JPH0463239A - High strength and high toughness ti alloy and method for heat treating it - Google Patents
High strength and high toughness ti alloy and method for heat treating itInfo
- Publication number
- JPH0463239A JPH0463239A JP17596390A JP17596390A JPH0463239A JP H0463239 A JPH0463239 A JP H0463239A JP 17596390 A JP17596390 A JP 17596390A JP 17596390 A JP17596390 A JP 17596390A JP H0463239 A JPH0463239 A JP H0463239A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- strength
- toughness
- weight
- reinforcing elements
- Prior art date
- Legal status (The legal status 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 status listed.)
- Pending
Links
- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 39
- 238000000034 method Methods 0.000 title claims description 9
- 230000032683 aging Effects 0.000 claims abstract description 15
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 10
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 9
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 9
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 9
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 9
- 238000010438 heat treatment Methods 0.000 claims abstract description 8
- 229910052742 iron Inorganic materials 0.000 claims abstract description 8
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 8
- 229910052718 tin Inorganic materials 0.000 claims abstract description 8
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 8
- 229910052802 copper Inorganic materials 0.000 claims abstract description 7
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 7
- 229910052733 gallium Inorganic materials 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052782 aluminium Inorganic materials 0.000 claims abstract 3
- 229910045601 alloy Inorganic materials 0.000 claims description 11
- 239000000956 alloy Substances 0.000 claims description 11
- 238000005728 strengthening Methods 0.000 claims description 11
- 229910052748 manganese Inorganic materials 0.000 claims description 2
- 230000003014 reinforcing effect Effects 0.000 abstract 5
- 230000000694 effects Effects 0.000 description 7
- 239000000243 solution Substances 0.000 description 6
- 150000001875 compounds Chemical class 0.000 description 5
- 230000007423 decrease Effects 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- 238000005242 forging Methods 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 238000005098 hot rolling Methods 0.000 description 2
