JP2015025167A - β-type titanium alloy - Google Patents
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Abstract
Description
本発明は、β型チタン合金に関し、さらに詳しくは、比強度が高くかつ冷間加工性に優れたβ型チタン合金に関する。 The present invention relates to a β-type titanium alloy, and more particularly to a β-type titanium alloy having high specific strength and excellent cold workability.
実用チタン合金は、
（１）最密六方晶のα相（低温相）からなるα型合金、
（２）体心立方晶のβ相（高温相）からなるβ型合金、
（３）α相とβ相の混合組織を持つα＋β型合金、
に大別される。
Practical titanium alloys are
(1) α-type alloy composed of close-packed hexagonal α-phase (low-temperature phase),
(2) β-type alloy consisting of a body-centered cubic β-phase (high-temperature phase),
(3) α + β type alloy having a mixed structure of α phase and β phase,
It is divided roughly into.
これらの内、α＋β型合金は、強度、比強度、熱処理性、加工性、耐食性などに優れたバランスの良い材料であり、従来は、主に宇宙航空機材料として用いられてきた。また、自動車用材料、機械構造部品用材料、一般民需用材料等としても使用されてきている。特に、α＋β型合金の中でもＴｉ−６Ａｌ−４Ｖ合金は、汎用高力チタン合金として広く用いられており、Ｔｉ合金使用量の約８０％を占めている。
しかしながら、Ｔｉ−６Ａｌ−４Ｖ合金は、高価なＶを含んでいるために高コストであり、かつ、冷間加工性に乏しい。
Among these, the α + β type alloy is a well-balanced material excellent in strength, specific strength, heat treatment property, workability, corrosion resistance, and the like, and has conventionally been mainly used as a spacecraft material. It has also been used as a material for automobiles, a material for mechanical structural parts, a material for general civilian use, and the like. In particular, among the α + β type alloys, the Ti-6Al-4V alloy is widely used as a general-purpose high-strength titanium alloy and occupies about 80% of the amount of Ti alloy used.
However, the Ti-6Al-4V alloy is expensive because it contains expensive V and has poor cold workability.
一方、β型チタン合金は、一般に、Ｔｉ−６Ａｌ−４Ｖ合金に比べて冷間加工性に優れている。また、成分元素を最適化すれば、その強度は、Ｔｉ−６Ａｌ−４Ｖ合金と同等となる。しかしながら、従来のβ型合金は、高価なＶを多量に含んだＶ系が一般的であり、高コストである。 On the other hand, β-type titanium alloys are generally excellent in cold workability as compared with Ti-6Al-4V alloys. Further, if the component elements are optimized, the strength becomes equivalent to that of the Ti-6Al-4V alloy. However, a conventional β-type alloy is generally a V system containing a large amount of expensive V and is expensive.
そこでこの問題を解決するために、従来から種々の提案がなされている。
例えば、特許文献１には、質量％で、Ｃｒ：１０〜２０％およびＦｅ：５％以下を含有し、残部がＴｉおよび不可避な不純物からなる合金組成を有するβ型チタン合金が開示されている。
同文献には、Ｃｒを添加することによって高強度で量産が容易なβ型チタン合金が得られ、高価な添加元素を必要としない点が記載されている。
In order to solve this problem, various proposals have heretofore been made.
For example, Patent Document 1 discloses a β-type titanium alloy having an alloy composition containing, by mass%, Cr: 10 to 20% and Fe: 5% or less, and the balance being Ti and inevitable impurities. .
This document describes that by adding Cr, a β-type titanium alloy having high strength and easy mass production can be obtained, and an expensive additive element is not required.
Ｃｒ系のβ型チタン合金は、Ｖ系に比べて低コストであり、溶体化処理ままでの強度も高い（Ｔｉ−６Ａｌ−４Ｖ合金と同等）。しかしながら、Ｃｒ系のβ型チタン合金は、冷間加工性が悪いという欠点がある。 The Cr-based β-type titanium alloy is lower in cost than the V-based alloy, and has a high strength as a solution treatment (equivalent to a Ti-6Al-4V alloy). However, Cr-based titanium alloys have the disadvantage of poor cold workability.
