JPS63223155A - Production of alpha+beta type titanium alloy extruded material - Google Patents
Production of alpha+beta type titanium alloy extruded materialInfo
- Publication number
- JPS63223155A JPS63223155A JP5526487A JP5526487A JPS63223155A JP S63223155 A JPS63223155 A JP S63223155A JP 5526487 A JP5526487 A JP 5526487A JP 5526487 A JP5526487 A JP 5526487A JP S63223155 A JPS63223155 A JP S63223155A
- Authority
- JP
- Japan
- Prior art keywords
- titanium alloy
- billet
- alpha
- type titanium
- toughness
- 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.)
- Pending
Links
- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 23
- 239000000463 material Substances 0.000 title claims abstract description 23
- 238000004519 manufacturing process Methods 0.000 title claims description 10
- 238000001125 extrusion Methods 0.000 claims abstract description 30
- 238000001816 cooling Methods 0.000 claims abstract description 16
- 230000009466 transformation Effects 0.000 claims abstract description 11
- 238000000137 annealing Methods 0.000 claims abstract description 9
- 238000010438 heat treatment Methods 0.000 abstract description 3
- 229910000734 martensite Inorganic materials 0.000 abstract description 3
- 238000000034 method Methods 0.000 abstract description 3
- 229910045601 alloy Inorganic materials 0.000 description 7
- 239000000956 alloy Substances 0.000 description 7
- 238000005242 forging Methods 0.000 description 6
- 239000000047 product Substances 0.000 description 6
- 229910000831 Steel Inorganic materials 0.000 description 3
- 235000012438 extruded product Nutrition 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 239000010959 steel Substances 0.000 description 3
- 238000000354 decomposition reaction Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 229910000883 Ti6Al4V Inorganic materials 0.000 description 1
- 238000003287 bathing Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 238000010301 surface-oxidation reaction Methods 0.000 description 1
Landscapes
- Extrusion Of Metal (AREA)
Abstract
Description
【発明の詳細な説明】
〈産業上の利用分野〉
この発明は、優れた強度、延性並びに靭性を兼備してい
て、航空機用構造部材等に適用した場合にそれらの更な
る性能向上を可能とする“型材”や“管材”等を工業的
規模で安定に生産し得るようにした、α＋β型チタン合
金押出材の製造方法に関するものである。[Detailed Description of the Invention] <Industrial Application Field> The present invention has excellent strength, ductility, and toughness, and when applied to aircraft structural members, etc., it is possible to further improve their performance. The present invention relates to a method for producing α+β type titanium alloy extruded material, which enables stable production of "shaped materials", "tube materials", etc. on an industrial scale.
く背景技術〉
α＋β型チタン合金は、優れた靭性を有していることに
加えて良好な強度、加工性、成形性ならびに溶接性をも
備えていることから、高い比強度と優れた耐食性が注目
されているチタン合金の中でも、航空機用構造部材や各
種設備・装置類の構造部材として最大の需要を誇るもの
であり、前記構造部材に供するためには、通常、押出成
形法によって所望素材形状への成形がなされてきた。Background technology α+β type titanium alloys have not only excellent toughness but also good strength, workability, formability, and weldability, so they have high specific strength and excellent corrosion resistance. Among the titanium alloys that are attracting attention, they are in the greatest demand as structural members for aircraft and various equipment and devices.In order to use these structural members, the material is usually shaped into the desired shape by extrusion molding. It has been shaped into
ところで、押出法によるα＋β型チタン合金の成形は変
形抵抗の小さいβ変態点以上の温度域で行われるのが一
般的であるが、β単相域で成形された押出材では“０．
２％耐力”や“延性”等がα＋β型域型出押出材べて低
いと言う問題点があった。By the way, α+β type titanium alloys are generally formed by extrusion in a temperature range above the β transformation point where deformation resistance is low, but extruded materials formed in the β single-phase region have “0.
There was a problem in that the α+β type extruded materials were all low in terms of 2% proof stress and ductility.
そこで、このような問題点を解消し、十分な強度、延性
、靭性等を備えた部材を提供すべり、Ｔｉ−６１１’−
４Ｖ系チタン合金を８５０〜９６０℃のα＋β域で押出
成形する方法が提案された（特開昭６１−１９３７１９
号）。Therefore, we solved these problems and provided a member with sufficient strength, ductility, toughness, etc.
A method of extrusion molding a 4V titanium alloy in the α+β region of 850 to 960°C was proposed (Japanese Patent Application Laid-open No. 193719-1983).
issue).