- 229910052761 rare earth metal Inorganic materials 0.000 description 2
- 239000000523 sample Substances 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910009843 Ti3Sn Inorganic materials 0.000 description 1
- 229910000756 V alloy Inorganic materials 0.000 description 1
- 238000003483 aging Methods 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 229910052731 fluorine Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 210000003625 skull Anatomy 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
Description
（産業上の利用分野）
本発明は、高強度高靭性Ｔｉ合金およびその熱処理方法
に係わり、例えば、航空機エンジン用ファンディスク、
タービンブレード、産業用ガスタービン、自動車用コネ
クティングロッド等の高強度、高靭性でかつ軽量である
ことが要求されるＴｉ合金製部材の素材として好適に利
用される高強度高靭性Ｔｉ合金およびその熱処理方法に
関するものである。
（従来の技術）
Ｔｉ合金は軽量でかつ高強度が得られる（高比強度であ
る）ので、従来より多くの合金が開発され、そして実用
に供されている。
このようなＴｉ合金には、α＋β型のＴｉ−６％Ａｎ−
４％Ｖ合金や、ｎｅａｒ β型ｃ７）Ｔｉ −１７（
Ｔｉ−５％ＡＪＩ−２％５ｎ−２％Ｚｒ−４％Ｃｒ−４
％Ｍ ｏ ）合金、Ｔｉ−１０％Ｖ−２％Ｆｅ−３％Ａ
旦合金等がある。
これらのＴｉ合金は、α強化元素であるＡ！；Ｌ（Ｓｎ
、Ｚｒ）とβ強化元素であるＭ ｏ 、 Ｃｒ 。
Ｖ、Ｆｅ等を適量組み合わせたものである。
（発明が解決しようとする課題）
上記した従来のＴｉ合金は、Ｎｉを多量に含む耐熱鋼や
耐熱合金などと比べるとかなり軽量であり、それなりの
強度および耐熱性を有しているが、上述したように、自
動車や航空機のエンジン、産業用ガスタービン等におい
ては、高性能化の要求が高まる一方であり、このような
要求に対応できるようにさらに高強度高靭性化したＴｉ
合金の開発が望まれているという課題があった。
（発明の目的）
本発明は、このような従来の課題にかんがみてなされた
もので、従来の高比強度のＴｉ合金において、その強度
および靭性をさらに向上させることができるようにする
ことを目的としている。(Industrial Application Field) The present invention relates to a high-strength, high-toughness Ti alloy and a heat treatment method thereof, and includes, for example, a fan disk for an aircraft engine,
A high-strength, high-toughness Ti alloy suitable for use as a material for Ti alloy components that require high strength, high toughness, and light weight, such as turbine blades, industrial gas turbines, and automobile connecting rods, and its heat treatment. It is about the method. (Prior Art) Since Ti alloys are lightweight and have high strength (high specific strength), many alloys have been developed and put into practical use. Such Ti alloys include α+β type Ti-6%An-
4% V alloy, near β type c7) Ti-17 (
Ti-5%AJI-2%5n-2%Zr-4%Cr-4
%Mo) alloy, Ti-10%V-2%Fe-3%A
There are other types such as dango. These Ti alloys contain A! which is an α-strengthening element. ;L(Sn
