JPH04214830A - Ti alloy excellent in cold forgeability - Google Patents
Ti alloy excellent in cold forgeabilityInfo
- Publication number
- JPH04214830A JPH04214830A JP3908991A JP3908991A JPH04214830A JP H04214830 A JPH04214830 A JP H04214830A JP 3908991 A JP3908991 A JP 3908991A JP 3908991 A JP3908991 A JP 3908991A JP H04214830 A JPH04214830 A JP H04214830A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- deformation resistance
- weight
- cold
- type
- 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.)
- Granted
Links
- 229910001069 Ti alloy Inorganic materials 0.000 title abstract description 18
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 9
- 229910052718 tin Inorganic materials 0.000 abstract description 3
- 229910052720 vanadium Inorganic materials 0.000 abstract description 3
- 229910052782 aluminium Inorganic materials 0.000 abstract description 2
- 238000009721 upset forging Methods 0.000 abstract 1
- 229910045601 alloy Inorganic materials 0.000 description 16
- 239000000956 alloy Substances 0.000 description 16
- 230000000052 comparative effect Effects 0.000 description 10
- 230000032683 aging Effects 0.000 description 8
- 229910052758 niobium Inorganic materials 0.000 description 8
- 230000006835 compression Effects 0.000 description 6
- 238000007906 compression Methods 0.000 description 6
- 238000010273 cold forging Methods 0.000 description 4
- 229910052804 chromium Inorganic materials 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 238000005242 forging Methods 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 230000035882 stress Effects 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- 229910000883 Ti6Al4V Inorganic materials 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 229910052729 chemical element Inorganic materials 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Forging (AREA)
Abstract
Description
【０００１】0001
【産業上の利用分野】本発明は、冷間鍛造性に優れたＴ
ｉ合金に関し、詳細には従来のβ型Ｔｉ合金と同程度の
強度を維持しつつ、冷間加工性及び延性を向上させたＴ
ｉ合金に関するものである。[Industrial Application Field] The present invention provides T
Regarding the i alloy, in detail, it is a T alloy with improved cold workability and ductility while maintaining the same strength as the conventional β-type Ti alloy.
This relates to i-alloy.
【０００２】0002
【従来の技術】Ｔｉ合金は添加元素の種類や量によって
組織がかわり、α型，α＋β型，β型等に分類され、各
々個有の特性を示すことが知られている。これまでのＴ
ｉ合金としてはα＋β型Ｔｉ合金であるＴｉ−６Ａｌ−
４Ｖが最も多く利用されており、航空機や宇宙開発機器
を中心として需要が拡大しつつある。最近では上記Ｔｉ
合金の、軽く，強く、しかも耐食性に優れるという特性
に着目して、自動車や家庭用電化製品等をはじめとする
量産型民生品の部品として使用することも検討されはじ
めている。量産に適した部品としては冷間鍛造が効率良
く行なえることが要求され、この為には変形抵抗が小さ
く延性が大きいことが必要である。しかしながら前記α
＋β型Ｔｉ合金であるＴｉ−６Ａｌ−４Ｖは冷間加工性
に乏しく量産用の素材としては不適当である。BACKGROUND OF THE INVENTION It is known that the structure of Ti alloys changes depending on the type and amount of added elements, and is classified into α-type, α+β-type, β-type, etc., each of which exhibits unique characteristics. T so far
The i alloy is Ti-6Al- which is an α+β type Ti alloy.
4V is the most commonly used type, and demand is increasing mainly for aircraft and space development equipment. Recently, the above Ti
Focusing on the characteristics of alloys, which are light, strong, and excellent in corrosion resistance, consideration has begun to be given to using them as parts for mass-produced consumer products such as automobiles and home appliances. Parts suitable for mass production must be able to be cold-forged efficiently, and for this purpose, they must have low deformation resistance and high ductility. However, the α
Ti-6Al-4V, which is a +β type Ti alloy, has poor cold workability and is unsuitable as a material for mass production.