本発明が解決しようとする課題は、低コスト、高強度、かつ、高い冷間加工性を有する新規なβ型チタン合金を提供することにある。 The problem to be solved by the present invention is to provide a novel β-type titanium alloy having low cost, high strength, and high cold workability.
上記課題を解決するために本発明に係るβ型チタン合金は、
８．０＜Ｍｎ＜２０．０ｍａｓｓ％、
０．５≦Ｆｅ＜５．０ｍａｓｓ％、及び、
０．５＜Ａｌ＜５．０ｍａｓｓ％
を含み、残部がＴｉ及び不可避的不純物からなることを要旨とする。
In order to solve the above problems, the β-type titanium alloy according to the present invention is
8.0 <Mn <20.0 mass%,
0.5 ≦ Fe <5.0 mass%, and
0.5 <Al <5.0 mass%
And the balance is made of Ti and inevitable impurities.
本発明では、Ｍｎをβ安定化元素として用いている。Ｍｎは、Ｖに比べて安価であるため材料自体も低コストである。また、成分元素を最適化すると、溶体化処理後の強度は、Ｔｉ−６Ａｌ−４Ｖ合金と同等となる。さらに、Ｍｎ添加により加工硬化能が上昇するため、冷間加工性が向上し、高強度も得られる。 In the present invention, Mn is used as a β stabilizing element. Since Mn is cheaper than V, the material itself is also low in cost. Further, when the component elements are optimized, the strength after the solution treatment is equivalent to that of the Ti-6Al-4V alloy. Furthermore, since the work hardening ability is increased by the addition of Mn, the cold workability is improved and high strength is also obtained.
以下に、本発明の一実施の形態について詳細に説明する。
［１． β型チタン合金］
本発明に係るβ型チタン合金は、以下のような元素を含み、残部がＴｉ及び不可避的不純物からなる。添加元素の種類、その成分範囲、及び、その限定理由は、以下の通りである。
Hereinafter, an embodiment of the present invention will be described in detail.
[1. β-type titanium alloy]
The β-type titanium alloy according to the present invention contains the following elements, with the balance being Ti and inevitable impurities. The kind of additive element, its component range, and the reason for limitation are as follows.
［１．１． 主構成元素］
（１）８．０＜Ｍｎ＜２０．０ｍａｓｓ％：
Ｍｎは、β型チタン合金で一般的にβ相を安定化させるために添加されている元素（Ｍｏ、Ｖなど）と同様に、β相を安定化させる。加えて、Ｍｎは、Ｍｏ、Ｖ、Ｃｒなどのこれまでに使用されてきた合金元素に比べて、地殻中の存在比率が高い。すなわち、Ｍｎは、合金価格が安定して安く、入手性に優れている。β相を安定化させるためには、Ｍｎ含有量は、８．０ｍａｓｓ％超である必要がある。Ｍｎ含有量は、さらに好ましくは、１０．０ｍａｓｓ％以上である。
一方、Ｍｎ含有量が過剰になると、冷間加工性が低下する。従って、Ｍｎ含有量は、２０．０ｍａｓｓ％未満である必要がある。
[1.1. Main constituent elements]
(1) 8.0 <Mn <20.0 mass%:
Mn stabilizes the β phase in the same manner as elements (Mo, V, etc.) that are generally added to stabilize the β phase in the β-type titanium alloy. In addition, Mn has a higher abundance ratio in the crust than alloy elements that have been used so far, such as Mo, V, and Cr. That is, Mn has a stable and inexpensive alloy price and is highly available. In order to stabilize the β phase, the Mn content needs to be more than 8.0 mass%. The Mn content is more preferably 10.0 mass% or more.
