JPH0754081A - High corrosion-resistant titanium alloy excellent in cold processibility and weldability - Google Patents
High corrosion-resistant titanium alloy excellent in cold processibility and weldabilityInfo
- Publication number
- JPH0754081A JPH0754081A JP19871693A JP19871693A JPH0754081A JP H0754081 A JPH0754081 A JP H0754081A JP 19871693 A JP19871693 A JP 19871693A JP 19871693 A JP19871693 A JP 19871693A JP H0754081 A JPH0754081 A JP H0754081A
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- Prior art keywords
- weldability
- alloy
- strength
- cold
- cold workability
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、化学工業（配管な
ど）、エネルギー開発（アンビリカルチューブ、石油開
発用油井管など）および航空機関連（油圧配管など）な
どで用いられる高耐食性チタン合金に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a highly corrosion-resistant titanium alloy used in the chemical industry (piping, etc.), energy development (umbilical tube, oil well pipe for oil development, etc.) and aircraft (hydraulic piping, etc.).
【０００２】[0002]
【従来の技術】チタンは比強度（強度／比重）が大き
く、耐食性に優れているという長所を持つ。従来、これ
らの長所を各々別個に改良する方向でチタン合金の開発
が行われてきた。これらの改良方法として、Al、Ｖ、Ni
などの元素を添加することが挙げられるが、冷間加工性
については十分な配慮が行われていない場合が多く、強
度や耐食性が改善されても冷間加工性を損ねることが多
かった。2. Description of the Related Art Titanium has the advantages of high specific strength (strength / specific gravity) and excellent corrosion resistance. Conventionally, titanium alloys have been developed in the direction of individually improving these advantages. As methods for improving these, Al, V, Ni
However, in many cases, sufficient consideration was not given to cold workability, and cold workability was often impaired even if strength and corrosion resistance were improved.
【０００３】チタン合金は一般的に冷間加工性や溶接性
に乏しく、熱間加工後、機械加工で仕上げなければなら
ない場合が多い。しかし、チタン合金は切削性が悪く、
そのため製品歩留りの低下、切削の長時間化などにより
コスト高を招く。Titanium alloys generally have poor cold workability and weldability, and in many cases they must be finished by machining after hot working. However, titanium alloy has poor machinability,
As a result, the product yield is lowered and the cutting time is prolonged, resulting in higher costs.
【０００４】チタンおよびチタン合金の中で冷間加工が
可能な合金としては、α型チタンである純Ti、α＋β型
チタン合金であるTi−３Al− 2.5Ｖ、および多くのβ型
チタン合金が挙げられる。Among titanium and titanium alloys, alloys that can be cold worked include pure Ti which is α-type titanium, Ti-3Al-2.5V which is α + β-type titanium alloy, and many β-type titanium alloys. To be
【０００５】これらのうち、β型チタン合金は冷間加工
は可能であるものの、熱間における変形抵抗が大き
く、従来工程では製造が困難であり、高温域(100〜 4
00℃前後) で使用した場合には、α相やω相の析出によ
り脆化し、熱的安定性に欠ける、という問題がある。Of these, the β-type titanium alloy can be cold worked, but has a large deformation resistance in the hot state, is difficult to manufacture in the conventional process, and has a high temperature range (100 to 4).
When it is used at around 00 ° C), there is a problem that it becomes brittle due to the precipitation of α phase and ω phase and lacks thermal stability.
【０００６】Ti−３Al− 2.5Ｖは代表的な冷間加工可能
なα＋β型チタン合金であり、その基本的な成分はAlが
2.5〜3.5 重量％、Ｖが 2.0〜3.0 重量％である (この
合金はＡＭＳに規格化されている) 。この合金も純Tiと
同様に冷間加工は可能であるものの、多くの他のチタン
合金と比べて強度が低い上に耐食性も十分とは言えず、
実用的な用途が狭められている。Ti-3Al-2.5V is a typical cold workable α + β type titanium alloy, the basic component of which is Al
2.5-3.5% by weight and V 2.0-3.0% by weight (this alloy is standardized to AMS). Although this alloy can be cold worked like pure Ti, its strength is lower and corrosion resistance is not sufficient compared to many other titanium alloys.
Practical use is narrowed.
【０００７】特開昭50−25418 号公報には、Al、Zr、M
o、Ｖ、Cr、NiおよびFeを含有するチタン合金が示され
ているが、これは強度および破壊靱性向上を目的として
発明されたものであり、冷間加工性や溶接性について
は、ほとんどまたは全く検討されていない。Japanese Patent Laid-Open No. 25418/1975 discloses Al, Zr, M
A titanium alloy containing o, V, Cr, Ni and Fe is shown, but it was invented for the purpose of improving strength and fracture toughness, and it has little or no cold workability or weldability. Not considered at all.