【０００３】冷間加工に適したＴｉ合金としてはβ型Ｔ
ｉ合金が有力視されており、応力誘起マルテンサイト変
態を生じるＴｉ−１６Ｖ−４Ｓｎや変形が双晶で起こる
Ｔｉ−１６Ｖ−１０Ｓｎ等が既に開発されている。本発
明者らが上記２種類のβ型Ｔｉ合金について変形抵抗を
比較調査したところ、Ｔｉ−１６Ｖ−４Ｓｎでは０．２
％耐力が３０ｋｇｆ／ｍｍ２程度、引張強さが５０ｋ
ｇｆ／ｍｍ２程度であるのに対して、Ｔｉ−１６Ｖ−１
０Ｓｎの０．２ ％耐力と引張強さは共に６０ｋｇｆ／
ｍｍ２程度にも及び、Ｔｉ−１６Ｖ−４Ｓｎの方が変形
抵抗の面で優れていることを確認している。[0003] β-type T is a Ti alloy suitable for cold working.
The i-alloy is considered to be a promising material, and Ti-16V-4Sn, which undergoes stress-induced martensitic transformation, and Ti-16V-10Sn, which undergoes deformation in the form of twin crystals, have already been developed. When the present inventors compared and investigated the deformation resistance of the above two types of β-type Ti alloys, it was found that Ti-16V-4Sn has a resistance of 0.2
% proof stress is about 30kgf/mm2, tensile strength is 50k
gf/mm2, while Ti-16V-1
The 0.2% yield strength and tensile strength of 0Sn are both 60kgf/
It has been confirmed that Ti-16V-4Sn is superior in terms of deformation resistance.
【０００４】但し、該Ｔｉ−１６Ｖ−４Ｓｎは据込み限
界においては既存のβ型Ｔｉ合金であるＴｉ−１５Ｖ−
３Ｃｒ−３Ｓｎ−３Ａｌ等に劣り、またＡｌを含有して
いないため耐酸化性に不安が残ると共に、時効処理時に
析出するα相が軟らかくて高強度が得られず、かと言っ
てＡｌを添加すると冷間鍛造性が極端に低下するという
問題を有している。However, at the upsetting limit, the Ti-16V-4Sn is inferior to the existing β-type Ti alloy Ti-15V-4Sn.
It is inferior to 3Cr-3Sn-3Al, etc., and since it does not contain Al, there are concerns about oxidation resistance, and the alpha phase that precipitates during aging treatment is soft, making it difficult to obtain high strength. There is a problem that cold forgeability is extremely reduced.
【０００５】ところで本発明者らは冷間鍛造性に優れた
Ｔｉ合金を開発すべく研究を重ねてきており、これまで
にも冷間鍛造に適した強度と延性を有するＴｉ合金を発
明して先に出願を行なった（特開平１−１２９９４１）
。By the way, the present inventors have been conducting research to develop a Ti alloy with excellent cold forging properties, and have so far invented a Ti alloy that has strength and ductility suitable for cold forging. The application was filed first (Japanese Patent Application Laid-open No. 1-129941)
.
【０００６】しかしながら上記先願合金で据込み鍛造を
行ない、既存のβ型Ｔｉ合金であるＴｉ−１５Ｖ−３Ｃ
ｒ−３Ｓｎ−３Ａｌと冷間鍛造性を比較したところ、変
形抵抗の面では優れているが、据込み限界の点ではＴｉ
−１５Ｖ−３Ｃｒ−３Ｓｎ−３Ａｌが８０％の圧縮率を
有するのに対して、上記先願合金は７５％と幾分低い圧
縮率を示している。そこでさらに冷間鍛造性の優れたＴ
ｉ合金を開発することが要望されている。However, upsetting forging was performed using the above-mentioned prior alloy, and Ti-15V-3C, which is an existing β-type Ti alloy, was used.