On the other hand, when the Mn content is excessive, cold workability is lowered. Therefore, the Mn content needs to be less than 20.0 mass%.
（２）０．５≦Ｆｅ＜５．０ｍａｓｓ％：
Ｆｅは、Ｍｎと同様にβ相を安定化させるとともに、固溶強化により強度を高める。加えて、添加元素として安価であり、Ｆｅを多く含む、より低廉なＴｉ原料を使用することができ、結果として作製する合金の価格を抑制することができる。そのためには、Ｆｅ含有量は、０．５ｍａｓｓ％以上である必要がある。ＳＴ状態での引張強度を高めるためには、Ｆｅ含有量は、１．０ｍａｓｓ％以上が好ましい。
一方、Ｆｅ含有量が過剰になると、脆い金属間化合物が生成する。従って、Ｆｅ含有量は、５．０ｍａｓｓ％未満である必要がある。Ｆｅ含有量は、さらに好ましくは、２．０ｍａｓｓ％以下である。
(2) 0.5 ≦ Fe <5.0 mass%:
Fe stabilizes the β phase in the same way as Mn, and increases the strength by solid solution strengthening. In addition, it is possible to use a cheaper Ti raw material that is inexpensive as an additive element and contains a large amount of Fe, and as a result, the price of the alloy to be manufactured can be suppressed. For that purpose, Fe content needs to be 0.5 mass% or more. In order to increase the tensile strength in the ST state, the Fe content is preferably 1.0 mass% or more.
On the other hand, when the Fe content is excessive, brittle intermetallic compounds are produced. Therefore, the Fe content needs to be less than 5.0 mass%. The Fe content is more preferably 2.0 mass% or less.
（３）０．５＜Ａｌ＜５．０ｍａｓｓ％：
Ａｌは、β相から生成する準安定相であるω相の生成を抑制する。ω相は脆性であり、多量に析出すると材料の靱延性を著しく損なう。ω相の生成を抑制するためには、Ａｌ含有量は、０．５ｍａｓｓ％超である必要がある。Ａｌ含有量は、さらに好ましくは、２．０ｍａｓｓ％以上である。
一方、Ａｌは、強力なα相安定化元素であり、多く添加すると溶体化処理後に室温でもβ単相を安定的に持ち来すことができなくなる。従って、Ａｌ含有量は、５．０ｍａｓｓ％未満である必要がある。
(3) 0.5 <Al <5.0 mass%:
Al suppresses the generation of the ω phase, which is a metastable phase generated from the β phase. The ω phase is brittle, and when it is precipitated in a large amount, the toughness of the material is significantly impaired. In order to suppress the formation of the ω phase, the Al content needs to be more than 0.5 mass%. The Al content is more preferably 2.0 mass% or more.
On the other hand, Al is a strong α-phase stabilizing element, and if added in a large amount, Al cannot stably bring the β single phase even at room temperature after the solution treatment. Therefore, the Al content needs to be less than 5.0 mass%.
［１．２． 副構成元素］
本発明に係るβ型チタン合金は、上述した主構成元素に加えて、さらに以下のいずれか１種以上の副構成元素をさらに含んでいても良い。
[1.2. Sub-constituent elements]
The β-type titanium alloy according to the present invention may further contain any one or more of the following sub-constituent elements in addition to the main constituent elements described above.
（４）Ｃ＜０．１ｍａｓｓ％：
（５）Ｎ＜０．１ｍａｓｓ％：
Ｃ、Ｎは、いずれも固溶強化元素であり、β相に固溶してβ相を固溶強化させる。このような効果を得るためには、Ｃ含有量は、０．０１ｍａｓｓ％以上が好ましい。
同様に、Ｎ含有量は、０．０１ｍａｓｓ％以上が好ましい。
(4) C <0.1 mass%:
(5) N <0.1 mass%:
C and N are both solid solution strengthening elements, and solid dissolve in the β phase to strengthen the β phase. In order to obtain such an effect, the C content is preferably 0.01 mass% or more.