【０００８】チタンは周知のように、耐食性に優れた材
料であるという長所を持つが、苛酷な腐食環境での使用
にはさらなる耐食性の向上が必要であり、用途によって
は高い強度も要求される。これらの要求に対して、例え
ば特開昭61−257448号公報には、Al、Ni、Zrなどを添加
し、NiとZrの複合作用により高い耐食性と高強度を付与
したチタン合金が開示されている。また、特開昭63−17
9033号公報には、Al、Ni、Moなどを添加し、高強度と高
耐食性を達成したチタン合金が開示されている。しか
し、これらのチタン合金では、冷間加工性と溶接性につ
いて十分な検討がなされていない。特に前者の発明で
は、冷間圧延の圧下率が30％のときの耳割れの発生程度
を冷間加工性良否の判断基準としている。しかし、この
30％という圧下率はかなり低い基準であって、さらに高
い圧下率の場合でも冷間加工性に優れたチタン合金は示
されていない。As is well known, titanium has an advantage that it is a material excellent in corrosion resistance, but further improvement in corrosion resistance is required for use in a severe corrosive environment, and high strength is also required for some applications. . To meet these requirements, for example, JP-A-61-257448 discloses a titanium alloy to which Al, Ni, Zr, etc. are added, and which has a high corrosion resistance and high strength due to the combined action of Ni and Zr. There is. In addition, JP-A-63-17
Japanese Patent No. 9033 discloses a titanium alloy to which high strength and high corrosion resistance are achieved by adding Al, Ni, Mo and the like. However, these titanium alloys have not been sufficiently examined for cold workability and weldability. In particular, in the former invention, the degree of occurrence of edge cracking when the reduction ratio of cold rolling is 30% is used as a criterion for determining the quality of cold workability. But this
The reduction rate of 30% is a fairly low standard, and even if the reduction rate is higher, a titanium alloy excellent in cold workability is not shown.
【０００９】特開平３−166350号公報および特開平３−
274238号公報には、β相安定化元素( Fe、Ni、Co、Cr、
Ｍo 、Ｖ )の添加によりβ相率を増加させて、高い冷間
加工性と固溶強化による強度向上を達成したチタン合金
が示されている。また本発明者らは、特開平５−117791
号公報において、Ti−３Al− 2.5Ｖ合金にNbを 0.1％以
上10.0％以下添加し、良好な冷間加工性を維持しながら
高強度と高靱性を有するチタン合金を開示した。しか
し、これらの発明では、耐食性および溶接性については
明らかとなっていない。Japanese Unexamined Patent Publication No. 3-166350 and Japanese Unexamined Patent Publication No. 3-166350
No. 274238 discloses a β-phase stabilizing element (Fe, Ni, Co, Cr,
It is shown that titanium alloys which increase the β phase ratio by adding Mo, V) and achieve high cold workability and strength improvement by solid solution strengthening. The inventors of the present invention have disclosed in Japanese Patent Laid-Open No. 5-117791.
In the publication, Nb is added to Ti-3Al-2.5V alloy in an amount of 0.1% or more and 10.0% or less, and a titanium alloy having high strength and high toughness while maintaining good cold workability is disclosed. However, in these inventions, the corrosion resistance and weldability have not been clarified.
【００１０】[0010]
【発明が解決しようとする課題】チタン合金は、高耐食
性、高比強度の特性を活かし、腐食環境用構造材として
用いることが期待されている。しかし、多くのチタン合
金は苛酷な腐食環境での使用に耐え得る耐食性があると
は言い難い。また、一般的に冷間加工性と溶接性に乏し
いためにチタン合金を構造材として使用する場合、熱間
仕上げの状態から機械加工によって製品を製造する必要
がある。そのため、製品歩留りの低下とコスト上昇を招
いている。Titanium alloys are expected to be used as structural materials for corrosive environments by taking advantage of the characteristics of high corrosion resistance and high specific strength. However, it is hard to say that many titanium alloys have sufficient corrosion resistance to withstand use in harsh corrosive environments. Further, when a titanium alloy is used as a structural material because it is generally poor in cold workability and weldability, it is necessary to manufacture a product by machining from a state of hot finish. Therefore, the product yield is lowered and the cost is increased.
【００１１】本発明は、チタン合金から構造用部材を製
造する際の製品歩留りを向上させ、生産コストを低減す
るために、冷間加工性と溶接性にも優れた高耐食性チタ
ン合金を提供することを目的としてなされたものであ
る。The present invention provides a highly corrosion resistant titanium alloy excellent in cold workability and weldability in order to improve the product yield when manufacturing structural members from a titanium alloy and reduce the production cost. It was made for the purpose.
【００１２】具体的な目標は次の〜のとおりとし
た。The specific goals are as follows.
【００１３】冷間加工性は、後述の冷間加工性試験に
おいてTi−３Al− 2.5Ｖ合金以上であること。The cold workability should be Ti-3Al-2.5V alloy or more in the cold workability test described later.
【００１４】溶接性を示す室温の溶接部の0.2 ％耐力
が 600ＭＰa 以上であり、室温の母材部の0.2 ％耐力に
おいても 600ＭＰa 以上であること。The 0.2% proof stress of the welded portion at room temperature showing weldability is 600 MPa or more, and the 0.2% proof stress of the base material portion at room temperature is also 600 MPa or more.
