JP2002235133A - beta TYPE TITANIUM ALLOY - Google Patents
beta TYPE TITANIUM ALLOYInfo
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- JP2002235133A JP2002235133A JP2001032460A JP2001032460A JP2002235133A JP 2002235133 A JP2002235133 A JP 2002235133A JP 2001032460 A JP2001032460 A JP 2001032460A JP 2001032460 A JP2001032460 A JP 2001032460A JP 2002235133 A JP2002235133 A JP 2002235133A
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、自動車エンジン用
コンロッド、バルブ、ばね、航空機エンジン用ブレー
ド、ディスク等の軽量、高強度を必要とする各種部材、
あるいは釣り具、ゴルフクラブ等のレジャー用品、車椅
子等の医療福祉機器等の各種構造部材に適した強度、靱
延性および耐摩耗性に優れた経済的なβ型チタン合金に
関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to various members requiring light weight and high strength, such as connecting rods for automobile engines, valves, springs, blades for aircraft engines, disks, and the like.
Also, the present invention relates to an economical β-type titanium alloy excellent in strength, toughness and ductility, and abrasion resistance suitable for various structural members such as fishing gear, leisure articles such as golf clubs, and medical and welfare equipment such as wheelchairs.
【０００２】[0002]
【従来の技術】チタン合金は、軽量・高強度であること
から航空機エンジン用コンプレッサのブレード、ディス
ク用の材料として用いられていたが、近年、自動車用エ
ンジンの高出力化、燃費改善の要求が高まるに伴い、コ
ンロッド、エンジンバルブ、バルブスプリング等の軽量
化を目的にチタン合金の使用が進められるようになっ
た。また、釣り具、ゴルフクラブなどのレジャー用品に
ついても、軽量・高強度、および耐食性に優れたチタン
合金の利用が大いに増大している。これらの部材はいず
れも強靭性が要求されるので、これらに用いる材料とし
ては高強度が得やすいβ型チタン合金が有利である。2. Description of the Related Art Titanium alloys have been used as materials for blades and disks of aircraft engine compressors because of their light weight and high strength. In recent years, however, there has been a demand for higher output and improved fuel economy of automobile engines. With the increase, the use of titanium alloys has been promoted to reduce the weight of connecting rods, engine valves, valve springs, and the like. In addition, for leisure goods such as fishing gear and golf clubs, the use of titanium alloys having excellent lightweight and high strength and excellent corrosion resistance has been greatly increased. Since all of these members are required toughness, a β-type titanium alloy which is easy to obtain high strength is advantageous as a material used for these members.
【０００３】従来、β型チタン合金としては、Ｔｉ−１
５Ｖ−３Ａｌ−３Ｃｒ−３Ｓｎ、Ｔｉ−３Ａｌ−８Ｖ−
６Ｃｒ−４Ｍｏ−４Ｓｎ、Ｔｉ−１３Ｖ−１１Ｃｒ−３
Ａｌ、Ｔｉ−１５Ｍｏ−５Ｚｒ−３Ａｌ、Ｔｉ−２９Ｎ
ｂ−１３Ｔａ−−４．６Ｚｒ等が開発されている。Conventionally, as a β-type titanium alloy, Ti-1
5V-3Al-3Cr-3Sn, Ti-3Al-8V-
6Cr-4Mo-4Sn, Ti-13V-11Cr-3
Al, Ti-15Mo-5Zr-3Al, Ti-29N
b-13Ta--4.6Zr and the like have been developed.
【０００４】[0004]
【発明が解決しようとする課題】しかしながら、上記の
ごとき従来のβ型チタン合金は、いずれもＶ、Ｍｏ、Ｎ
ｂ、Ｔａといった全率固溶形のβ安定化元素を多量に含
んでいるので高価であり、その用途が制限されるという
問題があった。本発明は、安価な合金元素の添加によっ
て、高強度を有する低廉なβ型チタン合金を提供するこ
とを目的とする。However, the conventional β-type titanium alloys as described above all use V, Mo, N
Since it contains a large amount of the β-stabilizing element in the form of solid solution such as b and Ta, it is expensive and its use is limited. An object of the present invention is to provide an inexpensive β-type titanium alloy having high strength by adding an inexpensive alloy element.