Similarly, the N content is preferably 0.01 mass% or more.
一方、これらの元素の含有量が過剰になると、炭化物、窒化物、又は、炭窒化物の生成を促進し、機械的特性の低下要因となる。従って、Ｃ含有量は、０．１ｍａｓｓ％未満が好ましい。
同様に、Ｎ含有量は、０．１ｍａｓｓ％未満が好ましい。
On the other hand, when the content of these elements is excessive, the formation of carbides, nitrides, or carbonitrides is promoted, resulting in a decrease in mechanical properties. Therefore, the C content is preferably less than 0.1 mass%.
Similarly, the N content is preferably less than 0.1 mass%.
（６）Ｈ＜０．０１ｍａｓｓ％：
Ｈは、β型チタン合金に固溶し、β型チタン合金の靱性を著しく低下させる。従って、Ｈ含有量は、０．０１ｍａｓｓ％未満が好ましい。
(6) H <0.01 mass%:
H dissolves in the β-type titanium alloy and significantly reduces the toughness of the β-type titanium alloy. Therefore, the H content is preferably less than 0.01 mass%.
（７）Ｚｒ＜５．０ｍａｓｓ％：
（８）Ｓｎ＜５．０ｍａｓｓ％：
Ｚｒ、Ｓｎは、いずれもＡｌと同様に、ω相の生成を抑制し、かつ、固溶強化元素として働く。Ａｌに代えてこれら元素を添加することができるが、元素ｍの含有量をＸm（ｍａｓｓ％）としたとき、Ａｌ当量＝ＸAl＋（ＸSn／３）＋（ＸZr／６）の関係式を満たす量が０．５超となるようにする。
(7) Zr <5.0 mass%:
(8) Sn <5.0 mass%:
Zr and Sn, like Al, suppress the generation of the ω phase and work as a solid solution strengthening element. These elements can be added in place of Al. When the content of the element m is X m (mass%), Al equivalent = X Al + (X Sn / 3) + (X Zr / 6) The amount satisfying the relational expression is set to be more than 0.5.
一方、これらの元素の含有量が過剰になると、溶体化処理後に室温でもβ単相を持ち来すことができなくなる。従って、Ｚｒ含有量は、５．０ｍａｓｓ％未満が好ましい。
同様に、Ｓｎ含有量は、５．０ｍａｓｓ％未満が好ましい。
さらに、Ａｌ当量が５．０未満となるように、Ｚｒ及び／又はＳｎを添加するのが好ましい。
On the other hand, when the content of these elements becomes excessive, it becomes impossible to bring the β single phase even at room temperature after the solution treatment. Therefore, the Zr content is preferably less than 5.0 mass%.
Similarly, the Sn content is preferably less than 5.0 mass%.
Furthermore, it is preferable to add Zr and / or Sn so that the Al equivalent is less than 5.0.
（９）Ｓｉ＜５．０ｍａｓｓ％：
Ｓｉは、β型チタン合金の耐酸化性を向上させる。このような効果を得るためには、Ｓｉ含有量は、０．５ｍａｓｓ％以上が好ましい。
一方、Ｓｉ含有量が過剰になると、シリサイドの生成を促進し、機械的特性の低下要因となる。従って、Ｓｉ含有量は、５．０ｍａｓｓ％未満が好ましい。
(9) Si <5.0 mass%:
Si improves the oxidation resistance of the β-type titanium alloy. In order to obtain such an effect, the Si content is preferably 0.5 mass% or more.
On the other hand, when the Si content is excessive, the formation of silicide is promoted, which causes a decrease in mechanical properties. Therefore, the Si content is preferably less than 5.0 mass%.