【００１５】室温における溶接部の破断強度が母材部
のそれの90％以上であること。The fracture strength of the weld at room temperature is 90% or more of that of the base metal.
【００１６】構造材などに適用する実用面から、溶接
性を示す伸びについても下限値を設け、室温での母材部
と溶接部の引張伸びが、それぞれ10.0％以上、 5.0％以
上であること。From the viewpoint of practical application to structural materials, a lower limit is set for the elongation indicating weldability, and the tensile elongations of the base material and weld at room temperature are 10.0% or more and 5.0% or more, respectively. .
【００１７】後述の曲げ試験において溶接部に割れが
発生しないこと。No cracks occur in the welded portion in the bending test described later.
【００１８】耐食性は、後述の耐食性試験において純
チタンの倍以上であること。Corrosion resistance should be more than double that of pure titanium in the corrosion resistance test described later.
【００１９】[0019]
【課題を解決するための手段】本発明者らは種々の添加
元素が冷間加工性、強度、溶接性および耐食性に与える
影響を検討し、耐食性と冷間加工性、強度および溶接性
を高度にバランスさせたチタン合金を開発した。[Means for Solving the Problems] The present inventors have examined the effects of various additive elements on cold workability, strength, weldability and corrosion resistance, and have made it possible to improve the corrosion resistance and cold workability, strength and weldability. We have developed a balanced titanium alloy.
【００２０】本発明の要旨は次のチタン合金にある。The gist of the present invention lies in the following titanium alloys.
【００２１】(1)重量％で、Al： 1.5〜4.5 ％、Ｖ： 1.
5〜4.5 ％およびMo： 0.1％〜2.5 ％未満を含有し、残
部はTiおよび不可避的不純物からなる冷間加工性および
溶接性に優れた高耐食性チタン合金。(1) Al: 1.5 to 4.5% by weight, V: 1.
5 to 4.5% and Mo: 0.1% to less than 2.5%, with the balance being Ti and inevitable impurities, a highly corrosion resistant titanium alloy with excellent cold workability and weldability.
【００２２】(2)上記(1) 記載の成分に加えてさらに、
重量％で、Zr： 0.1〜10.0％を含有し、残部はTiおよび
不可避的不純物からなる冷間加工性および溶接性に優れ
た高耐食性チタン合金。(2) In addition to the components described in (1) above,
A highly corrosion-resistant titanium alloy containing 0.1 to 10.0% by weight of Zr and the balance of Ti and unavoidable impurities and having excellent cold workability and weldability.
【００２３】[0023]
【作用】本発明のチタン合金は、TiにAl、ＶおよびMoを
数％添加し、さらに必要に応じてZrを添加し、さらなる
強度、冷間加工性および溶接性の向上を図ったものであ
る。化学組成を前記のように限定した理由について説明
する。以下、％は重量％を意味する。The titanium alloy of the present invention is obtained by adding a few% of Al, V and Mo to Ti and further adding Zr if necessary to further improve strength, cold workability and weldability. is there. The reason for limiting the chemical composition as described above will be described. Hereinafter,% means% by weight.
【００２４】Al： 1.5〜4.5 ％ Alはα相安定化元素である。固溶強化と耐食性向上の目
的で含有させるが、目標の強度と耐食性を得るには、Al
を1.5 ％以上含有させる必要がある。一方、Al含有量が
4.5 ％を超えると冷間加工性が低下するために、冷間加
工時に割れを生じる。よって、Al含有量の範囲は1.5 〜
4.5％とした。好ましいのは2.5 〜 3.5％の範囲であ
る。Al: 1.5 to 4.5% Al is an α-phase stabilizing element. Although it is contained for the purpose of solid solution strengthening and corrosion resistance improvement, in order to obtain the target strength and corrosion resistance, Al
Must be contained in an amount of 1.5% or more. On the other hand, if the Al content is
If it exceeds 4.5%, the cold workability deteriorates, so that cracking occurs during cold work. Therefore, the Al content range is 1.5-
It was set to 4.5%. The preferred range is 2.5 to 3.5%.
【００２５】Ｖ： 1.5〜4.5 ％ Ｖはβ相安定化元素である。固溶強化の目的で含有させ
るが、目標強度を得るには1.5 ％以上含有させる必要が
ある。一方、Ｖ含有量が4.5 ％を超えると冷間加工性と
耐食性を劣化させる。よって、Ｖ含有量の範囲は 1.5〜
4.5 ％とした。V: 1.5-4.5% V is a β-phase stabilizing element. Although it is contained for the purpose of solid solution strengthening, it is necessary to contain 1.5% or more to obtain the target strength. On the other hand, if the V content exceeds 4.5%, the cold workability and corrosion resistance deteriorate. Therefore, the range of V content is 1.5-
It was set to 4.5%.
【００２６】好ましいのは 2.5〜3.5 ％の範囲である。
またＶは、Moと同様に溶接性を劣化させる元素である
が、その程度はMoに比べて小さく、上記の範囲内であれ
ば問題はない。The preferred range is 2.5-3.5%.
Further, V is an element that deteriorates weldability like Mo, but the degree thereof is smaller than that of Mo, and there is no problem if it is within the above range.