【０００５】[0005]
【課題を解決するための手段】上記問題を解決するため
に、本発明のβ型チタン合金は、Ｖ、Ｍｏ、Ｎｂ、Ｔａ
といった高価な元素を含まずにβ相を安定化させる方法
として、安価なＣｒ，Ｆｅ、Ｎｉといった共析形のβ安
定化元素を用い、これらを適量組み合わせることで、従
来β相の安定化のために省略することのできなかった
Ｖ、Ｍｏなどの添加を省略し合金の低廉化を図ったもの
である。すなわち、本発明のβ型チタン合金は、 （１）質量％で、Ｃｒ：２〜１２％、Ｆｅ：８．８％以
下を含み、かつ、含有するＦｅの質量％を〔Ｆｅ〕、含
有するＣｒの質量％を〔Ｃｒ〕として〔Ｆｅ〕＋０．６
〔Ｃｒ〕の値が６〜１０％であり、残部Ｔｉおよび不可
避的不純物からなることを特徴とする。 （２）質量％で、Ｃｒ：２〜１２％、Ｆｅ：８．８％以
下、Ｎｉ：７％以下を含み、かつ、含有するＦｅの質量
％を〔Ｆｅ〕、含有するＣｒの質量％を〔Ｃｒ〕、含有
するＮｉの質量％を〔Ｎｉ〕として〔Ｆｅ〕＋０．６
〔Ｃｒ〕＋０．４〔Ｎｉ〕の値が６〜１０％であり、残
部Ｔｉおよび不可避的不純物からなることを特徴とす
る。 （３）上記（１）または（２）のいずれか一項に記載す
る要件に加えて、さらに、Ａｌ：６％以下を含むことを
特徴とする。In order to solve the above problems, a β-type titanium alloy of the present invention comprises V, Mo, Nb, Ta
As a method of stabilizing the β phase without including such expensive elements, inexpensive eutectoid β-stabilizing elements such as Cr, Fe, and Ni are used, and by combining them in an appropriate amount, the stabilization of the conventional β-phase can be achieved. Therefore, the addition of V, Mo, etc., which could not be omitted, was omitted to reduce the cost of the alloy. That is, the β-type titanium alloy of the present invention contains (1) mass% of Cr: 2 to 12% and Fe: 8.8% or less, and also contains [Fe], which is the mass% of the contained Fe. [Fe] +0.6, where the mass% of Cr is [Cr]
It is characterized in that the value of [Cr] is 6 to 10%, and the balance consists of Ti and unavoidable impurities. (2) By mass%, it contains Cr: 2 to 12%, Fe: 8.8% or less, Ni: 7% or less, and the mass% of the contained Fe is [Fe] and the mass% of the contained Cr is [Fe]. [Cr], [Fe] +0.6
The value of [Cr] +0.4 [Ni] is 6 to 10%, and the balance is made up of Ti and unavoidable impurities. (3) In addition to the requirements described in any one of the above (1) and (2), the composition further includes Al: 6% or less.
