JPH08157987A - High strength and high ductility titanium alloy - Google Patents
High strength and high ductility titanium alloyInfo
- Publication number
- JPH08157987A JPH08157987A JP29512894A JP29512894A JPH08157987A JP H08157987 A JPH08157987 A JP H08157987A JP 29512894 A JP29512894 A JP 29512894A JP 29512894 A JP29512894 A JP 29512894A JP H08157987 A JPH08157987 A JP H08157987A
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- Japan
- Prior art keywords
- alloy
- strength
- ductility
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- present
- 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.)
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Links
- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 36
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 13
- 229910052742 iron Inorganic materials 0.000 claims abstract description 11
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 11
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 10
- 229910052782 aluminium Inorganic materials 0.000 abstract description 7
- 238000000137 annealing Methods 0.000 abstract description 6
- 238000010438 heat treatment Methods 0.000 abstract description 2
- 239000000956 alloy Substances 0.000 description 25
- 229910045601 alloy Inorganic materials 0.000 description 23
- 230000000694 effects Effects 0.000 description 11
- 239000000243 solution Substances 0.000 description 8
- 238000009864 tensile test Methods 0.000 description 8
- 238000000034 method Methods 0.000 description 7
- 230000009466 transformation Effects 0.000 description 7
- 238000012545 processing Methods 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- 229910000883 Ti6Al4V Inorganic materials 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 238000012937 correction Methods 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- 230000032683 aging Effects 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 238000011160 research Methods 0.000 description 3
- 230000000087 stabilizing effect Effects 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 238000002360 preparation method Methods 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910000756 V alloy Inorganic materials 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000003889 chemical engineering Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 239000013077 target material Substances 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
Landscapes
- Forging (AREA)
- Powder Metallurgy (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、航空機をはじめ化学工
学機械や深海調査船等、様々な用途で適用されているＴ
ｉ合金に関するものであり、特にアルミニウムと共に窒
素または炭素を添加することによってＴｉ−６Ａｌ−４
Ｖ合金を改良し、高強度と高延性を達成したＴｉ合金に
関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention is applicable to various applications such as aircraft, chemical engineering machines and deep sea research vessels.
i-alloy, especially Ti-6Al-4 by adding nitrogen or carbon with aluminum.
The present invention relates to a Ti alloy obtained by improving V alloy and achieving high strength and high ductility.
【０００２】[0002]
【従来の技術】近年、航空機等の更なる軽量化が望まれ
ており、それに伴って、高強度で高延性のα＋β型Ｔｉ
合金、特にＴｉ−６Ａｌ−４Ｖ合金への要求が高まって
いる。しかしながら、Ｔｉ−６Ａｌ−４Ｖ合金では、焼
鈍処理で得られる引張強さはせいぜい１．１ＧＰａが限
度である。一方、Ｔｉ合金の高強度化を達成するには、
α＋β２相高温域の溶体化を含む溶体化時効処理または
溶体化過時効処理が行われるのが一般的であるが、同処
理を行なうと、処理後のＴｉ合金材料に反り等が発生
し、矯正加工が必要になるという欠点がある。2. Description of the Related Art In recent years, further weight reduction of aircraft and the like has been demanded, and along with this, α + β type Ti which has high strength and high ductility.
There is an increasing demand for alloys, especially Ti-6Al-4V alloys. However, in the Ti-6Al-4V alloy, the tensile strength obtained by the annealing treatment is limited to 1.1 GPa at most. On the other hand, in order to achieve high strength of Ti alloy,
In general, solution aging treatment or solution overaging treatment including solution treatment in the α + β2 phase high temperature region is performed. However, if the treatment is performed, the Ti alloy material after the treatment may be warped and straightened. There is a disadvantage that processing is required.