When comparing cold forgeability with r-3Sn-3Al, it is superior in terms of deformation resistance, but Ti is superior in terms of upsetting limit.
While -15V-3Cr-3Sn-3Al has a compressibility of 80%, the prior application alloy has a somewhat lower compressibility of 75%. Therefore, T with even better cold forging properties
There is a desire to develop i-alloys.
【０００７】[0007]
【発明が解決しようとする課題】本発明は上記事情に着
目してなされたものであって、既存のβ型Ｔｉ合金であ
るＴｉ−１５Ｖ−３Ｃｒ−３Ｓｎ−３Ａｌと同程度の据
込み限界を有すると共に変形抵抗がＴｉ−１６Ｖ−４Ｓ
ｎと同程度若しくはそれ以上に低い冷間鍛造性に優れた
Ｔｉ合金を提供することを目的とするものである。[Problems to be Solved by the Invention] The present invention has been made in view of the above circumstances, and it is an object of the present invention to achieve an upsetting limit comparable to that of Ti-15V-3Cr-3Sn-3Al, which is an existing β-type Ti alloy. Ti-16V-4S with deformation resistance
The object of the present invention is to provide a Ti alloy with excellent cold forgeability that is as low as or lower than n.
【０００８】[0008]
【課題を解決するための手段】上記目的を達成した本発
明とはＭｏおよび／またはＮｂ：０．５ 〜１８重量％
，Ｖ：１３〜１９重量％，Ａｌ：０．５ 〜６重量％，
Ｓｎ：０．５ 〜６重量％を含有し、残部がＴｉおよび
不可避不純物からなることを要旨とするものである。[Means for Solving the Problems] The present invention that achieves the above object is: Mo and/or Nb: 0.5 to 18% by weight
, V: 13 to 19% by weight, Al: 0.5 to 6% by weight,
The gist is that it contains Sn: 0.5 to 6% by weight, and the remainder consists of Ti and inevitable impurities.
【０００９】[0009]
【作用】本発明者らは変形に伴なって応力誘起マルテン
サイト変態を示すβ型Ｔｉ合金であるＴｉ−１６Ｖ−４
Ｓｎが低い変形抵抗を示すことに着目して、これに種々
の合金元素を添加して実験を繰り返す中で、Ａｌを適量
添加して適当な強度をもたせた上で、ある種のβ相安定
化元素を添加すれば、Ａｌ添加によるα相の安定化を抑
制し、強度及び冷間加工性が共に適切なレベルに改良さ
れることを知見して本発明に想到した。[Operation] The present inventors have developed Ti-16V-4, a β-type Ti alloy that exhibits stress-induced martensitic transformation upon deformation.
Focusing on the fact that Sn exhibits low deformation resistance, we repeated experiments by adding various alloying elements to it, and after adding an appropriate amount of Al to give it appropriate strength, we found that a certain type of β-phase stability was achieved. The present invention was conceived based on the finding that adding a chemical element suppresses the stabilization of the α phase caused by the addition of Al, and improves both strength and cold workability to appropriate levels.
【００１０】上記β相安定化元素を選択するにあたって
は、Ｍｏ，Ｎｂ，Ｆｅ，Ｃｒの中から選び、種々の添加
量を変えて実験を行なったところ、次の様な結果を得た
。即ちＦｅ，Ｃｒは合金の据込み限界を向上させる点で
は寄与するが、変形抵抗をも上昇させてしまうのに対し
、Ｍｏ，Ｎｂは据込み限界を向上させると同時に変形抵
抗もＴｉ−１６Ｖ−４Ｓｎより低く抑えることが可能で
あることを見い出したのである。[0010] In selecting the β-phase stabilizing element, the element was selected from among Mo, Nb, Fe, and Cr, and experiments were conducted with various addition amounts, and the following results were obtained. That is, although Fe and Cr contribute to improving the upsetting limit of the alloy, they also increase the deformation resistance, whereas Mo and Nb improve the upsetting limit and at the same time also increase the deformation resistance. They discovered that it is possible to keep the amount lower than 4Sn.