［１．３． 溶体化処理］
上述した組成となるように配合された原料を溶解・鋳造し、得られた鋳塊に対して溶体化処理を行うと、室温でも安定なβ単相からなる組織を得ることができる。溶体化処理は、鋳塊を所定の温度で保持し、急冷することにより行う。
[1.3. Solution treatment]
When the raw materials blended so as to have the above-described composition are melted and cast, and the resulting ingot is subjected to a solution treatment, a structure composed of a β single phase that is stable even at room temperature can be obtained. The solution treatment is performed by holding the ingot at a predetermined temperature and rapidly cooling it.
βトランザス温度（α＋βの二相領域とβ相単相領域の境界温度）は、偏析等の影響で部分的にばらつく。そのため、溶体化処理の温度が低すぎると、β単相からなる合金は得られない。従って、溶体化処理の温度は、βトランザス温度＋５℃以上が好ましい。
一方、溶体化処理の温度が高すぎると、結晶粒が成長し、機械的特性が低下する。従って、溶体化処理の温度は、βトランザス温度＋５０℃以下が好ましい。
β transus temperature (boundary temperature between α + β two-phase region and β-phase single-phase region) varies partially due to the influence of segregation or the like. Therefore, if the solution treatment temperature is too low, an alloy composed of a β single phase cannot be obtained. Therefore, the solution treatment temperature is preferably β transus temperature + 5 ° C. or higher.
On the other hand, if the temperature of the solution treatment is too high, crystal grains grow and the mechanical properties deteriorate. Accordingly, the solution treatment temperature is preferably β transus temperature + 50 ° C. or less.
急冷方法及び急冷条件は、高温安定相であるβ相を室温まで持ち来すことができる限りにおいて、特に限定されない。急冷方法としては、例えば、水焼き入れ、油焼き入れ、空気又はガスによる空冷などがある。 The rapid cooling method and rapid cooling conditions are not particularly limited as long as the β phase, which is a high-temperature stable phase, can be brought to room temperature. Examples of the rapid cooling method include water quenching, oil quenching, air cooling with air or gas.
［１．４． 冷間加工］
β型チタン合金は、室温での塑性変形能に優れるため、溶体化処理によりβ単相とした後、冷間加工により線材、帯材などに加工することができる。また、Ｍｎを添加したβ型チタン合金は、加工硬化が大きいため、冷間加工により高い強度を得ることができる。一般に、冷間加工の加工率が大きくなるほど、高い強度が得られる。
ここで、「加工率（％）」とは、冷間加工前の断面積（Ｓ0）に対する冷間加工後の断面積（Ｓ）の変化量の割合（＝|Ｓ−Ｓ0|×１００／Ｓ0）をいう。
[1.4. Cold working]
Since the β-type titanium alloy is excellent in plastic deformability at room temperature, it can be processed into a wire material, a strip, or the like by cold working after forming a β single phase by solution treatment. Moreover, since the β-type titanium alloy to which Mn is added has a large work hardening, a high strength can be obtained by cold working. In general, the higher the working rate of cold working, the higher the strength.
Here, the “working rate (%)” is the ratio of the amount of change in the cross-sectional area (S) after cold working to the cross-sectional area (S 0 ) before cold working (= | S−S 0 | × 100 / S 0 ).
高い強度を得るためには、加工率は、５％以上が好ましい。
一方、加工率が高すぎると、高強度化する代わりに延性が低下し、塑性加工が困難となる。従って、加工率は、８０％以下が好ましい。
In order to obtain high strength, the processing rate is preferably 5% or more.
On the other hand, if the processing rate is too high, the ductility decreases instead of increasing the strength, and plastic processing becomes difficult. Therefore, the processing rate is preferably 80% or less.
［２． β型チタン合金の製造方法］
本発明に係るβ型チタン合金の製造方法は、溶解・鋳造工程と、溶体化処理工程と、冷間加工工程とを備えている。
[2. Method for producing β-type titanium alloy]
The method for producing a β-type titanium alloy according to the present invention includes a melting / casting step, a solution treatment step, and a cold working step.