【０００３】上記の様な反り等の発生を低減するという
観点から、例えば特開平５−５９５１０号の様な技術も
提案されている。この技術は、所定の化学成分を有する
α＋β型Ｔｉ合金素材を、（β変態点−１５０℃）〜β
変態点未満の範囲内の温度に加熱し、次いで、０．５〜
１０℃／ｓｅｃの範囲の冷却速度で冷却して、素材に溶
体化処理を施し、このように溶体化処理を施した前記素
材に、４００〜６００℃の範囲の温度で時効処理を施す
ものである。しかしながらこの技術では、反り等の発生
が低減されるとは言うものの、溶体化処理および時効処
理の２段階のステップを必要とし、工程が複雑になると
いう問題がある。[0003] From the viewpoint of reducing the occurrence of the above-mentioned warpage or the like, a technique as disclosed in Japanese Patent Laid-Open No. 5-59510 has been proposed. This technology converts an α + β-type Ti alloy material having a predetermined chemical component into (β transformation point −150 ° C.) to β
Heat to a temperature in the range below the transformation point, then 0.5 to
The material is subjected to a solution treatment by cooling at a cooling rate in a range of 10 ° C./sec, and the material subjected to the solution treatment is subjected to an aging treatment at a temperature in a range of 400 to 600 ° C. is there. However, with this technique, the occurrence of warpage and the like is reduced, but there is a problem that the process is complicated because it requires two steps of solution treatment and aging treatment.
【０００４】また引張り強さが１．１ＧＰａを超えるＴ
ｉ合金としては、ｎｅａｒβ系のα＋β型Ｔｉ合金やβ
型Ｔｉ合金が考えられるが、本発明者らが調査したとこ
ろ、従来のｎｅａｒβ系α＋β型Ｔｉ合金やβ型Ｔｉ合
金では、高速変形下での延性に劣ることがわかった。尚
高速変形下での延性に関し、本発明者らが検討したとこ
ろによると、Ｔｉ合金のＭｏ当量（Ｍｏ当量＝Ｍｏ＋
０．６７Ｖ＋２．９Ｆｅ＋１．６Ｃｒ＋０．２８Ｎｂ＋
０．２２Ｔａ）が４．０以下で高速変形下での延性に優
れることがわかった。In addition, T having a tensile strength exceeding 1.1 GPa
As the i alloy, a near β type α + β type Ti alloy or β
Although a type Ti alloy is conceivable, the present inventors have investigated and found that the conventional near β-based α + β type Ti alloy and β type Ti alloy are inferior in ductility under high-speed deformation. According to a study conducted by the present inventors regarding ductility under high-speed deformation, the Mo equivalent of the Ti alloy (Mo equivalent = Mo +
0.67V + 2.9Fe + 1.6Cr + 0.28Nb +
It was found that 0.22 Ta) was 4.0 or less and the ductility under high-speed deformation was excellent.
【０００５】一方、特開平６−１０８１８７号には、高
強度で高延性のＴｉ合金を開発するという観点から、比
較的多めのＮ（０．０６〜０．２０％）を含有すると共
に、１％以上のＭｏを必須成分として含有する「窒素添
加高強度Ｔｉ合金」について開示されている。しかしな
がらこの合金には、Ｍｏを添加することによって、Ｍｏ
当量が４．０以上を有し、高速変形下での延性に劣ると
いう欠点がある。On the other hand, from the viewpoint of developing a high-strength and high-ductility Ti alloy, Japanese Patent Application Laid-Open No. 6-108187 discloses that a relatively large amount of N (0.06 to 0.20%) A "nitrogen-added high-strength Ti alloy" containing at least Mo as an essential component is disclosed. However, by adding Mo to this alloy, Mo is added.
There is a drawback that the equivalent weight is 4.0 or more and the ductility under high-speed deformation is poor.
【０００６】[0006]
【発明が解決しようとする課題】本発明はこうした技術
的背景の下になされたものであって、その目的は、溶体
化処理を施さずとも焼鈍処理だけで高強度が得られ、し
かも高延性を達成することのできるＴｉ合金を提供する
ことにある。SUMMARY OF THE INVENTION The present invention has been made under such a technical background. It is an object of the present invention to obtain high strength by only annealing treatment without performing solution treatment, and to obtain high ductility. To provide a Ti alloy capable of achieving the following.
【０００７】[0007]
【課題を解決するための手段】上記目的を達成すること
のできた本発明のＴｉ合金は、Ａｌ：６．７５超〜８．
００％，Ｖ：３．５〜４．５％，Ｆｅ：０．２５〜０．
３５％，Ｏ：０．１５〜０．２５％，Ｃ：０．１０％以
下，Ｎ：０．１５％以下を夫々含有し、残部がＴｉおよ
び不可避不純物からなる点に要旨を有するものである。Means for Solving the Problems The Ti alloy of the present invention, which has achieved the above object, has an Al content of more than 6.75 to 8.