【００２７】Mo： 0.1％〜2.5 ％未満 Moは冷間加工性、強度および耐食性の向上に寄与する
が、Mo含有量が0.1 ％未満ではその効果は小さい。しか
し、Moを多量に含有させると、溶接性が劣化し、また高
融点金属であるため偏析を生じる懸念があること、伸び
が低下することなどを考慮すると、Mo含有量は2.5 ％未
満に抑えるべきである。このため、Mo含有量の範囲は0.
1 ％〜2.5 ％未満とした。好ましい下限は0.8 ％であ
る。Mo: 0.1% to less than 2.5% Mo contributes to the improvement of cold workability, strength and corrosion resistance, but if the Mo content is less than 0.1%, its effect is small. However, if a large amount of Mo is contained, weldability deteriorates, and since it is a refractory metal, segregation may occur, and elongation may decrease, so the Mo content should be kept below 2.5%. Should be. Therefore, the Mo content range is 0.
It was set to 1% to less than 2.5%. A preferable lower limit is 0.8%.
【００２８】なお、ＶとMoは単体の金属として添加して
もよいが、Al−Ｖ母合金、Al−Mo母合金またはAl−Mo−
Ｖ母合金という形で添加してもよい。Although V and Mo may be added as simple metals, they are Al-V master alloy, Al-Mo master alloy or Al-Mo-.
You may add in the form of V mother alloy.
【００２９】Zr： 0.1〜10.0％ Zrは、耐食性、冷間加工性および強度の向上に寄与し、
特に冷間加工性の向上効果が大きい元素である（後述の
図２参照）から、必要に応じて含有させる。Zr含有量が
0.1 ％未満ではその効果は小さい。一方、10.0％を超え
ると耐食性と強度は上昇するが、伸び、冷間加工性およ
び溶接性が著しく劣化する。このために、Zrを含有させ
る場合の範囲は 0.1〜10.0％とすべきである。好ましい
のは 0.5〜7.0 ％の範囲である。Zr: 0.1-10.0% Zr contributes to the improvement of corrosion resistance, cold workability and strength,
In particular, since it is an element that has a great effect of improving cold workability (see FIG. 2 described later), it is contained if necessary. Zr content is
If it is less than 0.1%, the effect is small. On the other hand, if it exceeds 10.0%, the corrosion resistance and strength increase, but the elongation, cold workability and weldability deteriorate significantly. For this reason, the range when Zr is contained should be 0.1 to 10.0%. The preferred range is 0.5 to 7.0%.
【００３０】その他：不可避的な不純物とは、Ｃ、Ｈ、
Ｏ、Ｎ、FeおよびＹなどを指すが、通常の含有量レベル
であれば特に問題はない。Others: Inevitable impurities include C, H,
It refers to O, N, Fe, Y and the like, but there is no particular problem as long as it is a normal content level.
【００３１】Feは、スポンジTiや添加元素原料に幾分か
含まれているため、不可避的に混入するが、0.5 ％以下
であれば問題はない。Feは固溶強化度が大きく、少量で
も強度向上に寄与するが、その含有量が0.5 ％を超える
と、Tiと反応して金属間化合物を生成し、冷間加工性を
著しく劣化させる。また、耐食性を劣化させたり、イン
ゴット中の偏析に起因するβフレック（Feのマクロ偏
析）の生成をもたらしたりするので好ましくない。その
ため、Fe含有量は0.5 ％以下とするのがよい。Since Fe is contained in sponge Ti and some of the additional element raw materials, Fe is inevitably mixed, but no problem occurs if it is 0.5% or less. Fe has a large degree of solid solution strengthening and contributes to the improvement of strength even with a small amount, but if its content exceeds 0.5%, it reacts with Ti to form an intermetallic compound, which significantly deteriorates the cold workability. Further, it is not preferable because it deteriorates the corrosion resistance and causes β-fleck (macrosegregation of Fe) due to segregation in the ingot. Therefore, the Fe content is preferably 0.5% or less.
【００３２】Ｏも固溶強化度が大きく、少量でも強度向
上に寄与するが、その反面、冷間加工性を劣化させる。
そのため、Ｏ含有量は0.2 ％以下とすることが望まし
い。O also has a large degree of solid solution strengthening, and even a small amount contributes to the improvement of strength, but on the other hand, it deteriorates the cold workability.
Therefore, the O content is preferably 0.2% or less.
【００３３】上記の化学組成とすることで、前記の目標
とする強度、伸び、冷間加工性、溶接性および耐食性を
備えたチタン合金を得ることができる。With the above chemical composition, it is possible to obtain a titanium alloy having the above-mentioned target strength, elongation, cold workability, weldability and corrosion resistance.