［２．１． 溶解・鋳造工程］
まず、本発明に係るβ型チタン合金となるように配合された原料を溶解及び鋳造する（溶解・鋳造工程）。
本発明に係るβ型チタン合金は、必須の元素としてＦｅを含んでいるので、Ｔｉ源には、高純度のスポンジチタンだけでなく、０．１〜２．０ｍａｓｓ％のＦｅを含む低純度のスポンジチタンを用いることができる。
配合された原料の溶解・鋳造方法は、特に限定されるものではなく、周知の方法を用いることができる。
[2.1. Melting / casting process]
First, a raw material blended so as to be a β-type titanium alloy according to the present invention is melted and cast (melting / casting process).
Since the β-type titanium alloy according to the present invention contains Fe as an essential element, the Ti source includes not only high-purity sponge titanium but also low-purity containing 0.1 to 2.0 mass% Fe. Sponge titanium can be used.
The method for melting and casting the blended raw material is not particularly limited, and a known method can be used.
［２．２． 溶体化処理工程］
次に、必要に応じて、得られた鋳塊を溶体化処理する（溶体化処理工程）。適切な溶体化処理を行うと、β単相のチタン合金が得られる。好適な溶体化処理の条件は、上述した通りであるので、説明を省略する。
[2.2. Solution treatment process]
Next, if necessary, the obtained ingot is subjected to a solution treatment (solution treatment step). When an appropriate solution treatment is performed, a β single phase titanium alloy is obtained. Since the suitable solution treatment conditions are as described above, description thereof is omitted.
［２．３． 冷間加工工程］
次に、必要に応じて、溶体化処理後の材料を冷間加工する（冷間加工工程）。溶体化処理後に適切な冷間加工を行うと、加工硬化により高強度化する。好適な冷間加工の条件は、上述した通りであるので、説明を省略する。
[2.3. Cold working process]
Next, if necessary, the material after the solution treatment is cold worked (cold working step). When an appropriate cold working is performed after the solution treatment, the strength is increased by work hardening. Since the suitable cold working conditions are as described above, description thereof is omitted.
［３． 作用］
本発明では、Ｍｎをβ安定化元素として用いている。Ｍｎは、Ｖに比べて安価であるため材料自体も低コストである。また、成分元素を最適化すると、溶体化処理後の強度は、Ｔｉ−６Ａｌ−４Ｖ合金と同等となる。さらに、Ｍｎ添加により加工硬化能が上昇するため、冷間加工性が向上し、高強度も得られる。
[3. Action]
In the present invention, Mn is used as a β stabilizing element. Since Mn is cheaper than V, the material itself is also low in cost. Further, when the component elements are optimized, the strength after the solution treatment is equivalent to that of the Ti-6Al-4V alloy. Furthermore, since the work hardening ability is increased by the addition of Mn, the cold workability is improved and high strength is also obtained.
（実施例１〜１６、比較例１〜５）
［１． 試料の作製］
表１に示す組成となるように配合された原料をコールドクルーシブル半浮遊溶解炉で溶製し、１０ｋｇのインゴットを得た。溶製したインゴットをφ３０ｍｍの棒材に鍛造加工した。次いで、鍛造加工した材料について、７００〜９００℃で溶体化処理（ＳＴ）を行った。さらに、ＳＴ後の丸棒を５０％の加工率で押し出し加工した。
(Examples 1-16, Comparative Examples 1-5)
[1. Preparation of sample]
The raw materials blended to have the composition shown in Table 1 were melted in a cold crucible semi-floating melting furnace to obtain 10 kg of ingot. The melted ingot was forged into a rod of φ30 mm. Subsequently, the forged material was subjected to a solution treatment (ST) at 700 to 900 ° C. Furthermore, the round bar after ST was extruded at a processing rate of 50%.