【０００６】[0006]
【発明の実施の形態】以下、本発明のβ型チタン合金に
おいて化学成分の含有率を限定する理由について説明す
る。本発明のチタン合金において、Ｆｅ、Ｃｒ、Ｎｉ
は、合金を強度の高いβ相とするために添加する。Ｆｅ
は、Ｃｒ、Ｎｉに比べて安価な元素であり、Ｆｅ含有量
の増加に伴ってチタン合金の強度は上昇するが、Ｆｅの
単独添加によって強度上昇したβチタン合金は延性に乏
しく、強度−延性のバランスに劣る。そこで、本発明の
チタン合金においては、上記の欠点を補うため適量のＣ
ｒを添加する。DESCRIPTION OF THE PREFERRED EMBODIMENTS The reasons for limiting the content of chemical components in the β-type titanium alloy of the present invention will be described below. In the titanium alloy of the present invention, Fe, Cr, Ni
Is added to make the alloy into a β phase having high strength. Fe
Is an element that is inexpensive compared to Cr and Ni, and the strength of the titanium alloy increases with an increase in the Fe content. However, the β-titanium alloy whose strength has been increased by the single addition of Fe has poor ductility, and the strength-ductility is low. Poor balance. Therefore, in the titanium alloy of the present invention, an appropriate amount of C
Add r.
【０００７】すなわち、Ｃｒは、Ｔｉをβ相化する効果
を有するとともに合金の延性を高める効果を有する比較
的安価な元素であり、本発明のβ型チタン合金の構成に
必須の元素として含有率２〜１２％の範囲で添加する。
Ｃｒ含有率２％未満では延性向上の効果が十分でないの
で、Ｃｒ含有率の下限を２％とする。That is, Cr is a relatively inexpensive element that has the effect of turning Ti into the β phase and also has the effect of increasing the ductility of the alloy, and its content as an essential element in the structure of the β-type titanium alloy of the present invention. Add in the range of 2-12%.
If the Cr content is less than 2%, the effect of improving ductility is not sufficient, so the lower limit of the Cr content is set to 2%.
【０００８】β相をある程度安定化し、良好な強度−延
性バランスを得るためには、上記のようにＣｒ含有率を
２％以上とし、かつ、〔Ｆｅ〕＋０．６〔Ｃｒ〕の値を
６％以上とする必要がある。ここに〔Ｆｅ〕、〔Ｃｒ〕
はそれぞれＦｅ、Ｃｒの含有率（質量％）とする。ま
た、Ｃｒ：１２％、Ｆｅ：８．８％を超えるか、または
〔Ｆｅ〕＋０．６〔Ｃｒ〕の値が１０％を超えると、熱
処理の際に、脆化要因となる金属間化合物（ＴｉＣ
ｒ2、ＴｉＦｅ等）が形成されやすくなり、合金の強度
−延性バランスが低下するので、それぞれの含有率の上
限を、Ｃｒについては１２％、Ｆｅについては８．８％
とし、また、〔Ｆｅ〕＋０．６〔Ｃｒ〕については１０
％とする。In order to stabilize the β phase to some extent and obtain a good strength-ductility balance, as described above, the Cr content should be 2% or more, and the value of [Fe] +0.6 [Cr] should be 6%. % Or more. Where [Fe], [Cr]
Is the content (% by mass) of Fe and Cr, respectively. On the other hand, if the content of Cr exceeds 12% and the content of Fe exceeds 8.8%, or the value of [Fe] +0.6 [Cr] exceeds 10%, the intermetallic compound which causes embrittlement during heat treatment ( TiC
r 2 , TiFe, etc.) are easily formed and the strength-ductility balance of the alloy is reduced. Therefore, the upper limit of each content is set to 12% for Cr and 8.8% for Fe.
And [Fe] +0.6 [Cr] is 10
%.