, Zr) and β-strengthening elements Mo, Cr. It is a combination of appropriate amounts of V, Fe, etc. (Problems to be Solved by the Invention) The conventional Ti alloys described above are considerably lighter than heat-resistant steels and heat-resistant alloys containing a large amount of Ni, and have a certain degree of strength and heat resistance. As mentioned above, there is an ever-increasing demand for higher performance in automobile and aircraft engines, industrial gas turbines, etc., and in order to meet these demands, we are developing Ti, which has even higher strength and toughness.
The problem was that the development of an alloy was desired. (Object of the Invention) The present invention was made in view of such conventional problems, and an object thereof is to further improve the strength and toughness of conventional Ti alloys with high specific strength. It is said that
（課題を解決するための手段）
本発明に係わ高強度高靭性Ｔｉ合金は、α強化元素であ
るＡ文、Ｓｎ、Ｚｒ、Ｇａのうちから選ばれる１種また
は２種以上の元素と、β強化元素であるＭｏ、Ｖ、Ｎｂ
、Ｔａ、Ｃｒ、Ｗ、Ｆｅ。
Ｃｏ 、Ｎｉ 、Ｃｕのうちから選ばれる１種または２
種以上の元素と、０．５〜３０重量％のＭｎを含み、残
部Ｔｉおよび不純物よりなる構成としたことを特徴とし
ており、実施態様においては、Ａ文、Ｓｎ、Ｚｒ含有量
が、
１重量％≦ＡｆＬ＋ （Ｓ ｎ／３）＋ （Ｚ ｒ／６
）５１０重量％
Ｍ ｏ 、 Ｖ 、 Ｎ ｂ 、 Ｔ ａ 、 Ｃｒ
、 Ｗ 、 Ｍ ｎ 、 Ｆ ｅ 。
Ｃｏ、Ｎｉ、Ｃｕ含有量が、
５重量％≦Ｍ ｏ ＋ （Ｖ／ １ 、５）＋（Ｎｂ／
３．６）＋ （Ｔａ／４．５）＋ （Ｃｒｌｏ 、６４
）＋ （Ｗ／２．６）＋ （Ｍｎ１０．６４）＋ （Ｆ
ｅ１０．３５）＋ （Ｃｏ１０．７）＋ （Ｎｉ１０．
９）＋（Ｃｕ／１．３）≦３０重量％
の関係を満足する構成としたことを特徴としており、上
記した高強度高靭性Ｔｉ合金の構成を前述した従来の課
題を解決するための手段としている。
また、本発明に係わる高強度高靭性Ｔｉ合金の熱処理方
法は、前記Ｔｉ合金を６５０〜１２００℃で熱間加工し
た後、３５０〜６５０℃で直接時効処理する構成とした
ことを特徴としておりまた、そのほか、前記Ｔｉ合金を
６５０〜１２００℃で熱間加工した後、６５０〜９５０
℃で溶体化処理を施し、３５０〜６５０℃で時効処理す
る構成としたことを特徴としており、上記した高強度高
靭性Ｔｉ合金の熱処理方法の構成を前述した従来の課題
を解決するための手段としている。
次に、本発明に係わる高強度高靭性Ｔｉ合金の化学成分
限定理由について説明する。
Ａｌｌ、Ｓｎ、Ｚｒ、Ｇａはα相に固溶してこれを強化
するのに有効な元素群である。
これらのうち、Ａｎ含有量が多すぎるとＴｉ２Ａｌ化合
物が生成して延性を低下させるようになるため、１０％
以下とすることが望ましく、必要に応じて８％以下とす
るのがよい、また、Ｓｎ含有量が多すぎるとＴｉ３Ｓｎ
化合物が生成して延性を低下させるようになるため、１
５％以下とすることが望ましく、さらにＺｒ含有量が多
すぎるとβ相の量が増大してクリープ特性を低下させる
ようになるため、１５％以下とすることが望ましい。さ
らにまた、Ｇａはα相を固溶強化すると共に、Ｔｉ合金
の耐熱性を改善するのに有効な元素であるので、このよ
うな効果を得るために０．０１％以上含有させることも
必要に応じて望ましいが、Ｇａ含有量が多すぎるとＴｉ
３Ｇａ化合物が生成して延性を低下させるようになるた
め、１５％以下とすることが望ましい。
そして、Ａｎ当量として表わされるＡＭ＋（Ｓ ｎ／３
）＋ （Ｚ ｒ／６）の値が１重量％よりも少ないと、
α相の強化が図れなくなる傾向となるので、１重量％以
上とすることがとくに望ましい、しかし、Ａｎ当量で１
０重量％を超えると化合物が生成するようになって靭延
性が低下する傾向となるので、１０重量％以下とするこ
とがとくに望ましい。
ＭｎはＴｉ合金の強度および靭性を改善するのに有効な
元素であるので、これを必須元素として含有させるのが
よいが、０．５重量％未満では強靭化の効果が少なくな
るので、０．５重量％以上とする必要がある。しかし、
３０重量％を超えて含有させるとβ相の安定度が高くな
りすぎてα相の時効析出までに長時間を必要とするよう
になるので、３０重量％以下とする必要がある。
Ｍ ｏ 、 Ｖ 、 Ｎ ｂ 、 Ｔ ａ 、 Ｃｒ
、 Ｗ 、 Ｆ ｅ 。
Ｃｏ、Ｎｉ、Ｃｕはβ相に固溶してこれを強化し、熱処
理性を改善するのに有効であって、短時間強度の改善に
有効な元素群であるので、必要に応じてこれらの１種ま
たは２種以上を添加することも望ましいが、あまり多く
含有させてもβ相の固溶強化にはさほど寄与しなくなる
ので、３０重量％以下とすることが望ましい。
この場合、Ｍｏ＋（Ｖ／１．５）
＋ （Ｎｂ／３．６）＋ （Ｔａ／４．５）＋ （Ｃｒ
ｌｏ 、６４）＋ （Ｗ／２．６）＋ （Ｍｎ１０．６
４）＋ （Ｆｅ１０．３５）＋ （Ｃｏ１０．７）＋
（Ｎｉ１０．９）＋（Ｃｕ／１．３）で表わされるＭＯ
当量での関係においてこの値が５重量％よりも少ないと