［２． 試験方法］
［２．１． 組織の同定］
ＳＴ後の素材よりミクロ組織の観察用試料を作製した。フッ酸を用いて試料の観察面をエッチングした後、光学顕微鏡を用いて観察した。
［２．２． Ｘ線回折］
ＳＴ後の素材より１０×１０×２ｍｍの試料を切り出し、Ｘ線回折パターンを測定した。
[2. Test method]
[2.1. Tissue Identification]
A sample for observing the microstructure was prepared from the material after ST. After etching the observation surface of the sample using hydrofluoric acid, the sample was observed using an optical microscope.
[2.2. X-ray diffraction]
A 10 × 10 × 2 mm sample was cut out from the material after ST, and the X-ray diffraction pattern was measured.
［２．３． 冷間圧縮試験］
ＳＴ後の素材を直径φ１５ｍｍ、高さ２２．５ｍｍの円柱に加工した。円柱状試料に対し、インストロン型試験機を用いて圧縮試験を行った。試験応力、歪量、及び、試験片の割れ状態を測定及び観察した。
［２．４． 引張試験］
ＳＴ後及び冷間加工後の素材から、それぞれ、ＪＩＳ Ｇ ０５６７に準拠した試験片（平行部径φ８ｍｍ、評点間距離４０ｍｍ）を作製した。この試験片に対し、室温にて引張試験を行い、０．２％耐力及び引張強度を測定した。
[2.3. Cold compression test]
The material after ST was processed into a cylinder having a diameter of 15 mm and a height of 22.5 mm. The cylindrical sample was subjected to a compression test using an Instron type testing machine. The test stress, the strain amount, and the cracked state of the test piece were measured and observed.
[2.4. Tensile test]
From the material after ST and after cold working, test pieces (parallel part diameter φ8 mm, distance between grades 40 mm) in accordance with JIS G 0567 were prepared. The test piece was subjected to a tensile test at room temperature, and 0.2% proof stress and tensile strength were measured.
［３． 結果］
表２に、結果を示す。表２より、以下のことがわかる。
（１）チタン合金において、α相は稠密六方格子結晶構造をなし、活動するすべり系がβ相に比べて少ないために、加工性はβ相に比較して劣る。これに対し、β相は体心立方格子結晶構造をなし、加工性に優れ、強度が高い。実施例の合金は、いずれもＳＴ状態でβ相の単相組織を呈しており、冷間加工性は良好であった。対して、比較例１はβ単相組織であったが、Ｍｎを多量に含有するため、硬さが高く、冷間加工時に割れを生じて加工性は劣位であった。比較例２〜５は、ＳＴ処理によりβ単相組織が得られず、α＋β組織であった。これらα＋β合金は、ＳＴ状態で非常に硬く、冷間加工が困難であった。
[3. result]
Table 2 shows the results. Table 2 shows the following.
(1) In a titanium alloy, the α phase has a dense hexagonal lattice crystal structure, and since the active slip system is less than the β phase, the workability is inferior to that of the β phase. In contrast, the β phase has a body-centered cubic lattice crystal structure, excellent workability, and high strength. The alloys of the examples all exhibited a β-phase single phase structure in the ST state, and the cold workability was good. On the other hand, Comparative Example 1 had a β single-phase structure, but contained a large amount of Mn, so the hardness was high, and cracking occurred during cold working, resulting in inferior workability. In Comparative Examples 2 to 5, a β single-phase structure was not obtained by ST treatment, and was an α + β structure. These α + β alloys were very hard in the ST state and were difficult to cold work.
（２）実施例の合金は、いずれも冷間加工後の強度が大きく向上している。従って、本発明は、合金価格が比較的安価で入手性の良いＭｎ及びＦｅを添加元素とし、かつ、Ｔｉ原料にも低廉なものを使用できることから、製造コストを抑えることができる。また、ＳＴ状態でβ相からなり、冷間加工性に優れると共に、冷間加工後に高い強度特性を有するＴｉ基合金を提供することができる。 (2) All the alloys of the examples have greatly improved strength after cold working. Therefore, the present invention can reduce the manufacturing cost because Mn and Fe, which are relatively inexpensive and easily available, can be used as additive elements and inexpensive Ti raw materials can be used. In addition, it is possible to provide a Ti-based alloy that is composed of a β phase in the ST state, has excellent cold workability, and has high strength characteristics after cold work.