しかしながら、α＋β型チタン合金の加工温度と変形抵
抗との関係を示す第１図からも明らかなように、α＋β
域（８５０〜９６０℃）ではやはり変形抵抗が高く、そ
のため押出製品の寸法や加工度等の面で制限を受け、複
雑形状品の製造が困難であるとの問題を如何ともし難か
った。However, as is clear from Figure 1, which shows the relationship between processing temperature and deformation resistance of α+β type titanium alloy, α+β
In the temperature range (850 to 960°C), the deformation resistance is still high, which limits the dimensions and processing rate of extruded products, making it difficult to manufacture products with complex shapes.
〈問題点を解決する手段〉
本発明者等は、α＋β型チタン合金の押出成形品に係る
上記問題を解決し、強度、延性、靭性が共に優れたα＋
β型チタン合金の押出成形品を形状・寸法に格別な制限
を受けることなく安定製造すべく、様々な観点から研究
を行った結果、以下（ａｌ〜（ｄ）に示されるような知
見を得るに至ったのである。即ち、
（ａ） α＋β型チタン合金押出成形品に十分満足で
きる強度、延性並びに靭性を確保するには、最終製品の
ミクロ組織を“微細なβ粒の中に極めて微細な針状αが
存在する状態”とすることが重要であり、押出の最終形
状品を上記ミクロ組織とすれば良好な強度、延性並びに
靭性を兼備したα＋β型チタン合金部材が実現されるこ
と、（ｂｌ ただ、変形抵抗の低いβ域での押出成形
により微細なβ粒を得ることは極めて困難なことである
が、思い掛けないことに、押出素材たるビレットとして
その製作時に十分な加工を加えることで容易に実現でき
る“微細な等軸α＋β組織”を有するものを使用すると
共に、押出成形後に適切な処置を講ずれば、β域押出に
よっても十分に細かな再結晶β粒が得られ、該微細８粒
中に極めて微細な針状αを析出させたミクロ組織の実現
が可能となること、
（Ｃ） 再結晶β粒の成長を抑え、がっ延性を低下さ
せる要因である“β粒界へのα相の析出”を抑えるには
、上述のように押出成形後に適切な処置を講じる必要が
あるが、この処置は“押出成形後そのまま直ちに急冷す
る”手段でなければならないこと、
（ｄ） 上記急冷により得られるミクロ組織はマルテ
ンサイト（α′）と針状のα＋βの混合組織となってい
るが、十分に高い延性と靭性とを発揮する“微細なβ粒
の中に極めて微細な針状αが存在するミクロ組織”を実
現するためには、前記急冷後の押出材に所定条件の焼鈍
を施してマルテンサイト（α′）の分解を図る必要があ
ること。<Means for Solving the Problems> The present inventors have solved the above-mentioned problems regarding extrusion molded products of α+β type titanium alloys, and have developed α+ type titanium alloys that have excellent strength, ductility, and toughness.
In order to stably manufacture β-type titanium alloy extrusion products without any particular restrictions on shape or dimensions, we conducted research from various perspectives and obtained the knowledge shown in (al to (d)) below. (a) In order to ensure sufficient strength, ductility, and toughness for α+β type titanium alloy extruded products, the microstructure of the final product must be modified to have “extremely fine grains in the fine β grains”. It is important to create a state in which acicular α exists, and if the final shape of the extruded product has the above microstructure, an α + β type titanium alloy member with good strength, ductility, and toughness can be realized. bl However, it is extremely difficult to obtain fine β grains by extrusion molding in the β region where deformation resistance is low, but unexpectedly, it is possible to apply sufficient processing at the time of manufacturing the extruded material billet. If we use a material with a "fine equiaxed α+β structure" that can be easily achieved by extrusion and take appropriate measures after extrusion, sufficiently fine recrystallized β grains can be obtained even by β region extrusion. It is possible to realize a microstructure in which extremely fine acicular α particles are precipitated in eight fine grains, and (C) “β grain boundaries, which are a factor that suppresses the growth of recrystallized β grains and reduces ductility. In order to suppress the "precipitation of α phase into the material," as mentioned above, it is necessary to take appropriate measures after extrusion molding, but this treatment must be a means of "quenching immediately after extrusion molding." (d ) The microstructure obtained by the above rapid cooling is a mixed structure of martensite (α') and acicular α+β, but there are extremely fine β grains in the fine β grains that exhibit sufficiently high ductility and toughness. In order to realize a "microstructure in which acicular α exists," it is necessary to subject the extruded material after the rapid cooling to annealing under predetermined conditions to decompose martensite (α').