【００３４】本発明の合金は、これらの特性によって腐
食環境用構造材などに適用することが可能であり、特に
溶接性、強度、冷間加工性および耐食性などが要求され
るアンビリカルチューブ用素材として好適である。アン
ビリカルチューブとは、海底の油田と海上のプラットホ
ームを結ぶ制御管のことであり、管中に油圧を制御する
電線などが通されるものである。The alloy of the present invention can be applied to a structural material for corrosive environment due to these characteristics, and particularly as a material for an umbilical tube which is required to have weldability, strength, cold workability and corrosion resistance. It is suitable. An umbilical tube is a control pipe that connects an oil field on the sea floor and a platform on the sea, and an electric wire for controlling hydraulic pressure is passed through the pipe.
【００３５】[0035]
【実施例】表１と表２に示す組成の合金を真空溶解法に
よって溶製し、直径 120mm×長さ300mm の円柱状インゴ
ットとした。表１の合金 No.１〜13が本発明例、表２の
合金 No.14〜22が本発明範囲外の組成の比較例、表２の
合金 No.23、24が既存の冷間加工可能な純Ti、Ti−３Al
− 2.5Ｖ合金である。EXAMPLE Alloys having the compositions shown in Tables 1 and 2 were melted by a vacuum melting method to obtain a cylindrical ingot having a diameter of 120 mm and a length of 300 mm. Alloy Nos. 1 to 13 in Table 1 are examples of the present invention, Alloys Nos. 14 to 22 in Table 2 are comparative examples having compositions outside the scope of the present invention, and Alloys Nos. 23 and 24 in Table 2 are existing cold workable. Pure Ti, Ti-3Al
-2.5V alloy.
【００３６】[0036]
【表１】 [Table 1]
【００３７】[0037]
【表２】 [Table 2]
【００３８】これらのインゴットを1100℃に加熱した
後、 850℃以上で鍛造を行い、厚さ60mm×幅70mm×長さ
680mm の角状とした。その後、熱間圧延(900℃加熱、 7
50℃打ち上げ) を施して厚さ15mm×幅70mmの板材にした
後、 750℃で焼鈍を行った。After heating these ingots to 1100 ° C., they are forged at 850 ° C. or higher, and the thickness is 60 mm × width 70 mm × length.
It has a 680 mm square shape. After that, hot rolling (900 ℃ heating, 7
(Up to 50 ° C) was applied to form a plate material having a thickness of 15 mm and a width of 70 mm, and then annealed at 750 ° C.
【００３９】熱間加工性の評価は、上記の熱間鍛造、熱
間圧延によって割れが生じた場合を熱間加工性が劣悪
「×」、割れが生じない場合を良好「○」とした。In the evaluation of hot workability, the hot workability was poor when the crack was generated by the above-mentioned hot forging and hot rolling, and "Good" when the crack was not generated.
【００４０】このようにして得られた各供試材から、冷
間圧延試験片 (厚さ12mm×幅35mm×長さ200mm)と冷間据
え込み加工試験片 (φ６mm×長さ９mm) および塩酸腐食
試験片 (厚さ10mm×幅20mm×長さ20mm) を切り出し、冷
間加工性と耐食性の各試験に供した。From each of the test materials thus obtained, a cold rolling test piece (12 mm thick x 35 mm wide x 200 mm long), a cold upsetting test piece (φ6 mm x 9 mm long) and hydrochloric acid were used. A corrosion test piece (thickness 10 mm x width 20 mm x length 20 mm) was cut out and subjected to each test of cold workability and corrosion resistance.
【００４１】また、熱間圧延後の板材から切り出した供
試材 (厚さ３mm×幅70mm) に、ＴＩＧ溶接 (Ar雰囲気
中、両面各１パス、溶接棒も熱間圧延後の板材から切り
出したもの) を行った後、溶接部と母材部からそれぞれ
平行部寸法：厚さ２mm×幅6.25mm×長さ32mmの板引張試
験片を切り出し、引張強度を測定した。さらに各供試材
の溶接部の曲げ加工性を調べるために曲げ試験片 (厚さ
２mm×幅15mm×長さ100mm)を切り出し、曲げ試験を実施
した。In addition, TIG welding (1 pass each on both sides in Ar atmosphere, welding rod was also cut from the sheet material after hot rolling to a test material (thickness 3 mm × width 70 mm) cut from the sheet material after hot rolling. Test piece), a plate tensile test piece having dimensions of parallel part: thickness 2 mm x width 6.25 mm x length 32 mm was cut out from the welded part and the base metal part, and the tensile strength was measured. Further, a bending test piece (thickness 2 mm × width 15 mm × length 100 mm) was cut out and a bending test was conducted in order to examine the bending workability of the welded portion of each test material.
【００４２】次に各試験の詳細な内容について述べる。Next, the detailed contents of each test will be described.
【００４３】〔冷間圧延試験〕厚さ12mm×幅35mm×長さ
200mm の前記試験片を、ロールで１パスあたり 0.5mmづ
つ減厚し、板端部から３mm以上の長さの耳割れが板側面
に沿って５cm以内の間隔で生じた場合を限界冷間加工度
とし、下記 (1)式に従い算出した。[Cold Rolling Test] Thickness 12 mm × width 35 mm × length
The 200 mm test piece is reduced by 0.5 mm per pass with a roll, and the limit cold working is performed when edge cracks with a length of 3 mm or more from the plate edge occur at intervals of 5 cm or less along the plate side surface. Was calculated according to the following formula (1).