（３）実施例１と実施例８は、Ｍｎ量及びＡｌ量が同等で、Ｆｅ量が異なる。また、Ｆｅ量の相違に起因してＳＴ状態の引張強度が相違する。表２より、ＳＴ状態における引張強度を向上させるためには、Ｆｅ含有量を１．０ｍａｓｓ％以上とするのが好ましいことがわかる。 (3) Example 1 and Example 8 have the same amount of Mn and Al, but differ in the amount of Fe. In addition, the tensile strength in the ST state differs due to the difference in the amount of Fe. Table 2 shows that in order to improve the tensile strength in the ST state, the Fe content is preferably set to 1.0 mass% or more.
以上、本発明の実施の形態について詳細に説明したが、本発明は、上記実施の形態に何ら限定されるものではなく、本発明の要旨を逸脱しない範囲内で種々の改変が可能である。 The embodiment of the present invention has been described in detail above, but the present invention is not limited to the above embodiment, and various modifications can be made without departing from the scope of the present invention.
本発明に係るβ型チタン合金は、ゴルフクラブヘッド、化学工業装置、電気機器、宇宙機器、航空機、船舶、車両、医療器、復水器、熱交換器、海水淡水化装置などに用いられる各種構造用部品、耐食用部品等に用いることができる。 The β-type titanium alloy according to the present invention is variously used for golf club heads, chemical industrial equipment, electrical equipment, space equipment, airplanes, ships, vehicles, medical equipment, condensers, heat exchangers, seawater desalination equipment, etc. It can be used for structural parts, corrosion resistant parts and the like.
Claims (7)
０．５≦Ｆｅ＜５．０ｍａｓｓ％、及び、
０．５＜Ａｌ＜５．０ｍａｓｓ％
を含み、残部がＴｉ及び不可避的不純物からなるβ型チタン合金。 8.0 <Mn <20.0 mass%,
0.5 ≦ Fe <5.0 mass%, and
0.5 <Al <5.0 mass%
Β-type titanium alloy comprising the balance of Ti and inevitable impurities.
Ｎ＜０．１ｍａｓｓ％
をさらに含む請求項１に記載のβ型チタン合金。 C <0.1 mass% and / or
N <0.1 mass%
The β-type titanium alloy according to claim 1, further comprising:
をさらに含む請求項１又は２に記載のβ型チタン合金。 H <0.01 mass%
The β-type titanium alloy according to claim 1 or 2, further comprising:
Ｓｎ＜５．０ｍａｓｓ％
をさらに含み、かつ、
元素ｍの含有量をＸm（ｍａｓｓ％）としたとき、Ａｌ当量＝ＸAl＋（ＸSn／３）＋（ＸZr／６）が０．５超５．０未満である
請求項１から３までのいずれか１項に記載のβ型チタン合金。 Zr <5.0 mass% and / or
Sn <5.0 mass%
And further including
The Al equivalent = X Al + (X Sn / 3) + (X Zr / 6) is more than 0.5 and less than 5.0 when the content of the element m is X m (mass%). The β-type titanium alloy according to any one of 3 to 3.
をさらに含む請求項１から４までのいずれか１項に記載のβ型チタン合金。 Si <5.0 mass%
The β-type titanium alloy according to any one of claims 1 to 4, further comprising:
得られた鋳塊をβトランザス温度＋５〜５０℃の温度で保持後、急冷する溶体化処理を行うことにより得られる請求項１から５までのいずれか１項に記載のβ型チタン合金。 Melting and casting the raw materials blended to the prescribed composition,
The β-type titanium alloy according to any one of claims 1 to 5, which is obtained by performing a solution treatment in which the obtained ingot is held at a temperature of β transus temperature + 5 to 50 ° C and then rapidly cooled.
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