00%, V: 3.5-4.5%, Fe: 0.25-0.
It contains 35%, O: 0.15 to 0.25%, C: 0.10% or less, and N: 0.15% or less, and has a gist in that the balance consists of Ti and unavoidable impurities. .
【０００８】また上記の合金において、Ｎの好ましい含
有量は０．０３〜０．１５％であり、この範囲ではＮに
よる作用が最大限に発揮される。In the above alloy, the preferable content of N is 0.03 to 0.15%, and the effect of N is maximized in this range.
【０００９】更に、Ａｌ：６．７５超〜８．００％，
Ｖ：３．５〜４．５％，Ｆｅ：０．２５〜０．３５％，
Ｏ：０．１５〜０．２５％，Ｃ：０．１０超〜０．２０
％，Ｎ：０．０３％以下を夫々含有し、残部がＴｉおよ
び不可避不純物からなるＴｉ合金によっても本発明の目
的が達成される。Further, Al: more than 6.75 to 8.00%,
V: 3.5-4.5%, Fe: 0.25-0.35%,
O: 0.15 to 0.25%, C: more than 0.10 to 0.20
% And N: 0.03% or less, respectively, and the balance of Ti and the unavoidable impurities also achieves the object of the present invention.
【００１０】[0010]
【作用】上記Ｔｉ−６Ａｌ−４Ｖ合金中のＯ，Ｃ，Ｎ，
Ｆｅ等の元素については、米国において不純物としてそ
の上限が規格化されており（ＡＭＳ ４９２８Ｌ）、夫
々Ｏ：０．２０％以下，Ｃ：０．１０％以下，Ｎ：０．
０５％以下，Ｆｅ：０．３０％以下とされている。しか
しながら、本発明者らが検討したところ、上記規格通り
に含有させても必ずしも希望する特性が得られるとは限
らないことがわかった。そこで本発明者らは、前記Ｔｉ
−６Ａｌ−４Ｖ系合金の特性を改善して高強度且つ高延
性を達成するという観点から、Ａｌ，Ｏ，Ｃ，Ｎ，Ｆｅ
等の元素の最適な含有量について更に検討を重ねた。In the above Ti-6Al-4V alloy, O, C, N,
The upper limit of elements such as Fe is standardized as impurities in the United States (AMS 4928L). O: 0.20% or less, C: 0.10% or less, N: 0.
It is set to not more than 05% and Fe: 0.30% or less. However, the present inventors have studied and found that even if they are contained according to the above-mentioned standard, desired characteristics are not always obtained. Therefore, the present inventors
From the viewpoint of improving the properties of -6Al-4V alloy to achieve high strength and high ductility, Al, O, C, N, Fe
Further studies were conducted on the optimum content of elements such as.
【００１１】従来Ｔｉ合金にＮを添加すると、強度は上
がるが延性が著しく劣化すると言われてきた。例えば、
特公平５−７２４５２号には、純ＴｉにＮを添加するこ
とによって、強度は上昇するが延性が劣化することが報
告されている。しかしながら、本発明者らが詳細に検討
したところによると、Ａｌ，Ｏ，ＣおよびＦｅをバラン
ス良く添加すれば、図１に示す様にＮを０．１５％以下
（好ましくは、０．０３〜０．１５％）添加することに
よって、高強度且つ高延性が達成されることを見いだ
し、本発明を完成した。またＣに関しても、Ａｌ，Ｏ，
ＮおよびＦｅをバランス良く添加すれば、図２に示す様
にＣを０．１０超〜０．２０％添加することによって、
高強度且つ高延性が達成されることを見いだした。即
ち、本発明のＴｉ合金は、α安定化元素であるＡｌを多
量に添加すると共に、ＯおよびＮまたはＣを添加し、更
にβ安定化元素であるＦｅをバランス良く添加したもの
である。まず本発明のＴｉ合金における化学成分限定理
由は、下記の通りである。It has been conventionally said that when N is added to a Ti alloy, the strength is increased but the ductility is remarkably deteriorated. For example,
Japanese Patent Publication No. 5-72452 reports that the addition of N to pure Ti increases the strength but deteriorates the ductility. However, the present inventors have studied in detail that, when Al, O, C and Fe are added in a well-balanced manner, N is 0.15% or less as shown in FIG. 0.15%), it was found that high strength and high ductility were achieved, and the present invention was completed. As for C, Al, O,
If N and Fe are added in a well-balanced manner, as shown in FIG. 2, by adding C in excess of 0.10 to 0.20%,
It has been found that high strength and high ductility are achieved. That is, the Ti alloy of the present invention is obtained by adding a large amount of Al as an α-stabilizing element, adding O, N or C, and further adding Fe as a β-stabilizing element in a well-balanced manner. First, the reasons for limiting the chemical components in the Ti alloy of the present invention are as follows.