【００１１】以下本発明合金における各成分元素の添加
量の限定理由について述べる。The reason for limiting the amount of each component element added in the alloy of the present invention will be described below.
【００１２】Ａｌは時効処理によって十分な引張強度を
得る目的で添加するが、０．５ 重量％未満では時効処
理を施しても十分な引張強度が得られず、６重量％を超
えると延性及び冷間鍛造性が著しく低下するので、Ａｌ
の添加量は０．５ 〜６重量％とした。Al is added to obtain sufficient tensile strength through aging treatment, but if it is less than 0.5% by weight, sufficient tensile strength cannot be obtained even after aging treatment, and if it exceeds 6% by weight, ductility and Since cold forgeability is significantly reduced, Al
The amount added was 0.5 to 6% by weight.
【００１３】ＭｏとＮｂは据込み限界を向上させ、変形
抵抗を低くする目的で添加するが、０．５ 重量％未満
ではその効果が見られず、１８重量％を超えると変形抵
抗がかえって上昇するので、０．５ 〜１８重量％とし
た。尚この変形抵抗の上昇は固溶硬化によるものである
と考えられる。また本合金においてＭｏとＮｂはほぼ同
様に作用するので、両元素の添加量の合計が上記範囲内
に入っていれば、単独に用いても同時に用いても良い。[0013] Mo and Nb are added for the purpose of improving the upsetting limit and lowering the deformation resistance, but if it is less than 0.5% by weight, no such effect is seen, and if it exceeds 18% by weight, the deformation resistance increases. Therefore, the content was set at 0.5 to 18% by weight. It is believed that this increase in deformation resistance is due to solid solution hardening. Furthermore, since Mo and Nb act in substantially the same manner in this alloy, they may be used alone or simultaneously as long as the total amount of both elements added falls within the above range.
【００１４】ＶおよびＳｎの範囲を決定するにあたって
はＡｌおよびＭｏとＮｂを前記範囲内で添加した上で、
ＶおよびＳｎの添加量を変動させながら冷間鍛造性を評
価することによって行なった。Ｖは１３重量％未満では
据込み限界が低く、１９重量％を超えて添加すると変形
抵抗が上昇するので１３〜１９重量％とした。一方Ｓｎ
は０．５ 重量％未満になると据え込み限界が極端に低
下し、６重量％を超えて添加すると変形抵抗が上昇する
ので０．５ 〜６重量％とした。尚上記据込み限界の低
下は焼入れ時に拡散変態が進行するからであると考えら
れ、また変形抵抗の上昇は固溶硬化によるものと思われ
る。[0014] In determining the range of V and Sn, after adding Al, Mo and Nb within the above range,
The cold forgeability was evaluated while varying the amounts of V and Sn added. If V is added in an amount less than 13% by weight, the upsetting limit is low, and if it is added in an amount exceeding 19% by weight, the deformation resistance increases. On the other hand, Sn
If it is less than 0.5% by weight, the upsetting limit will be extremely lowered, and if it is added in excess of 6% by weight, the deformation resistance will increase, so it is set at 0.5 to 6% by weight. The decrease in the upsetting limit is thought to be due to the progress of diffusion transformation during quenching, and the increase in deformation resistance is thought to be due to solid solution hardening.
【００１５】[0015]
【実施例】表１及び表２に示す種々の組成を有するＴｉ
合金をボタン溶解にて溶製し（各６００ｇ）、２０ｍｍ
φになるまで１０００℃で約５０％の熱間鍛造を行なっ
た後、９００℃で１０分間保持することによって溶体化
処理を施し水冷を行なった。これより直径１６ｍｍ，高
さ２４ｍｍの円柱状試験片を切り出し、端面拘束状態で
冷間における据込み鍛造を行なった。[Example] Ti having various compositions shown in Tables 1 and 2
The alloy is melted by button melting (600g each), 20mm
After about 50% hot forging was performed at 1000°C until it reached φ, solution treatment was performed by holding at 900°C for 10 minutes and water cooling was performed. A cylindrical test piece with a diameter of 16 mm and a height of 24 mm was cut from this, and cold upsetting forging was performed with the end face restrained.