β相の強化が図れなくなる傾向となるので、５重量％以
上とすることがとくに望ましい。しかし、ＭＯ当量で３
０重量％を超えるとβ相の安定度が高くなりすぎてα相
の時効析出までに長時間を必要とするようになるので、
３０重量％以下とすることがとくに望ましい、なお、上
記各元素のうちＭ ｏ 、 Ｎ ｂ 、 Ｔ ａはＴｉ
中での拡散速度が遅く、とりわけクリープ特性の改善に
有効であり、また、耐酸化性を改善する効果も大きい。
そのほか、Ｃ，Ｓｉ 、Ｓ、Ｙ、ＲＥＭ（希土類元素の
うちの１種または２種以上）はＴｉ合金中の不純物と介
在物ないしは化合物を形成して、クリープ強度を改善す
るのに有効な元素群であるので、必要に応じてこれらの
１種または２種以上を添加することも可能であるが、含
有量が多すぎると製造性を劣化させ、また延性も低下さ
せるようになるため、添加するとしてもこれらの１種ま
たは２種以上の合計で１重量％以下とすることが望まし
い。
Ｔｉ：残部
Ｔｉは軽量でかつ耐熱性、耐食性に優れ、高比強度が得
られるので残部とした。
本発明に係わる高強度高靭性Ｔｉ合金は、上記した化学
成分よりなるものであり、これを熱処理する際には、前
記Ｔｉ合金を６５０〜１２００℃で熱間鍛伸あるいは熱
間圧延等の熱間加工を行った後、３５０〜６５０℃で直
接時効処理するようになすことが望ましい。
この場合、熱間加工温度が６５０℃よりも低いとＴｉ合
金の変態能が低下し、変形抵抗も増大するため、加工が
困難となり、１２００℃よりも高いと高温加工のため回
復再結晶現象が起こるようになり、加工ひずみが残留し
にくくなるため直接時効材ではその効果がうすれてしま
い、また、結品粒の粗大化が生じると時効処理後の延性
が低下するので、熱間加工温度は６５０〜１２００℃の
範囲とするのがよい。
また、熱間加工に統〈直接時効処理は、Ｔ１合金の高強
度化に有効であるほか、析出α相が均質に分散しやすく
、靭性改善にも有効であることを見いだした。一般にｎ
ｅａｒ β型Ｔｉ合金あるいはβ型Ｔｉ合金のα相の
析出反応は、３５０〜６５０℃の温度域で活発であり、
このような温度範囲内での処理が実用的であって短時間
時効が可能となり、この直接時効処理において、その温
度が３５０℃よりも低いと時効硬化に時間がかかるよう
になるので好ましくなく、６５０℃よりも高くなると過
時効により強度が低下し、熱処理の効果が薄れるので好
ましくなく、したがって、直接時効処理は３５０〜６５
０℃の範囲とするのがよい。
また、上記化学成分のＴｉ合金を熱処理する際には、前
記Ｔｉ合金を６５０〜１２００℃で熱間鍛伸あるいは熱
間圧延等の熱間加工を行った後、６５０〜９５０℃で溶
体化処理を施し、３５０〜６５０℃で時効処理するよう
になすこともできる。
このように、必要に応じて時効処理前に溶体化処理を施
すことも望ましく、熱間加工の際の加工ひずみが不均一
であって時効処理後の機械的性質が場所によって不均一
となることが予想される場合には、時効処理前に溶体化
処理を施すことによってあらかじめ加工ひずみを軽減し
ておくようになすことも有効である。そして、この溶体
化処理は６５０〜９５０℃で行うことが望ましく、６５
０℃未満では合金成分の溶は込みが十分でなく、９５０
℃を超えるとα相が粗大化して靭性が低下し、その結果
割れを生じやすくなるので好ましくない。
（発明の作用）
本発明に係わる高強度高靭性Ｔｉ合金は、上記した構成
を有しているので、Ｔｉ中にＡＭ。
Ｓｎ、Ｚｒ、Ｇａの１種または２種以上を適量添加する
ことによってα相が固溶強化され、Ｍｏ。
Ｖ、Ｎｂ、Ｔａ、Ｃｒ、Ｗ、Ｆｅ、Ｃｏ、Ｎｉ 。
Ｃｕのうちの１種または２種以上を適量含有させること
によってβ相が固溶強化され、熱処理性が改善されて短
時間強度が向上したものとなり、さらに、Ｍｎを適量含
有させることによってβ相が固溶強化されると共に強度
および靭性がさらに改善されたものとなる。
（実施例）
第１表に示す化学成分組成のＴｉ合金をプラズマスカル
炉により溶製し、それぞれについて直径的１００ｍｍの
鋳塊を得たのち、１１００℃で板厚５０ｍｍまで鍛造し
、続いて９５０℃（ただし、比較例Ｎｏ、２５では１０
２５℃）で仕上げ鍛伸加工を行って、３０ ｍ ｍ Ｘ
７０ ｍ ｍ Ｘ ８００ｍｍの板材を製作した。
次いで、同じく第１表に示す条件で一部について溶体化
処理を行ったのち時効処理を施して供試材とした。
続いて、各供試材の０．２％耐力と破壊靭性値を調べて
これを図にあられしたところ、第１図に示す結果となっ
た。なお、破壊靭性値の測定は、鍛伸方向に直角に切込
みを入れた幅２５．４ｍｍのコンパクトテンション試験
片を用いて実施した。
第１表に示すように、本発明実施例合金陥、１〜１４は
いずれも比較例合金崩、２１〜２５に比べて、高強度か
つ高靭性となっていることが認められた。(Means for Solving the Problems) The high-strength, high-toughness Ti alloy according to the present invention contains one or more elements selected from α-strengthening elements A, Sn, Zr, and Ga; β-strengthening elements Mo, V, Nb
, Ta, Cr, W, Fe. One or two selected from Co, Ni, and Cu