【００１２】Ａｌ：６．７５超〜８．００％ Ａｌは、固溶型α安定化元素であり、ＡｌをＴｉに添加
すると、β変態点は上がり、６％の添加によって約１０
０℃上昇する。このようにＡｌはＴｉ合金の低温相であ
るα相を安定化し、主としてα相中に固溶してα相を強
化するし、Ｔｉ合金の強度を上げるのに有効な合金元素
である。通常Ａｌを６％よりも多く添加すると、熱処理
条件によってα2 相（Ｔｉ3 Ａｌ相）という規則相を生
じ、脆化の原因になると言われている。しかしながら、
本発明ではβ安定化元素として、Ｖに加えＦｅを所定量
添加することによって、Ａｌを６．７５％よりも多く添
加したＴｉ合金においても、靭性を確保したまま強度向
上が達成されたのである。但し、Ａｌの含有量が８．０
０％を超えると、延性および靭性が著しく劣化し、目標
とする材料特性を得ることができなくなるので、その含
有量は８．００％以下とする必要がある。Al: more than 6.75 to 8.00% Al is a solid solution type α stabilizing element. When Al is added to Ti, the β transformation point rises, and when 6% is added, it becomes about 10%.
Increase by 0 ° C. As described above, Al is an effective alloying element for stabilizing the α phase, which is a low-temperature phase of the Ti alloy, mainly for solid solution in the α phase to strengthen the α phase, and to increase the strength of the Ti alloy. Usually, when Al is added in an amount of more than 6%, it is said that an ordered phase called an α 2 phase (Ti 3 Al phase) is generated depending on the heat treatment conditions, which causes embrittlement. However,
In the present invention, by adding a predetermined amount of Fe in addition to V as a β-stabilizing element, even in a Ti alloy to which more than 6.75% of Al is added, improvement in strength is achieved while maintaining toughness. . However, the content of Al is 8.0.
If it exceeds 0%, the ductility and toughness are significantly deteriorated and the target material properties cannot be obtained. Therefore, the content must be 8.00% or less.
【００１３】Ｖ：３．５〜４．５％ Ｖは、全率固溶型のβ安定化元素であり、Ｖの添加によ
ってβ変態点が下がり、ほぼ４％の添加によって、室温
でβ相が安定なα＋β型合金となる。このようにＶは、
高温相のβ相を安定化し、塑性加工が容易なβ相を存在
させて、熱間加工性を良くする効果を有する。この様な
効果は、その含有量が３．５％から発揮されるが、４．
５％を超えると、却って延性を劣化させる。V: 3.5-4.5% V is a β-stabilizing element in the form of a complete solid solution. The addition of V lowers the β transformation point. Is a stable α + β type alloy. Thus, V is
This has the effect of stabilizing the β phase of the high temperature phase and allowing the β phase that is easily plastically worked to exist to improve the hot workability. Such an effect is exhibited when the content is 3.5%,
If it exceeds 5%, the ductility is rather deteriorated.
【００１４】Ｆｅ：０．２５〜０．３５％ Ｆｅは、β共析型のβ安定化元素であり、Ｖと同様にβ
変態点を低下させてβ相領域を広げる効果を有する。ま
た微量の添加によって、強度を向上させることができ
る。このような効果を発揮させるためには、０．２５％
以上添加する必要があるが、０．３５％を超えると、延
性が著しく劣化する。Fe: 0.25 to 0.35% Fe is a β-eutectoid type β-stabilizing element.