【００１６】冷間鍛造性の評価は参考文献［塑性と加工
，第２７巻，第３０４号（１９８６），５６８頁「冷間
鍛造用炭素鋼線材の変形抵抗と延性に関するデータシー
ト」］記載の手法に基づいて７０％及び８０％の変形抵
抗を測定すると共に、８０％圧縮したときの割れ発生の
有無を観察して行なった。[0016] The cold forgeability was evaluated according to the reference document [Plasticity and Processing, Vol. 27, No. 304 (1986), p. 568 "Data Sheet on Deformation Resistance and Ductility of Carbon Steel Wire Rods for Cold Forging"]. Based on this method, the deformation resistance at 70% and 80% was measured, and the presence or absence of cracking was observed when compressed by 80%.
【００１７】また一部の合金に対しては５００℃で８時
間保持する時効処理を施して引張試験を行ない、引張強
度及び伸びを測定した。結果は表１及び表２に併記する
。Further, some of the alloys were subjected to an aging treatment at 500° C. for 8 hours and subjected to a tensile test, and the tensile strength and elongation were measured. The results are also listed in Tables 1 and 2.
【００１８】[0018]
【表１】[Table 1]
【００１９】[0019]
【表２】[Table 2]
【００２０】Ｎｏ．１〜２０は各合金成分が本発明範囲
にある実施例であり、８０％の圧縮によっても割れの発
生は見られず、７０％及び８０％の変形抵抗も比較的低
い値を示している。Ｎｏ．１〜１４の実施例については
時効処理後の引張性質を調べたが、引張強度は９０ｋｇ
ｆ／ｍｍ２台と適度であり、伸びも１４％以上と高い。[0020]No. Examples 1 to 20 are examples in which each alloy component is within the range of the present invention, and no cracking was observed even under 80% compression, and the deformation resistance at 70% and 80% also showed relatively low values. No. For Examples 1 to 14, the tensile properties after aging treatment were investigated, and the tensile strength was 90 kg.
The f/mm is moderate at 2 levels, and the elongation is high at over 14%.
【００２１】Ｎｏ．２１〜３６は合金成分のいずれかが
本発明範囲をはずれた場合の比較例であり、下記の様に
冷間加工性若しくは時効処理後の引張強度の点で劣るこ
とがわかる。尚表１では８０％の圧縮で割れが発生した
場合は変形抵抗が測定できないので空欄にしている。Ｎ
ｏ．２１，２２はＭｏ，Ｎｂの添加量が少ない場合の比
較例であり、８０％の圧縮で割れが発生しており、変形
抵抗は測定不可能になっている。[0021]No. Nos. 21 to 36 are comparative examples in which any of the alloy components were outside the range of the present invention, and as shown below, it can be seen that they are inferior in cold workability or tensile strength after aging treatment. In Table 1, if cracking occurs at 80% compression, the deformation resistance cannot be measured, so the column is left blank. N
o. Comparative examples No. 21 and No. 22 have small amounts of Mo and Nb added, and cracks occurred at 80% compression, making it impossible to measure the deformation resistance.