【０００９】Ｎｉは、Ｆｅ、Ｃｒと同様にβ相を安定化
する比較的安価な元素であって、本発明の合金において
は、Ｆｅ、Ｃｒの一部に置換して添加することができ
る。Ｎｉを含む本発明の合金においては、β相をある程
度安定化し、良好な強度−延性バランスを得るために
は、上記のようにＣｒ含有率を２％以上とし、かつ、
〔Ｆｅ〕＋０．６〔Ｃｒ〕＋０．４〔Ｎｉ〕の値を６％
以上とする必要がある。しかし、Ｎｉを過剰に含有する
と、熱処理の際に、脆化要因となる金属間化合物（Ｔｉ
Ｎｉ2 ）が形成されやすくなり、合金の強度−延性バラ
ンスが低下するので、Ｎｉ含有率については７％、ま
た、〔Ｆｅ〕＋０．６〔Ｃｒ〕＋０．４〔Ｎｉ〕につい
ては１０％を上限とする。Ni is a relatively inexpensive element that stabilizes the β phase similarly to Fe and Cr. In the alloy of the present invention, Ni can be added by substituting a part of Fe and Cr. In the alloy of the present invention containing Ni, in order to stabilize the β phase to some extent and obtain a good strength-ductility balance, the Cr content is set to 2% or more as described above, and
[Fe] +0.6 [Cr] +0.4 [Ni] is 6%
It is necessary to do above. However, if Ni is excessively contained, an intermetallic compound (Ti
Ni 2 ) is easily formed, and the strength-ductility balance of the alloy is reduced. Therefore, the Ni content is 7%, and the [Fe] +0.6 [Cr] +0.4 [Ni] is 10%. Upper limit.
【００１０】本発明のβ型チタン合金は、βトランザス
以上の温度に加熱したのち急冷することにより均一なβ
相とし、優れた強度と延性を有するものとすることがで
きるが、さらに、３５０〜６００℃、好ましくは４００
〜５００℃で時効処理を施すことにより合金の硬さを増
して耐摩耗性を向上することができる。Ａｌは、合金の
時効処理時に生じるα相を強化する元素として添加する
が、過剰に添加すると金属間化合物Ｔｉ3Ａｌを析出し
て合金を脆化するので、含有率の上限を６％とする。The β-type titanium alloy of the present invention is heated to a temperature equal to or higher than β transus and then rapidly cooled to obtain a uniform β-type titanium alloy.
Phase, and can have excellent strength and ductility.
By performing aging treatment at a temperature of up to 500 ° C., the hardness of the alloy can be increased and the wear resistance can be improved. Al is added as an element that strengthens the α phase generated during the aging treatment of the alloy, but if added excessively, it precipitates the intermetallic compound Ti 3 Al and embrittles the alloy, so the upper limit of the content is set to 6%. .
【００１１】[0011]
【実施例】純度９９．８％のスポンジチタン、純度９
９．９％の純鉄、純度９９．３％の純クロム、低炭素フ
ェロクロム２号、純度９９．９％の純Ｎｉ、ＳＵＳ３０
４鋼屑を原材料として、プラズマスカル炉を用いて、質
量約６ｋｇ、直径１００ｍｍのチタン合金インゴットを
溶製した。また、比較材として、公知のＴｉ−６Ａｌ−
４Ｖ合金およびＴｉ−１５Ｖ−３Ａｌ−３Ｃｒ−３Ｓｎ
合金を溶製した。得られたインゴットの化学組成を表１
に示す。前記インゴットを９５０℃に加熱し、熱間鍛造
によって直径２０ｍｍの丸棒とした。該丸棒に表１に示
す熱処理を加えて試験材とした。ここに、実施例３、実
施例８および実施例１２は固溶化処理後時効処理を施し
たものであり、その他の試験材は固溶化処理のみを施し
たものである。Example: 99.8% pure titanium sponge, purity 9
9.9% pure iron, 99.3% pure chromium, low carbon ferrochrome No. 2, 99.9% pure Ni, SUS30
Using a steel scrap as a raw material, a titanium alloy ingot having a mass of about 6 kg and a diameter of 100 mm was melted using a plasma skull furnace. In addition, as a comparative material, a known Ti-6Al-
4V alloy and Ti-15V-3Al-3Cr-3Sn
The alloy was melted. Table 1 shows the chemical composition of the obtained ingot.
Shown in The ingot was heated to 950 ° C. and formed into a round bar having a diameter of 20 mm by hot forging. The round bar was subjected to the heat treatment shown in Table 1 to obtain a test material. Here, in Examples 3, 8 and 12, the aging treatment was performed after the solution treatment, and the other test materials were subjected to only the solution treatment.