It is characterized by having a structure containing 0.5 to 30% by weight of Mn and 0.5 to 30% by weight of Mn, and the remainder being Ti and impurities. %≦AfL+ (S n/3)+ (Z r/6
) 510% by weight Mo, V, Nb, Ta, Cr
, W, Mn, Fe. The Co, Ni, and Cu contents are 5% by weight≦M o + (V/ 1, 5) + (Nb/
3.6)+ (Ta/4.5)+ (Crlo, 64
)+ (W/2.6)+ (Mn10.64)+ (F
e10.35)+ (Co10.7)+ (Ni10.
9)+(Cu/1.3)≦30% by weight The structure of the high-strength, high-toughness Ti alloy described above is a means for solving the above-mentioned conventional problems. It is said that Further, the method for heat treatment of a high strength and high toughness Ti alloy according to the present invention is characterized in that the Ti alloy is hot worked at 650 to 1200°C and then subjected to direct aging treatment at 350 to 650°C. , In addition, after hot working the Ti alloy at 650 to 1200°C, 650 to 950°C
It is characterized by a structure in which solution treatment is carried out at 350 to 650 degrees Celsius, and the structure of the above-described heat treatment method for high-strength, high-toughness Ti alloy is a means for solving the above-mentioned conventional problems. It is said that Next, the reason for limiting the chemical composition of the high-strength, high-toughness Ti alloy according to the present invention will be explained. All, Sn, Zr, and Ga are a group of elements that are effective in solidly dissolving in the α phase and strengthening it. Among these, if the An content is too large, Ti2Al compounds will be generated and the ductility will be reduced, so 10%
It is desirable that the Sn content be 8% or less, if necessary, and if the Sn content is too high, Ti3Sn
1 because compounds are generated and reduce ductility.
It is desirable that the Zr content be 5% or less, and if the Zr content is too high, the amount of β phase will increase and the creep properties will be degraded, so it is desirable that the Zr content be 15% or less. Furthermore, since Ga is an effective element for solid solution strengthening the α phase and improving the heat resistance of Ti alloys, it is necessary to contain 0.01% or more to obtain such effects. However, if the Ga content is too high, Ti
Since 3Ga compounds are generated and reduce ductility, it is desirable that the content be 15% or less. Then, AM+(S n/3
) + (Z r/6) is less than 1% by weight,
Since this tends to make it difficult to strengthen the α phase, it is particularly desirable to set the content to 1% by weight or more.