It has the effect of lowering the transformation point and widening the β phase region. Also, the strength can be improved by adding a small amount. 0.25%
It is necessary to add the above, but if it exceeds 0.35%, the ductility is remarkably deteriorated.
【００１５】Ｏ：０．１５〜０．２５％ Ｏは、その含有量を調節することによって、所定の強度
レベルを得ることができる。Ｏは侵入型のα安定化元素
で、β変態点を上げるが、微量の添加によって強度向上
に寄与する効果を発揮する。このような効果を発揮させ
るためには、０．１５％以上添加する必要があるが、
０．２５％を超えると、延性が劣化する。O: 0.15 to 0.25% O can obtain a predetermined strength level by adjusting its content. O is an interstitial α-stabilizing element which raises the β transformation point, but exerts an effect of improving the strength by adding a small amount. In order to exert such effects, it is necessary to add 0.15% or more,
If it exceeds 0.25%, ductility deteriorates.
【００１６】Ｃ：０．１０％以下または０．１０超〜
０．２０％ Ｃは、侵入固溶型の元素であり、微量の添加によって強
度向上に寄与することができる。しかしながら、Ｎの添
加量が０．１５％以下（特に、０．０３〜０．１５％）
のときは、Ｃの過剰添加は延性を著しく劣化させるの
で、０．１０％以下とすべきである。尚Ｎの添加量を
０．０３％以下に制限したときには、Ｃの添加量を０．
１０超〜０．２０％とすることによって、却って高強度
且つ高延性を得ることができ、このときはＣの添加量が
０．２０％を超えると延性が劣化することになる。C: 0.10% or less or more than 0.10%
0.20% C is an element of an interstitial solid solution type, and can contribute to improvement in strength by adding a small amount. However, the addition amount of N is 0.15% or less (particularly, 0.03 to 0.15%).
In this case, the excessive addition of C significantly deteriorates the ductility, so the content should be 0.10% or less. When the amount of N added was limited to 0.03% or less, the amount of C added was set to 0.
By setting the content to more than 10 to 0.20%, high strength and high ductility can be obtained, and in this case, if the added amount of C exceeds 0.20%, the ductility is deteriorated.
【００１７】Ｎ：０．１５％以下 Ｎは侵入固溶型のα安定化元素であり、微量の添加によ
ってβ変態点が上がり、また強度向上に寄与することが
できる。しかしながら、Ｎの含有量が０．１５％を超え
ると、延性が低下する。またＮによる上記効果を有効に
発揮させるという観点からすれば、Ｃの添加量が０．１
０％以下のときは、Ｎは０．０３％以上添加することが
好ましく、より好ましくは０．０６％以上添加するのが
良い。尚Ｃの添加量を０．１０超〜０．２０％としたと
きには、上記の如くＮの添加量を０．０３％以下に制限
する必要があり、これによって高強度且つ高延性を得る
ことができる。N: 0.15% or less N is an interstitial solid solution type α-stabilizing element, and can be added to a small amount to increase the β transformation point and contribute to improvement in strength. However, if the N content exceeds 0.15%, the ductility decreases. From the viewpoint of effectively exerting the above effect of N, the addition amount of C is 0.1
When it is 0% or less, N is preferably added at 0.03% or more, more preferably 0.06% or more. When the addition amount of C is more than 0.10 to 0.20%, it is necessary to limit the addition amount of N to 0.03% or less as described above, thereby obtaining high strength and high ductility. it can.
【００１８】純Ｔｉにおいては、Ｎ添加は同量のＯと比
較して、同程度かそれ以上に強度を向上させる作用があ
ることが報告されているが（例えば、「W.L.Finday and
J.A.Snyder:Trans.AIME.188 Feb(1950),p277」 や「R.I.J
affee, H.B.Ogden and D.J.Maykuth: Trans. AIME. 188
Oct (1950), p1261」 等）、本発明はこの様なＮの作用
をＴｉ合金に応用したものである。また前記特開平６−
１０８１８７号に開示されたＴｉ合金は、ＡＭＳ規格値
よりも多めのＮを含有させてＮの添加効果を発揮させる
趣旨の下でなされたものといえるが、前述の如くこの合
金はＭｏを必須成分として含むものであり、しかもＭｏ
当量が４．０以上であり、高速変形下での延性に劣ると
いう欠点を有するものである。In pure Ti, it has been reported that the addition of N has an effect of improving the strength to the same degree or more as compared with the same amount of O (for example, "WLFinday and
JASnyder: Trans.AIME.188 Feb (1950), p277 '' and `` RIJ
affee, HBOgden and DJMaykuth: Trans.AIME. 188
Oct (1950), p1261 "etc.), the present invention applies such an action of N to a Ti alloy. Further, the above-mentioned JP-A-6-
The Ti alloy disclosed in Japanese Patent No. 108187 can be said to have been made under the intent of containing N more than the AMS standard value and exerting the effect of adding N. As described above, this alloy contains Mo as an essential component. And Mo
It has a drawback that the equivalent weight is 4.0 or more and the ductility under high-speed deformation is poor.