【００４４】[0044]
【数１】 [Equation 1]
【００４５】〔冷間据え込み加工試験〕φ６mm×長さ９
mmの前記試験片を、歪速度＝ 1.0×10-2 sec-1で加工フ
ォーマスター試験装置により冷間据え込み加工を行い、
割れが発生した加工度を限界冷間加工度とした。なお、
この据え込み加工試験は各合金につき３回試験を行い、
その平均値を限界冷間加工度とし、下記 (2)式に従い算
出した。[Cold upsetting processing test] φ6 mm × length 9
The above-mentioned test piece of mm is subjected to cold upsetting by a processing master tester at a strain rate of 1.0 × 10 -2 sec -1 ,
The workability at which cracks occurred was defined as the limit cold workability. In addition,
This upsetting test is done three times for each alloy,
The average value was used as the limit cold workability and calculated according to the following equation (2).
【００４６】[0046]
【数２】 [Equation 2]
【００４７】〔塩酸腐食試験〕厚さ10mm×幅20mm×長さ
20mmの前記試験片を、５重量％ＨCl沸騰溶液中に20時間
浸漬して腐食減量を測定し、腐食減量をmm／年に換算し
て耐食性を評価した。[Hydrochloric acid corrosion test] Thickness 10 mm x width 20 mm x length
The 20 mm test piece was immersed in a 5 wt% HCl boiling solution for 20 hours to measure the corrosion weight loss, and the corrosion weight loss was converted to mm / year to evaluate the corrosion resistance.
【００４８】〔引張試験〕母材部と溶接部から切り出し
た平行部寸法：厚さ２mm×幅6.25mm×長さ32mmの前記試
験片に、0.2 ％耐力までは 0.5％歪/min、耐力後は15％
歪/minの引張速度を与えて破断させ、強度を測定して溶
接性を評価した。この引張試験は室温で２回行い、平均
値で強度、伸びを比較した。[Tensile test] Parallel part dimension cut out from the base metal part and the welded part: 0.5% strain / min up to 0.2% proof stress, after proof stress on the above test piece of thickness 2 mm x width 6.25 mm x length 32 mm Is 15%
Weldability was evaluated by applying a tensile rate of strain / min to rupture and measuring the strength. This tensile test was performed twice at room temperature, and the average values were compared for strength and elongation.
【００４９】〔溶接部曲げ試験〕厚さ２mm×幅15mm×長
さ100mm の前記試験片を各供試材の溶接部から切り出
し、２mmの曲げ半径で90℃曲げを行った。曲げ試験後、
光学顕微鏡にて曲げ部の20倍観察を行い、割れの有無を
調査して溶接性を評価した。図１はこの試験片の形状を
示す図である。[Welding Bending Test] The above-mentioned test piece having a thickness of 2 mm, a width of 15 mm and a length of 100 mm was cut out from the welded portion of each test material and bent at a bending radius of 2 mm at 90 ° C. After the bending test,
The bent portion was observed 20 times with an optical microscope, and the presence or absence of cracks was investigated to evaluate the weldability. FIG. 1 is a view showing the shape of this test piece.
【００５０】以上の各評価試験の結果を表３、表４およ
び図２に示す。The results of the above evaluation tests are shown in Tables 3 and 4 and FIG.
【００５１】[0051]
【表３】 [Table 3]
【００５２】[0052]
【表４（１）】 [Table 4 (1)]
【００５３】[0053]
【表４（２）】 [Table 4 (2)]
【００５４】表３、表４の結果から以下のことが明らか
である。From the results of Tables 3 and 4, the following is clear.
【００５５】合金 No.１〜３および No.14、15の結果に
よれば、Alは固溶強化による強度向上に大きく寄与する
が、含有量が少ないとその効果は小さい (合金 No.14で
は、Alは0.5 ％であり強度が低い) 。また、過度のAl含
有は冷間加工性を低下させる( 合金No.15 では同じく6.
0 ％であり冷間加工性が劣悪 )。According to the results of Alloy Nos. 1 to 3 and Nos. 14 and 15, Al greatly contributes to the strength improvement by solid solution strengthening, but the effect is small when the content is small (in Alloy No. 14, , Al is 0.5% and the strength is low). In addition, excessive Al content deteriorates cold workability (Alloy No. 15 also has 6.
0% and poor cold workability).
【００５６】合金 No.４、５および No.16、17の結果に
よれば、Ｖも固溶強化による強度向上に寄与する。しか
し、含有量が少ないとその効果は小さい (合金 No.16
では、Ｖは0.5 ％であり強度が低い) 。また、過度のＶ
含有は冷間加工性を低下させる (合金 No.17では、同じ
く6.0 ％であり、冷間加工性はTi-3Al-2.5Ｖ合金の場合
以下に低下している）。According to the results of Alloy Nos. 4 and 5 and Nos. 16 and 17, V also contributes to the strength improvement by solid solution strengthening. However, if the content is low, the effect is small (alloy No. 16
Then, V is 0.5% and the strength is low). Also, excessive V
The inclusion lowers the cold workability (in Alloy No. 17, it is also 6.0%, and the cold workability is lower than that in the case of Ti-3Al-2.5V alloy).