If it exceeds 0% by weight, compounds tend to form and the toughness and ductility tends to decrease, so it is particularly desirable to keep the content to 10% by weight or less. Mn is an effective element for improving the strength and toughness of Ti alloys, so it is better to include it as an essential element, but if it is less than 0.5% by weight, the toughening effect will be reduced, so if it is less than 0.5% by weight, the toughening effect will be reduced. It needs to be 5% by weight or more. but,
If the content exceeds 30% by weight, the stability of the β phase becomes too high and a long time is required for the aging precipitation of the α phase, so it is necessary to limit the content to 30% by weight or less. Mo, V, Nb, Ta, Cr
, W, F e. Co, Ni, and Cu are effective in solid-dissolving in the β phase to strengthen it and improve heat treatability, and are effective in improving short-term strength, so these elements may be added as necessary. It is also desirable to add one or more kinds, but if too much is added, it will not contribute much to the solid solution strengthening of the β phase, so it is desirable to add 30% by weight or less. In this case, Mo+(V/1.5) + (Nb/3.6)+ (Ta/4.5)+ (Cr
lo, 64) + (W/2.6) + (Mn10.6
4)+ (Fe10.35)+ (Co10.7)+
MO expressed as (Ni10.9) + (Cu/1.3)
In terms of equivalent weight, if this value is less than 5% by weight, it tends to be difficult to strengthen the β phase, so it is particularly desirable to set it to 5% by weight or more. However, the MO equivalent is 3
If it exceeds 0% by weight, the stability of the β phase will become too high and it will take a long time for the aging precipitation of the α phase.
It is particularly desirable that the content be 30% by weight or less. Among the above elements, Mo, Nb, and Ta are Ti
It has a slow diffusion rate and is particularly effective in improving creep characteristics, and is also highly effective in improving oxidation resistance. In addition, C, Si, S, Y, and REM (one or more rare earth elements) are effective elements that form inclusions or compounds with impurities in Ti alloys and improve creep strength. It is possible to add one or more of these as needed, but if the content is too large, it will deteriorate manufacturability and also reduce ductility. Even if it does, it is desirable that the total amount of one or more of these is 1% by weight or less. Ti: Remainder Ti is lightweight, has excellent heat resistance and corrosion resistance, and provides high specific strength, so it was designated as the remainder. The high-strength, high-toughness Ti alloy according to the present invention is composed of the above-mentioned chemical components, and when heat-treating it, the Ti alloy is heated by hot forging or hot rolling at 650 to 1200°C. After the temporary working, it is desirable to directly age the material at 350 to 650°C. In this case, if the hot working temperature is lower than 650°C, the transformation ability of the Ti alloy will decrease and the deformation resistance will increase, making processing difficult. If the hot working temperature is higher than 1200°C, the recovery recrystallization phenomenon will occur due to high temperature processing. The effect of directly aged material is lost because it becomes difficult for working strain to remain, and if the grains become coarser, the ductility after aging decreases, so the hot working temperature is The temperature is preferably in the range of 650 to 1200°C. In addition, it has been found that direct aging treatment combined with hot working is effective for increasing the strength of the T1 alloy, as well as for easily dispersing the precipitated α phase homogeneously, which is also effective for improving toughness. Generally n
The precipitation reaction of the α phase of the ear β-type Ti alloy or β-type Ti alloy is active in the temperature range of 350 to 650°C,
Treatment within such a temperature range is practical and allows short-time aging, but in this direct aging treatment, if the temperature is lower than 350°C, age hardening will take a long time, which is not preferable. If the temperature is higher than 650°C, the strength will decrease due to over-aging and the effect of heat treatment will be weakened, which is undesirable.
It is preferable to set it in the range of 0°C. In addition, when heat treating a Ti alloy having the above chemical composition, the Ti alloy is subjected to hot working such as hot forging or hot rolling at 650 to 1200°C, and then solution treatment is performed at 650 to 950°C. It is also possible to perform an aging treatment at 350 to 650°C. In this way, it is also desirable to perform solution treatment before aging treatment if necessary, since the processing strain during hot working is non-uniform and the mechanical properties after aging treatment will be non-uniform depending on the location. If this is expected, it is also effective to reduce processing strain in advance by performing solution treatment before aging treatment. This solution treatment is preferably carried out at 650 to 950°C, and 650 to 950°C.