【００１９】以下本発明を実施例によって更に詳細に説
明するが、下記実施例は本発明を限定する性質のもので
はなく、前・後記の趣旨に徴して設計変更することはい
ずれも本発明の技術的範囲に含まれるものである。The present invention will be described in more detail with reference to the following examples, but the following examples are not intended to limit the present invention, and any modification of the design of the present invention can be made without departing from the spirit of the preceding and following paragraphs. It is included in the technical scope.
【００２０】[0020]
【実施例】下記表１に示す化学成分組成を有するインゴ
ットをβ領域で鍛造し、鍛造組織を完全に破壊した後、
９００℃以上のα＋β領域の温度で十分な加工を施し
た。加工後は、７０５℃で焼鈍した後、室温にて引張試
験を行ない、各機械的性質（引張強さ、０．２％耐力、
伸び、絞り）を測定した。このとき、引張試験片の作成
および引張試験の実施は、ＡＳＴＭ Ｅ８に準処して行
なった。引張試験結果を、下記表２に示す。EXAMPLE An ingot having the chemical composition shown in Table 1 below was forged in the β region and the forged structure was completely destroyed.
Sufficient processing was performed at a temperature in the α + β region of 900 ° C. or more. After processing, after annealing at 705 ° C., a tensile test is performed at room temperature, and each mechanical property (tensile strength, 0.2% proof stress,
Elongation, drawing) were measured. At this time, the preparation of the tensile test piece and the execution of the tensile test were performed according to ASTM E8. The results of the tensile test are shown in Table 2 below.
【００２１】[0021]
【表１】 [Table 1]
【００２２】[0022]
【表２】 [Table 2]
【００２３】これらの結果から、次の様に考察できる。
まず合金Ｎｏ．１は、ＡＭＳ規格で作製したＴｉ−６Ａ
ｌ−４Ｖ合金であるが、焼鈍処理だけでは引張強さは
１．１ＧＰａを超えなかった。また合金Ｎｏ．２も、Ａ
ＭＳ規格で作製したＴｉ−６Ａｌ−４Ｖ合金であり、こ
の合金は合金Ｎｏ．１に比べ、Ａｌ，Ｆｅ，Ｏを規格限
界値に近い量まで添加したものであるが、引張強さで
１．１ＧＰａを超えることはなかった。From these results, the following can be considered.
First, alloy No. 1 is Ti-6A manufactured according to AMS standard
Although it is a 1-4V alloy, the tensile strength did not exceed 1.1 GPa only by annealing. Alloy No. 2 also A
This is a Ti-6Al-4V alloy manufactured according to the MS standard. Compared with No. 1, Al, Fe, and O were added to an amount close to the specification limit value, but the tensile strength did not exceed 1.1 GPa.
【００２４】合金Ｎｏ．８は、本発明で規定する範囲よ
りもＮ含有量を多くして作製したＴｉ合金（比較例）で
あるが、引張強さは大きくなったものの、延性（伸びお
よび絞り）が著しく劣化していた。合金Ｎｏ．９は、本
発明で規定する範囲よりもＦｅ含有量を少なくして作製
したＴｉ合金（比較例）であるが、この合金では延性
（伸びおよび絞り）は良好であるものの、引張強さが
１．１ＧＰａを下回っていた。合金Ｎｏ．１０は、本発
明で規定する範囲よりもＡｌ含有量を多くして作製した
Ｔｉ合金（比較例）であるが、伸びがＴｉ−６Ａｌ−４
Ｖの規格値である１０％を下回っていた。Alloy No. 8 is a Ti alloy (Comparative Example) produced with a higher N content than the range specified in the present invention, but the tensile strength was increased, but the ductility (elongation and drawing) was significantly deteriorated. Was. Alloy No. Reference numeral 9 denotes a Ti alloy (Comparative Example) produced with a Fe content lower than the range specified in the present invention. In this alloy, although the ductility (elongation and reduction) is good, the tensile strength is 1%. .1 GPa. Alloy No. 10 is a Ti alloy (Comparative Example) produced by increasing the Al content beyond the range specified in the present invention, but having an elongation of Ti-6Al-4.