【００５７】Moは、合金 No.６、７および No.18、19の
結果によれば、冷間加工性、強度および耐食性の向上に
寄与することがわかる。しかし、合金 No.18の結果によ
れば、Mo含有量が 0.1％未満であると、上記の三種類の
特性の向上に対する寄与は小さい。また、過度のMo含有
は溶接性の低下をもたらし、好ましくない (合金 No.19
では、Moは4.0 ％であり溶接部の曲げ加工性が低い) 。According to the results of the alloys Nos. 6 and 7 and Nos. 18 and 19, Mo contributes to the improvement of cold workability, strength and corrosion resistance. However, according to the results of Alloy No. 18, if the Mo content is less than 0.1%, the contribution to the improvement of the above-mentioned three types of properties is small. In addition, excessive Mo content causes a decrease in weldability, which is not preferable (alloy No. 19
Then, Mo is 4.0% and bendability of the weld is low).
【００５８】合金 No.８、９および No.21の結果によれ
ば、酸素は強度向上に大きく寄与するものの、冷間加工
性と溶接性を低下させる。しかし、通常の量(0.2％以
下) なら問題はない。According to the results of Alloys Nos. 8, 9 and 21, although oxygen greatly contributes to the improvement of strength, it deteriorates cold workability and weldability. However, there is no problem with the normal amount (0.2% or less).
【００５９】合金 No.10、20の結果によれば、Feは酸素
と同様に強度に大きく影響を与え、冷間加工性に悪影響
を与える。また、耐食性も劣化させるが、Fe含有量が0.
5 ％以下なら問題はない。According to the results of Alloy Nos. 10 and 20, Fe has a great influence on the strength like oxygen, and has a bad influence on the cold workability. It also deteriorates corrosion resistance, but the Fe content is 0.
If it is 5% or less, there is no problem.
【００６０】図２は、冷間据え込み加工試験の場合の、
限界冷間加工度に及ぼすZr含有量の影響の例を示す図で
ある。この場合のチタン合金のベース組成は、Al:3.0
％、Ｖ:3.0％、Mo:1.5％、Ｏ:0.1％、Fe:0.1％、bal.:T
i である。図示するように、Zr含有量が本発明で定める
範囲で限界冷間加工度が高くなる。FIG. 2 shows a cold upsetting test.
It is a figure which shows the example of the influence of Zr content which acts on the limit cold workability. The base composition of the titanium alloy in this case is Al: 3.0
%, V: 3.0%, Mo: 1.5%, O: 0.1%, Fe: 0.1%, bal.:T
i. As shown in the figure, the critical cold workability is high when the Zr content is in the range defined by the present invention.
【００６１】表３、表４および図２に示すように、合金
No.2、 No.11〜13および No.22の結果によれば、Zrは強
度、耐食性および冷間加工性の向上に寄与するが、過度
のZr含有 (例えば、合金 No.22ではZr:13 ％) は冷間加
工性、延びおよび溶接性を低下させる。しかし、本発明
で定める範囲内であれば冷間加工性と溶接性を損ねるこ
となく、強度と耐食性を向上させる効果がある。As shown in Tables 3 and 4 and FIG.
According to the results of No. 2, No. 11 to 13 and No. 22, Zr contributes to the improvement of strength, corrosion resistance and cold workability, but excessive Zr content (for example, alloy No. 22 has Zr: 13%) reduces cold workability, elongation and weldability. However, within the range defined by the present invention, there is an effect of improving strength and corrosion resistance without impairing cold workability and weldability.
【００６２】合金 No.23、24の既存の純TiやTi−３Al−
2.5Ｖ合金では、本発明合金に比べて強度が低く、耐食
性も悪い。Existing pure Ti and Ti-3Al-of alloy Nos. 23 and 24
The 2.5V alloy has lower strength and poorer corrosion resistance than the alloy of the present invention.
【００６３】[0063]
【発明の効果】本発明の合金は、冷間加工性および溶接
性（溶接部強度）にも優れた高強度高耐食性チタン合金
である。溶接性が良好であるから、機械切削によること
なく、化学工業、エネルギー開発、一般工業などの分野
の腐食環境雰囲気で用いるのに好適なチタン合金チュー
ブ材などを、低コストで製造することができる。The alloy of the present invention is a high strength and high corrosion resistance titanium alloy excellent in cold workability and weldability (welding strength). Since it has good weldability, it is possible to manufacture, at low cost, titanium alloy tube materials suitable for use in corrosive environment atmospheres in fields such as chemical industry, energy development, and general industry, without using mechanical cutting. .
【図１】溶接部曲げ試験の試験片形状を示す図である。FIG. 1 is a view showing a test piece shape of a welded portion bending test.
【図２】冷間据え込み加工試験の場合の、限界冷間加工
度に及ぼすZr含有量の影響の例を示す図である。FIG. 2 is a diagram showing an example of the effect of the Zr content on the critical cold workability in the case of a cold upsetting work test.