この発明は、上記知見に基づいてなされたものであり、
α＋β域で５０％以上の加工が行われて微細な等軸α＋
β組織とされたα＋β型チタン合金ビレットを、β変態
点〜〔β変態点＋１５０℃〕の温度に加熱して押出比１
０以上の押出加工を行うと共に、引き続いて５℃／秒以
上の冷却速度で５００℃以下にまで冷却し、その後７０
０〜８５０℃の温度で０．５〜４時間の焼鈍を行うこと
により、優れた強度、延性並びに靭性を兼備したα＋β
型チタン合金押出材を、複雑な形状・寸法のものであっ
ても容易かつ安定に製造し得るようにした点、に特徴を
有するものである。This invention was made based on the above knowledge, and more than 50% of the processing is performed in the α+β region, resulting in fine equiaxed α+
An α+β type titanium alloy billet with a β structure is heated to a temperature between the β transformation point and [β transformation point + 150°C], and the extrusion ratio is 1.
Extrusion processing of 0 or more is performed, followed by cooling to 500 °C or less at a cooling rate of 5 °C / sec or more, and then 70 °C
By annealing at a temperature of 0 to 850°C for 0.5 to 4 hours, α+β has excellent strength, ductility, and toughness.
This invention is characterized by the fact that it is possible to easily and stably manufacture type titanium alloy extruded materials even if they have complex shapes and dimensions.
なお、この発明の方法において、押出条件を上記の如く
に限定した理由を説明する。In addition, in the method of this invention, the reason why the extrusion conditions were limited as mentioned above will be explained.
Ａ）適用する押出ビレット
押出成形用ビレットとして“α＋β域で５０％以上加工
された微細な等軸組織を有するもの”を使用することと
したのは、α＋β域での加工率が５０％未満ではビレッ
トの組織を所望の微細な等軸α＋β組織とすることが出
来ずに針状或いはプレート状のα＋β組織となってしま
い、このようなミクロ組織のビレットを押出加工しても
微細な再結晶β粒が得られないからである。A) Applicable extrusion billet We decided to use a billet for extrusion molding that has a fine equiaxed structure that has been processed by 50% or more in the α+β region because if the processing rate in the α+β region is less than 50%, The structure of the billet cannot be made into the desired fine equiaxed α+β structure, but becomes an acicular or plate-like α+β structure, and even if a billet with such a microstructure is extruded, fine recrystallized β This is because grains cannot be obtained.
Ｂ）押出時の加熱温度
β変態点を下回る温度域での押出では、変形抵抗が高い
上、この発明が目指す“微細なβ粒の中に極めて微細な
針状αが析出したミクロ組織”を得ることが出来ずに靭
性の改善がなされない。一方、〔β変態点＋１５０℃〕
を超える温度で押出すると０．２％耐力、延性及び靭性
が劣化することに加えて、表面酸化による肌荒れにより
良好な製品を得ることが出来ない。従って、押出時の加
熱温度はβ変態点〜〔β変態点＋１５０’ｃ）の範囲と
限定した。B) Heating temperature during extrusion Extrusion in a temperature range below the β transformation point not only has high deformation resistance, but also reduces the ability to achieve the “microstructure in which extremely fine acicular α particles are precipitated within fine β grains” that this invention aims for. Therefore, the toughness cannot be improved. On the other hand, [β transformation point +150℃]
If extruded at a temperature exceeding 0.2%, the yield strength, ductility, and toughness will deteriorate, and a good product will not be obtained due to surface roughness due to surface oxidation. Therefore, the heating temperature during extrusion was limited to the range from the β transformation point to [β transformation point +150'c].
Ｃ）押出比
押出比が１０を下回る加工度では、再結晶β粒が加工中
に成長して０．２％耐力、延性及び靭性の劣化を招′く
こととなる。従って、押出比は１０以上と限定した。C) Extrusion Ratio If the extrusion ratio is less than 10, recrystallized β grains will grow during processing, resulting in a 0.2% deterioration of yield strength, ductility, and toughness. Therefore, the extrusion ratio was limited to 10 or more.