【００１２】[0012]
【表１】 [Table 1]
【００１３】前記試験材から機械加工によってＡＳＴＭ
Ｅ８に規定される３号引張試験片（直径６．２５ｍ
ｍ、標点距離２５ｍｍ）およびピン・オン・ディスク摩
耗試験片（直径７．９８ｍｍ、長さ１９ｍｍ）を製作し
た。引張試験は、インストロン型引張試験機を用いてク
ロスヘッド速度を５×１０ -5ｍ／ｓで行い、引張強さと
破断絞りを測定した。[0013] ASTM is machined from the test material.
No. 3 tensile test piece specified in E8 (diameter 6.25 m
m, gauge length 25 mm) and pin-on-disk wear
Wear test specimens (diameter 7.98mm, length 19mm)
Was. The tensile test was performed using an Instron type tensile tester.
5 x 10 loss head speed -Fivem / s, tensile strength and
The breaking draw was measured.
【００１４】摩耗試験は、ピン・オン・ディスク摩耗試
験機を用い、硬さＨＲＣ６１としたＳＵＳ４４０Ｃ鋼の
ディスク平面に前記ピン・オン・ディスク摩耗試験片の
端面を負荷荷重１０ｋｇｆで押付け、潤滑油なし、滑り
速度１ｍ／ｓで滑り距離４００ｍとして行い、摩耗減量
を測定した。The abrasion test was performed by using a pin-on-disk abrasion tester and pressing the end surface of the pin-on-disk abrasion test piece against a flat surface of SUS440C steel having hardness HRC61 at a load of 10 kgf without lubricating oil. The sliding speed was 1 m / s and the sliding distance was 400 m, and the wear loss was measured.
【００１５】上記の各試験結果を表２に示す。図１は、
本発明のＴｉ−Ｆｅ−Ｃｒ系合金（第１発明）、Ｔｉ−
Ｆｅ−Ｃｒ−Ｎｉ系合金（第２発明）、Ｔｉ−Ｆｅ−Ｃ
ｒ（−Ｎｉ）−Ａｌ系合金（第３発明）、比較例に層別
して引張強さと破断絞りとの関係を示したものである。Table 2 shows the results of the above tests. FIG.
Ti-Fe-Cr alloy of the present invention (first invention), Ti-
Fe-Cr-Ni alloy (second invention), Ti-Fe-C
It is a diagram showing the relationship between tensile strength and breaking reduction for each layer of an r (-Ni) -Al alloy (third invention) and a comparative example.
【００１６】[0016]
【表２】 [Table 2]
【００１７】表２および図１から判るように、本発明の
実施例は、公知のＴｉ−６Ａｌ−４Ｖ合金（比較例
１）、Ｔｉ−１５Ｖ−３Ａｌ−３Ｃｒ−３Ｓｎ合金(比
較例２)、Ｆｅのみの添加によって強化したＴｉ−Ｆｅ
合金（比較例３）およびＣｒのみの添加によって強化し
たＴｉ−Ｃｒ合金（比較例４）と同等の破断絞り値であ
るならば比較例よりも引張強さが大きく、同等の引張強
さならば比較例よりも破断絞りが大きい。すなわち、本
発明の実施例は、比較例に較べて強度−延性バランスに
優れているといえる。As can be seen from Table 2 and FIG. 1, the examples of the present invention include the known Ti-6Al-4V alloy (Comparative Example 1), Ti-15V-3Al-3Cr-3Sn alloy (Comparative Example 2), Ti-Fe strengthened by addition of Fe only
The tensile strength is higher than that of the comparative example if the breaking reduction value is equivalent to that of the alloy (Comparative Example 3) and the Ti—Cr alloy reinforced by adding only Cr (Comparative Example 4). Breaking draw is larger than that of the comparative example. That is, it can be said that the examples of the present invention are superior in the strength-ductility balance as compared with the comparative examples.