At temperatures below 0°C, the alloy components are not sufficiently penetrated, resulting in
If the temperature exceeds .degree. C., the alpha phase becomes coarse, the toughness decreases, and as a result, cracks are likely to occur, which is not preferable. (Function of the Invention) The high-strength, high-toughness Ti alloy according to the present invention has the above-described structure, so that Ti contains AM. By adding appropriate amounts of one or more of Sn, Zr, and Ga, the α phase is solid solution strengthened, and Mo. V, Nb, Ta, Cr, W, Fe, Co, Ni. By containing an appropriate amount of one or more of Cu, the β phase is solid solution strengthened, heat treatability is improved, and short-term strength is improved.Furthermore, by containing an appropriate amount of Mn, the β phase is strengthened. is strengthened by solid solution, and the strength and toughness are further improved. (Example) Ti alloys having the chemical composition shown in Table 1 were melted in a plasma skull furnace to obtain ingots with a diameter of 100 mm, and then forged at 1100°C to a plate thickness of 50 mm, followed by 950°C. °C (However, in Comparative Example No. 25, 10
Finish forging and stretching at 25°C) to a diameter of 30 mm
A board measuring 70 mm x 800 mm was manufactured. Next, part of the sample was subjected to solution treatment under the same conditions shown in Table 1, and then subjected to aging treatment to obtain a test material. Subsequently, the 0.2% proof stress and fracture toughness values of each sample material were investigated and plotted in a diagram, resulting in the results shown in Figure 1. Note that the fracture toughness value was measured using a compact tension test piece with a width of 25.4 mm in which cuts were made at right angles to the forging and elongation direction. As shown in Table 1, it was observed that all of the alloys according to the present invention, Nos. 1 to 14, had higher strength and toughness than the comparative alloys Nos. 21 to 25.
本発明に係わるＴｉ合金は、α強化元素であるＡ！；Ｌ
、Ｓｎ、Ｚｒ、Ｇａ（７）うちから選ばれる１種または
２種以上の元素と、β強化元素であるＭｏ、Ｖ、Ｎｂ、
Ｔａ、Ｃｒ、Ｗ、Ｆｅ、Ｃｏ。
Ｎｉ、Ｃｕのうちから選ばれる１種または２種以上の元
素と、０．５〜３０重量％のＭｎを含み、残部Ｔｉおよ
び不純物よりなる構成としたものであるから、従来の高
比強度のＴｉ合金において、その強度および靭性をより
一層向上させることが可能であり、従来以上に高強度高
靭性をそなえたＴｉ合金部材を提供することが可能であ
り、本発明に係わる高強度高靭性Ｔｉ合金の熱処理方法
によってＴｉ合金の高強度高靭性化を実現することが可
能になるという著しく優れた効果がもたらされる。The Ti alloy according to the present invention has an α-strengthening element A! ;L
, Sn, Zr, Ga (7) and one or more elements selected from among them, and β-strengthening elements Mo, V, Nb,
Ta, Cr, W, Fe, Co. Since it contains one or more elements selected from Ni and Cu, and 0.5 to 30% by weight of Mn, with the remainder being Ti and impurities, it has a high specific strength compared to the conventional one. It is possible to further improve the strength and toughness of a Ti alloy, and it is possible to provide a Ti alloy member with higher strength and toughness than ever before, and the high strength and high toughness Ti alloy member according to the present invention The heat treatment method for the alloy brings about the remarkable effect that it becomes possible to realize high strength and high toughness of the Ti alloy.
第１図は本発明に係わる高強度高靭性Ｔｉ合金の実施例
を比較例と共に示すグラフである。FIG. 1 is a graph showing examples of high-strength, high-toughness Ti alloys according to the present invention together with comparative examples.
Claims (4)
から選ばれる１種または２種以上の元素と、β強化元素
であるＭｏ、Ｖ、Ｎｂ、Ｔａ、Ｃｒ、Ｗ、Ｆｅ、Ｃｏ、
Ｎｉ、Ｃｕのうちから選ばれる１種または２種以上の元
素と、０．５〜３０重量％のＭｎを含み、残部Ｔｉおよ
び不純物よりなることを特徴とする高強度高靭性Ｔｉ合
金。(1) One or more elements selected from among α-strengthening elements Al, Sn, Zr, and Ga and β-strengthening elements Mo, V, Nb, Ta, Cr, W, Fe, and Co. ,
A high-strength, high-toughness Ti alloy comprising one or more elements selected from Ni and Cu, and 0.5 to 30% by weight of Mn, with the remainder being Ti and impurities.