V was below the standard value of 10%.
【００２５】これらに対し、合金Ｎｏ．３〜７のもの
は、本発明で規定する要件を満足する実施例であり、い
ずれも引張強さは１．１ＧＰａを超え、且つ伸びもＴｉ
−６Ａｌ−４Ｖの規格値である１０％を大きく上回って
いることがわかる。また合金Ｎｏ．１１および１２のも
のは、合金Ｎｏ．３〜７の実施例に比べてＣ含有量を増
やし且つＮの添加量を少なくした実施例であるが、いず
れも引張り強さは１．１ＧＰａを超え、且つ伸びもＴｉ
−６Ａｌ−４Ｖの規格値である１０％を大きく上回って
いることがわかる。尚合金Ｎｏ．１３および１４のもの
は、Ｃ含有量を本発明で規定する範囲（０．２０％）よ
りも多くして作成した比較例であるが、強度は１．１Ｇ
Ｐａを上回るものの、伸びが１０％を大きく下回ってい
た。On the other hand, alloy No. Examples 3 to 7 are examples satisfying the requirements defined in the present invention, and all have tensile strengths exceeding 1.1 GPa and elongations of Ti
It can be seen that it greatly exceeds the standard value of 10% of -6Al-4V. Alloy No. 11 and 12 are alloy Nos. In these examples, the C content was increased and the amount of N added was reduced as compared with the examples 3 to 7, but the tensile strength exceeded 1.1 GPa and the elongation was Ti.
It can be seen that it greatly exceeds the standard value of 10% of -6Al-4V. Alloy No. Samples Nos. 13 and 14 are comparative examples prepared by making the C content higher than the range (0.20%) specified in the present invention, but the strength is 1.1 G.
Although it exceeded Pa, the elongation was much less than 10%.
【００２６】[0026]
【発明の効果】本発明は以上の様に構成されており、溶
体化処理を施さずとも高強度が得られ、しかも高延性が
達成できるＴｉ合金が実現できた。またこのＴｉ合金
は、焼入れ等による材料の反りに対する矯正加工の必要
がなくなるので、加工しろを多くとる必要がなく、歩留
りが良いという効果も得られる。そしてこの様なＴｉ合
金は、Ｔｉ合金の適用範囲を更に拡大するものと期待さ
れる。EFFECTS OF THE INVENTION The present invention is constructed as described above, and it is possible to realize a Ti alloy which can obtain high strength and high ductility without being subjected to solution treatment. In addition, since the Ti alloy does not need to perform a correction process for the warpage of the material due to quenching or the like, there is no need to take a large amount of working margin, and an effect that the yield is good can be obtained. Such a Ti alloy is expected to further expand the application range of the Ti alloy.
【図１】Ｔｉ合金の機械的性質とＮ添加量の関係を示す
グラフである。FIG. 1 is a graph showing the relationship between the mechanical properties of a Ti alloy and the amount of N added.
【図２】Ｔｉ合金の機械的性質とＣ添加量の関係を示す
グラフである。FIG. 2 is a graph showing the relationship between the mechanical properties of a Ti alloy and the amount of C added.