【００１８】固溶化処理後時効処理を施した実施例３、
実施例８および実施例１２は、それぞれ時効処理を施さ
ない実施例２、実施例７および実施例１１に較べて著し
く引張強さが向上している。そして時効処理を施した各
実施例においても強度−延性バランスは比較材に較べて
良好である。さらに、表２から判るように、本発明の実
施例は、比較例に較べて摩耗減量が少なく、特に事項処
理を施した実施例３、実施例８および実施例１２につい
ては優れた耐摩耗性を有することを確認した。Example 3 in which aging treatment was performed after the solution treatment,
In Examples 8 and 12, the tensile strength is remarkably improved as compared with Examples 2, 7 and 11, respectively, in which the aging treatment is not performed. Also in each of the examples subjected to the aging treatment, the strength-ductility balance is better than the comparative material. Furthermore, as can be seen from Table 2, the examples of the present invention have less wear loss than the comparative examples, and particularly, the examples 3, 8 and 12 which have been subjected to the item treatment have excellent wear resistance. Was confirmed.
【００１９】[0019]
【発明の効果】以上に説明したように、本発明のβ型チ
タン合金によれば、従来のβ型チタン合金のようにＶ、
Ｍｏ、Ｎｂ、Ｔａといった高価な合金元素を含むことな
く、Ｆｅ、Ｃｒ、Ｎｉ、Ａｌといった比較的安価な合金
元素を添加することによって高強度を有する低廉なβ型
チタン合金を提供することができる。しかも、前記合金
元素の添加にあたっては、フェロクロムやステンレス鋼
屑などの安価な合金原料を用いて行うことができるので
チタン合金の用途拡大に有利であり、本発明の経済効果
は一層大きいといえる。As described above, according to the β-type titanium alloy of the present invention, V,
An inexpensive β-type titanium alloy having high strength can be provided by adding relatively inexpensive alloy elements such as Fe, Cr, Ni, and Al without including expensive alloy elements such as Mo, Nb, and Ta. . In addition, the addition of the alloy element can be performed using inexpensive alloy raw materials such as ferrochrome and stainless steel scrap, which is advantageous for expanding the use of titanium alloys, and the economic effect of the present invention can be said to be even greater.
【図１】引張強さと破断伸びとの関係を示す相関図であ
る。FIG. 1 is a correlation diagram showing the relationship between tensile strength and elongation at break.
Claims (3)
８．８％以下を含み、かつ、含有するＦｅの質量％を
〔Ｆｅ〕、含有するＣｒの質量％を〔Ｃｒ〕として〔Ｆ
ｅ〕＋０．６〔Ｃｒ〕の値が６〜１０％であり、残部Ｔ
ｉおよび不可避的不純物からなることを特徴とするβ型
チタン合金。1. The method according to claim 1, wherein in mass%, Cr: 2 to 12%, Fe:
8.8% or less, the mass% of Fe contained is [Fe], and the mass% of Cr contained is [Cr] [F
e] +0.6 [Cr] is 6 to 10%, and the balance T
A β-type titanium alloy comprising i and unavoidable impurities.
８．８％以下、Ｎｉ：７％以下を含み、かつ、含有する
Ｆｅの質量％を〔Ｆｅ〕、含有するＣｒの質量％を〔Ｃ
ｒ〕、含有するＮｉの質量％を〔Ｎｉ〕として〔Ｆｅ〕
＋０．６〔Ｃｒ〕＋０．４〔Ｎｉ〕の値が６〜１０％で
あり、残部Ｔｉおよび不可避的不純物からなることを特
徴とするβ型チタン合金。2. In mass%, Cr: 2 to 12%, Fe:
8.8% or less, Ni: 7% or less, and the contained mass% of Fe is [Fe], and the contained mass% of Cr is [C
r], the mass% of the contained Ni is [Ni] and [Fe]
A β-type titanium alloy, wherein the value of +0.6 [Cr] +0.4 [Ni] is 6 to 10% and the balance is Ti and unavoidable impurities.