Claims (2)
4.5 ％およびMo： 0.1％〜2.5 ％未満を含有し、残部は
Tiおよび不可避的不純物からなる冷間加工性および溶接
性に優れた高耐食性チタン合金。1. By weight%, Al: 1.5-4.5%, V: 1.5-
4.5% and Mo: 0.1% to less than 2.5%, the balance
A highly corrosion resistant titanium alloy consisting of Ti and unavoidable impurities with excellent cold workability and weldability.
％で、Zr： 0.1〜10.0％を含有し、残部はTiおよび不可
避的不純物からなる冷間加工性および溶接性に優れた高
耐食性チタン合金。2. In addition to the components according to claim 1, Zr: 0.1-10.0% by weight is further included, and the balance is Ti and unavoidable impurities, which are excellent in cold workability and weldability. Corrosion resistant titanium alloy.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP19871693A JP2797913B2 (en) | 1993-08-11 | 1993-08-11 | High corrosion resistance titanium alloy with excellent cold workability and weldability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP19871693A JP2797913B2 (en) | 1993-08-11 | 1993-08-11 | High corrosion resistance titanium alloy with excellent cold workability and weldability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0754081A true JPH0754081A (en) | 1995-02-28 |
| JP2797913B2 JP2797913B2 (en) | 1998-09-17 |
Family
ID=16395824
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP19871693A Expired - Fee Related JP2797913B2 (en) | 1993-08-11 | 1993-08-11 | High corrosion resistance titanium alloy with excellent cold workability and weldability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2797913B2 (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0969109A1 (en) * | 1998-05-26 | 2000-01-05 | KABUSHIKI KAISHA KOBE SEIKO SHO also known as Kobe Steel Ltd. | Titanium alloy and process for production |
| WO2002090607A1 (en) * | 2001-05-07 | 2002-11-14 | Verkhnaya Salda Metallurgical Production Association | Titanium-base alloy |
| US6786985B2 (en) | 2002-05-09 | 2004-09-07 | Titanium Metals Corp. | Alpha-beta Ti-Ai-V-Mo-Fe alloy |
| CN104923968A (en) * | 2015-06-24 | 2015-09-23 | 宝鸡钛业股份有限公司 | Special Ti-6Al-3V welding wire for Ti-6Al-4V ELI titanium alloy and machining process of special Ti-6Al-3V welding wire |
| CN105316524A (en) * | 2014-08-04 | 2016-02-10 | 中国科学院金属研究所 | Ti-Al-Zr-Mo-V system medium-strength high-plasticity titanium alloy and preparation method thereof |
| CN106636742A (en) * | 2016-11-17 | 2017-05-10 | 中世钛业有限公司 | ZSA-3 titanium alloy pipe, and preparation method and application thereof |
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|---|---|---|---|---|
| CN111519067B (en) * | 2020-05-26 | 2021-11-09 | 西北有色金属研究院 | High-performance, low-cost and high-strength titanium alloy |
-
1993
- 1993-08-11 JP JP19871693A patent/JP2797913B2/en not_active Expired - Fee Related
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0969109A1 (en) * | 1998-05-26 | 2000-01-05 | KABUSHIKI KAISHA KOBE SEIKO SHO also known as Kobe Steel Ltd. | Titanium alloy and process for production |
| US6228189B1 (en) | 1998-05-26 | 2001-05-08 | Kabushiki Kaisha Kobe Seiko Sho | α+β type titanium alloy, a titanium alloy strip, coil-rolling process of titanium alloy, and process for producing a cold-rolled titanium alloy strip |
| USRE38316E1 (en) * | 1998-05-26 | 2003-11-18 | Kabushiki Kaisha Kobe Seiko Sho | α+β type titanium alloy, a titanium alloy strip, coil-rolling process of titanium alloy, and process for producing a cold-rolled titanium alloy strip |
| WO2002090607A1 (en) * | 2001-05-07 | 2002-11-14 | Verkhnaya Salda Metallurgical Production Association | Titanium-base alloy |
| US6786985B2 (en) | 2002-05-09 | 2004-09-07 | Titanium Metals Corp. | Alpha-beta Ti-Ai-V-Mo-Fe alloy |
| CN105316524A (en) * | 2014-08-04 | 2016-02-10 | 中国科学院金属研究所 | Ti-Al-Zr-Mo-V system medium-strength high-plasticity titanium alloy and preparation method thereof |
| CN105316524B (en) * | 2014-08-04 | 2017-11-28 | 中国科学院金属研究所 | Strong high-ductility titanium alloy and preparation method thereof in a kind of Ti Al Zr Mo V systems |
| CN104923968A (en) * | 2015-06-24 | 2015-09-23 | 宝鸡钛业股份有限公司 | Special Ti-6Al-3V welding wire for Ti-6Al-4V ELI titanium alloy and machining process of special Ti-6Al-3V welding wire |
| CN106636742A (en) * | 2016-11-17 | 2017-05-10 | 中世钛业有限公司 | ZSA-3 titanium alloy pipe, and preparation method and application thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2797913B2 (en) | 1998-09-17 |
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