, Al, and Mo in the type titanium alloy, it has a ductility that can be cold worked, and a high tensile strength of 1200 MPa or more in strength after annealing. Outstanding β of elongation balance
It is possible to provide a type titanium alloy. And this β
Titanium alloys can be effectively used as head materials for titanium golf clubs, taking advantage of their excellent ductility and strength, as well as the high specific strength and corrosion resistance inherent to titanium alloys.
Claims (2)
２．０〜４．５％、Ｓｎ：２．０〜４．０％、Ａｌ：
２．５〜４．５％、Ｍｏ：０．５〜２％を含有すること
を特徴とする冷間加工性に優れた高強度β型チタン合
金。1. V: 11 to 16% by mass%, Cr:
2.0 to 4.5%, Sn: 2.0 to 4.0%, Al:
A high-strength β-type titanium alloy excellent in cold workability, characterized by containing 2.5 to 4.5% and Mo: 0.5 to 2%.
されるものである請求項1に記載の高強度β型チタン合
金。2. The high-strength β-type titanium alloy according to claim 1, which is used as a material for a golf club head.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP06525899A JP3977956B2 (en) | 1999-03-11 | 1999-03-11 | High strength β-type Ti alloy with excellent cold workability |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP06525899A JP3977956B2 (en) | 1999-03-11 | 1999-03-11 | High strength β-type Ti alloy with excellent cold workability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2000256769A true JP2000256769A (en) | 2000-09-19 |
| JP3977956B2 JP3977956B2 (en) | 2007-09-19 |
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| Application Number | Title | Priority Date | Filing Date |
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| JP06525899A Expired - Lifetime JP3977956B2 (en) | 1999-03-11 | 1999-03-11 | High strength β-type Ti alloy with excellent cold workability |
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006124810A (en) * | 2004-11-01 | 2006-05-18 | Kobe Steel Ltd | beta TITANIUM ALLOY FOR COLD WORKING AND ITS PRODUCTION METHOD |
| CN111306229A (en) * | 2020-03-03 | 2020-06-19 | 沈阳和世泰通用钛业有限公司 | Small-wire-diameter titanium alloy spring and preparation method and application thereof |
-
1999
- 1999-03-11 JP JP06525899A patent/JP3977956B2/en not_active Expired - Lifetime
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006124810A (en) * | 2004-11-01 | 2006-05-18 | Kobe Steel Ltd | beta TITANIUM ALLOY FOR COLD WORKING AND ITS PRODUCTION METHOD |
| JP4632239B2 (en) * | 2004-11-01 | 2011-02-16 | 株式会社神戸製鋼所 | Beta titanium alloy material for cold working |
| CN111306229A (en) * | 2020-03-03 | 2020-06-19 | 沈阳和世泰通用钛业有限公司 | Small-wire-diameter titanium alloy spring and preparation method and application thereof |
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| Publication number | Publication date |
|---|---|
| JP3977956B2 (en) | 2007-09-19 |
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