─────────────────────────────────────────────────────
─────────────────────────────────────────────────── ───
【手続補正書】[Procedure amendment]
【提出日】平成７年１１月７日[Submission date] November 7, 1995
【手続補正１】[Procedure Amendment 1]
【補正対象書類名】明細書[Document name to be amended] Statement
【補正対象項目名】００２０[Correction target item name] 0020
【補正方法】変更[Correction method] Change
【補正内容】[Correction content]
【００２０】[0020]
【実施例】下記表１に示す化学成分組成を有するインゴ
ットをβ領域で鍛造し、鋳造組織を完全に破壊した後、
９００℃以上のα＋β領域の温度で十分な加工を施し
た。加工後は、７０５℃で焼鈍した後、室温にて引張試
験を行ない、各機械的性質（引張強さ、０．２％耐力、
伸び、絞り）を測定した。このとき、引張試験片の作成
および引張試験の実施は、ＡＳＴＭ Ｅ８に準処して行
なった。引張試験結果を、下記表２に示す。EXAMPLE An ingot having the chemical composition shown in Table 1 below was forged in the β region, and the cast structure was completely destroyed.
Sufficient processing was performed at a temperature in the α + β region of 900 ° C. or more. After processing, after annealing at 705 ° C., a tensile test is performed at room temperature, and each mechanical property (tensile strength, 0.2% proof stress,
Elongation, drawing) were measured. At this time, the preparation of the tensile test piece and the execution of the tensile test were performed according to ASTM E8. The results of the tensile test are shown in Table 2 below.
フロントページの続き (72)発明者 北川 喜久 兵庫県神戸市西区高塚台１丁目５番５号 株式会社神戸製鋼所神戸総合技術研究所内 (72)発明者 小出 憲司 兵庫県神戸市西区高塚台１丁目５番５号 株式会社神戸製鋼所神戸総合技術研究所内Front Page Continuation (72) Inventor Yoshihisa Kitagawa 1-5-5 Takatsukadai, Nishi-ku, Kobe-shi, Hyogo Inside Kobe Research Institute of Kobe Steel, Ltd. (72) Kenji Koide 1 Takazukadai, Nishi-ku, Kobe-shi, Hyogo Prefecture 5th-5th Kobe Steel Works, Ltd. Kobe Research Institute
Claims (3)
の意味、以下同じ），Ｖ：３．５〜４．５％，Ｆｅ：
０．２５〜０．３５％，Ｏ：０．１５〜０．２５％，
Ｃ：０．１０％以下，Ｎ：０．１５％以下を夫々含有
し、残部がＴｉおよび不可避不純物からなることを特徴
とする高強度高延性Ｔｉ合金。1. Al: more than 6.75 to 8.00% (% by weight)
, V: 3.5 to 4.5%, Fe:
0.25 to 0.35%, O: 0.15 to 0.25%,
A high-strength, high-ductility Ti alloy containing C: 0.10% or less and N: 0.15% or less, with the balance being Ti and unavoidable impurities.
る請求項１に記載の高強度高延性Ｔｉ合金。2. The high-strength and high-ductility Ti alloy according to claim 1, wherein the content of N is 0.03 to 0.15%.
３．５〜４．５％，Ｆｅ：０．２５〜０．３５％，Ｏ：
０．１５〜０．２５％，Ｃ：０．１０超〜０．２０％，
Ｎ：０．０３％以下を夫々含有し、残部がＴｉおよび不
可避不純物からなることを特徴とする高強度高延性Ｔｉ
合金。3. Al: more than 6.75 to 8.00%, V:
3.5-4.5%, Fe: 0.25-0.35%, O:
0.15 to 0.25%, C: more than 0.10 to 0.20%,
N: 0.03% or less, the balance being Ti and unavoidable impurities, characterized by high strength and high ductility Ti
alloy.
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP29512894A JP2608689B2 (en) | 1994-11-29 | 1994-11-29 | High strength and high ductility Ti alloy |
| US08/564,622 US5759484A (en) | 1994-11-29 | 1995-11-29 | High strength and high ductility titanium alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP29512894A JP2608689B2 (en) | 1994-11-29 | 1994-11-29 | High strength and high ductility Ti alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH08157987A true JPH08157987A (en) | 1996-06-18 |
| JP2608689B2 JP2608689B2 (en) | 1997-05-07 |
Family
ID=17816654
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP29512894A Expired - Lifetime JP2608689B2 (en) | 1994-11-29 | 1994-11-29 | High strength and high ductility Ti alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2608689B2 (en) |
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| WO2012023620A1 (en) * | 2010-08-20 | 2012-02-23 | 日本発條株式会社 | High-strength titanium alloy member and process for production thereof |
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