％ Ｍｏ、Ｖ、Ｎｂ、Ｔａ、Ｃｒ、Ｗ、Ｍｎ、Ｆｅ、Ｃｏ、
Ｎｉ、Ｃｕ含有量が、 ５重量％≦Ｍｏ＋（Ｖ／１．５） ＋（Ｎｂ／３．６）＋（Ｔａ／４．） ＋（Ｃｒ／０．６４）＋（Ｗ／２．６） ＋（Ｍｎ／０．６４）＋（Ｆｅ／０．３５）＋（Ｃｏ／
０．７）＋（Ｎｉ／０．９） ＋（Ｃｕ／１．３）≦３０重量％ の関係を満足する請求項第１項に記載の高強度高靭性Ｔ
ｉ合金。(2) Al, Sn, Zr content is 1% by weight≦Al+(Sn/3)+(Zr/6≦10% by weight Mo, V, Nb, Ta, Cr, W, Mn, Fe, Co,
Ni, Cu content is 5% by weight≦Mo+(V/1.5) +(Nb/3.6)+(Ta/4.)+(Cr/0.64)+(W/2.6) +(Mn/0.64)+(Fe/0.35)+(Co/
0.7) + (Ni/0.9) + (Cu/1.3)≦30% by weight.
i-alloy.
５０〜１２００℃で熱間加工した後、３５０〜６５０℃
で直接時効処理することを特徴とする高強度高靭性Ｔｉ
合金の熱処理方法。(3) The Ti alloy according to claim 1 or 2 is
After hot working at 50-1200℃, 350-650℃
High-strength, high-toughness Ti characterized by direct aging treatment with
Alloy heat treatment method.
５０〜１２００℃で熱間加工した後、６５０〜９５０℃
で溶体化処理を施し、３５０〜６５０℃で時効処理する
ことを特徴とする高強度高靭性Ｔｉ合金の熱処理方法。(4) The Ti alloy according to claim 1 or 2 is
After hot working at 50-1200℃, 650-950℃
A method for heat treating a high-strength, high-toughness Ti alloy, the method comprising solution treatment at a temperature of 350 to 650°C and aging treatment at a temperature of 350 to 650°C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17596390A JPH0463239A (en) | 1990-07-03 | 1990-07-03 | High strength and high toughness ti alloy and method for heat treating it |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17596390A JPH0463239A (en) | 1990-07-03 | 1990-07-03 | High strength and high toughness ti alloy and method for heat treating it |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0463239A true JPH0463239A (en) | 1992-02-28 |
Family
ID=16005320
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP17596390A Pending JPH0463239A (en) | 1990-07-03 | 1990-07-03 | High strength and high toughness ti alloy and method for heat treating it |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0463239A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2005105388A (en) * | 2003-10-01 | 2005-04-21 | Furukawa Techno Material Co Ltd | Method of producing superelastic titanium alloy for living body, and titanium alloy for superelasticity |
| CN104060125A (en) * | 2014-07-07 | 2014-09-24 | 林娟娟 | Heat treatment method of engine blade |
| JP2015025167A (en) * | 2013-07-25 | 2015-02-05 | 大同特殊鋼株式会社 | β TYPE TITANIUM ALLOY |
| CN105457583A (en) * | 2015-12-10 | 2016-04-06 | 攀枝花市九鼎智远知识产权运营有限公司 | Ammonium chloride neutralization reaction kettle |
-
1990
- 1990-07-03 JP JP17596390A patent/JPH0463239A/en active Pending
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2005105388A (en) * | 2003-10-01 | 2005-04-21 | Furukawa Techno Material Co Ltd | Method of producing superelastic titanium alloy for living body, and titanium alloy for superelasticity |
| JP2015025167A (en) * | 2013-07-25 | 2015-02-05 | 大同特殊鋼株式会社 | β TYPE TITANIUM ALLOY |
| CN104060125A (en) * | 2014-07-07 | 2014-09-24 | 林娟娟 | Heat treatment method of engine blade |
| CN105457583A (en) * | 2015-12-10 | 2016-04-06 | 攀枝花市九鼎智远知识产权运营有限公司 | Ammonium chloride neutralization reaction kettle |
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