６％以下を含むことを特徴とする請求項１または２のい
ずれか一項記載のβ型チタン合金。3. In addition to the above chemical components, Al:
The β-type titanium alloy according to claim 1, wherein the β-type titanium alloy contains 6% or less.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2001032460A JP2002235133A (en) | 2001-02-08 | 2001-02-08 | beta TYPE TITANIUM ALLOY |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2001032460A JP2002235133A (en) | 2001-02-08 | 2001-02-08 | beta TYPE TITANIUM ALLOY |
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| Publication Number | Publication Date |
|---|---|
| JP2002235133A true JP2002235133A (en) | 2002-08-23 |
Family
ID=18896387
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2001032460A Pending JP2002235133A (en) | 2001-02-08 | 2001-02-08 | beta TYPE TITANIUM ALLOY |
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| Country | Link |
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| JP (1) | JP2002235133A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2005060821A (en) * | 2003-07-25 | 2005-03-10 | Daido Steel Co Ltd | beta TYPE TITANIUM ALLOY, AND COMPONENT MADE OF beta TYPE TITANIUM ALLOY |
| JP2006200008A (en) * | 2005-01-21 | 2006-08-03 | Daido Steel Co Ltd | beta-TYPE TITANIUM ALLOY AND PARTS MADE FROM beta-TYPE TITANIUM ALLOY |
| WO2008050892A1 (en) | 2006-10-26 | 2008-05-02 | Nippon Steel Corporation | Beta titanium alloy |
| JP2009270163A (en) * | 2008-05-08 | 2009-11-19 | Daido Steel Co Ltd | Titanium alloy |
| CN105838910A (en) * | 2016-05-31 | 2016-08-10 | 沈阳中核舰航特材科技有限公司 | Manufacturing method of antibacterial titanium alloy for bio-medical treatment |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0361341A (en) * | 1989-07-28 | 1991-03-18 | Amano Masuo | High strength titanium alloy having excellent workability |
-
2001
- 2001-02-08 JP JP2001032460A patent/JP2002235133A/en active Pending
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0361341A (en) * | 1989-07-28 | 1991-03-18 | Amano Masuo | High strength titanium alloy having excellent workability |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2005060821A (en) * | 2003-07-25 | 2005-03-10 | Daido Steel Co Ltd | beta TYPE TITANIUM ALLOY, AND COMPONENT MADE OF beta TYPE TITANIUM ALLOY |
| JP4581425B2 (en) * | 2003-07-25 | 2010-11-17 | 大同特殊鋼株式会社 | β-type titanium alloy and parts made of β-type titanium alloy |
| JP2006200008A (en) * | 2005-01-21 | 2006-08-03 | Daido Steel Co Ltd | beta-TYPE TITANIUM ALLOY AND PARTS MADE FROM beta-TYPE TITANIUM ALLOY |
| WO2008050892A1 (en) | 2006-10-26 | 2008-05-02 | Nippon Steel Corporation | Beta titanium alloy |
| US9816158B2 (en) | 2006-10-26 | 2017-11-14 | Nippon Steel & Sumitomo Metal Corporation | β-type titanium alloy |
| US9822431B2 (en) | 2006-10-26 | 2017-11-21 | Nippon Steel & Sumitomo Metal Corporation | β-type titanium alloy |
| US10125411B2 (en) | 2006-10-26 | 2018-11-13 | Nippon Steel & Sumitomo Metal Corporation | β-type titanium alloy |
| JP2009270163A (en) * | 2008-05-08 | 2009-11-19 | Daido Steel Co Ltd | Titanium alloy |
| CN105838910A (en) * | 2016-05-31 | 2016-08-10 | 沈阳中核舰航特材科技有限公司 | Manufacturing method of antibacterial titanium alloy for bio-medical treatment |
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