【００２２】Ｎｏ．２３〜２５はＭｏ，Ｎｂの添加量が
多過ぎる場合の比較例であり、変形抵抗が高い。Ｎｏ．
２６，２７はＡｌの含有量が少ない場合の比較例であり
、時効処理後の引張強さが低い。Ｎｏ．２８，２９はＡ
ｌの含有量が多い場合の比較例であり、８０％の圧縮に
よって割れが発生すると共に時効処理後の伸びが７％以
下と著しく低い。Ｎｏ．３０はＳｎ量が少ない場合の比
較例であり、８０％の圧縮によって割れが発生している
。一方Ｎｏ．３１はＳｎ量が多い場合の比較例であり、
７０％及び８０％での変形抵抗が著しく高い。Ｎｏ．３
２はＶの添加量が少ない場合の比較例であり、８０％の
圧縮によって割れが発生している。これに対してＮｏ．
３３はＶの添加量が多い場合の比較例であり、７０％及
び８０％の変形抵抗が高い。Ｎｏ．３４〜３６はＭｏ若
しくはＮｂに代わってＦｅ若しくはＣｒが添加された場
合の比較例であり、いずれも変形抵抗が著しく高い。[0022]No. Nos. 23 to 25 are comparative examples in which the amounts of Mo and Nb added are too large, and the deformation resistance is high. No.
Nos. 26 and 27 are comparative examples with a low Al content, and the tensile strength after aging treatment is low. No. 28 and 29 are A
This is a comparative example in which the content of 1 is high, and cracks occur at 80% compression, and the elongation after aging treatment is extremely low at 7% or less. No. No. 30 is a comparative example in which the amount of Sn is small, and cracks occur due to 80% compression. On the other hand, No. 31 is a comparative example when the amount of Sn is large,
The deformation resistance at 70% and 80% is significantly higher. No. 3
2 is a comparative example in which the amount of V added is small, and cracks occur due to 80% compression. On the other hand, No.
No. 33 is a comparative example in which a large amount of V is added, and the deformation resistance is high at 70% and 80%. No. Nos. 34 to 36 are comparative examples in which Fe or Cr was added instead of Mo or Nb, and all of them had extremely high deformation resistance.
【００２３】[0023]
【発明の効果】本発明は以上の様に構成されているので
、既存のβ型Ｔｉ合金よりも変形抵抗が低く、しかも８
０％までの据込み鍛造が可能なＴｉ合金を提供すること
が可能となった。Effects of the Invention Since the present invention is constructed as described above, the deformation resistance is lower than that of existing β-type Ti alloys, and the
It has become possible to provide a Ti alloy that can be upset forged down to 0%.
Claims (1)
１８重量％，Ｖ：１３〜１９重量％，Ａｌ：０．５ 〜
６重量％，Ｓｎ：０．５ 〜６重量％を含有し、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冷間
鍛造性に優れたＴｉ合金。[Claim 1] Mo and/or Nb: 0.5~
18% by weight, V: 13-19% by weight, Al: 0.5-
6% by weight, Sn: 0.5 to 6% by weight, and the remainder consists of Ti and unavoidable impurities.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2-31060 | 1990-02-09 | ||
| JP3106090 | 1990-02-09 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH04214830A true JPH04214830A (en) | 1992-08-05 |
| JP2936754B2 JP2936754B2 (en) | 1999-08-23 |
Family
ID=12320934
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3908991A Expired - Fee Related JP2936754B2 (en) | 1990-02-09 | 1991-02-08 | Ti alloy excellent in cold forgeability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2936754B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2013154629A1 (en) * | 2012-02-15 | 2013-10-17 | Rti International Metals, Inc. | Titanium alloys |
| CN120095001A (en) * | 2025-05-08 | 2025-06-06 | 西部超导材料科技股份有限公司 | Preparation method of TC16 titanium alloy and large single weight round wire for cold heading fasteners |
-
1991
- 1991-02-08 JP JP3908991A patent/JP2936754B2/en not_active Expired - Fee Related
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2013154629A1 (en) * | 2012-02-15 | 2013-10-17 | Rti International Metals, Inc. | Titanium alloys |
| CN120095001A (en) * | 2025-05-08 | 2025-06-06 | 西部超导材料科技股份有限公司 | Preparation method of TC16 titanium alloy and large single weight round wire for cold heading fasteners |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2936754B2 (en) | 1999-08-23 |
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