Ｄ）押出後の冷却速度、並びに急冷終了温度押出温度か
らの冷却速度を５℃／秒以上と定めたのは、冷却途中の
β粒の成長を抑え、かつ冷却途中で生成する粒界への粗
大なα相の析出を抑制するためであり、冷却速度が５℃
／秒未満であると上記抑制作用が十分でないからである
。また、急冷終了温度が５００℃を上回ると、やはりβ
粒の成長や粗大なα相析出の危険がある。従って、押出
の終了に引き続き、直ちに冷却速度５℃／秒以上で５０
０℃以下にまで冷却することと定めた。D) Cooling rate after extrusion and end temperature of quenching The cooling rate from the extrusion temperature was set at 5°C/sec or more to suppress the growth of β grains during cooling and to prevent the formation of grain boundaries during cooling. This is to suppress the precipitation of coarse α phase, and the cooling rate is 5℃.
This is because if it is less than /second, the above-mentioned suppressing effect will not be sufficient. Moreover, if the quenching end temperature exceeds 500℃, β
There is a risk of grain growth and coarse alpha phase precipitation. Therefore, immediately following the end of extrusion, the cooling rate is 5°C/sec or more to
It was decided that the temperature should be cooled to below 0°C.
Ｅ）焼鈍条件
先にも説明したように、冷却した後の押出材のミクロ組
織は（α′＋α＋β）の混合組織となっているが、α′
フマルンサイトが最終製品に存在すると著しい靭性低下
を招く。従って、冷却後の押出材は７００〜８５０℃の
温度で０．５〜４時間の焼鈍を施してα′フマルンサイ
トの分解を図る必要があるが、焼鈍温度が７００℃未満
であったり、焼鈍時間が０．５時間を下回る場合にはα
′−α＋βの分解が十分進行せず、一方、焼鈍温度が８
５０℃を超えたり、焼鈍時間が４時間を上回る場合には
、α′−α＋βの分解により生成したα相が成長して所
期の強度と靭性が得られない。E) Annealing conditions As explained earlier, the microstructure of the extruded material after cooling is a mixed structure of (α'+α+β), but α'
The presence of fumarunsite in the final product results in a significant decrease in toughness. Therefore, the extruded material after cooling needs to be annealed at a temperature of 700 to 850°C for 0.5 to 4 hours to decompose α' fumarunsite, but if the annealing temperature is less than 700°C, If the annealing time is less than 0.5 hours, α
′-α+β decomposition did not proceed sufficiently, and on the other hand, the annealing temperature was 8.
If the temperature exceeds 50°C or the annealing time exceeds 4 hours, the α phase produced by the decomposition of α'-α+β grows, making it impossible to obtain the desired strength and toughness.
続いて、この発明を実施例により比較例と対比しながら
具体的に説明する。Next, the present invention will be specifically explained using examples and comparing with comparative examples.
〈実施例〉
実施例 １
真空アーク溶解して得たところの、直径が４００ｍｍφ
で第１表に示す如き成分組成のＴｉ−６Ａｌ−４Ｖ合金
インゴットにβ鍛造及びα＋β鍛造を施した後（α＋β
鍛造の加工度は第２表に示す通り）、直径：１７０ｎφ
の押出用ビレットとした。<Example> Example 1 A piece with a diameter of 400 mmφ obtained by vacuum arc melting
After β forging and α+β forging were performed on a Ti-6Al-4V alloy ingot having the composition shown in Table 1 (α+β
The degree of forging is shown in Table 2), diameter: 170nφ
It was made into a billet for extrusion.
次いで、このビレットを用いて第２表に示ス条件で押出
加工を行い、焼鈍を施してＬ型材を製造した。Next, this billet was extruded under the conditions shown in Table 2 and annealed to produce an L-shaped material.
得られたし型材の機械的性質を調査し、その結果を第２
表に併せて示した。The mechanical properties of the obtained mold material were investigated and the results were used in the second
It is also shown in the table.
第２表に示される結果からも明らかなように、本発明の
条件通りに製造されたし型材は強度、延性及び靭性が共
に優れた値を示すのに対して、製造条件の何れかが本発
明の条件を満たさないものは、上記特性の全てを満足す
るものとならないことが分かる。As is clear from the results shown in Table 2, the shape material produced under the conditions of the present invention exhibits excellent values for both strength, ductility, and toughness, whereas It can be seen that a product that does not satisfy the conditions of the invention does not satisfy all of the above characteristics.
実施例 ２
真空アーク溶解して得たところの、直径が４００１１φ
で第３表に示す如き成分組成のＴｉ−６Ａｊ？−６Ｖ−
２Ｓｎ合金インゴットにβ鍛造及びα＋β鍛造を施した
後（α＋β鍛造の加工度は第４表に示す通り）、直径：
１６０ｍｍφの押出用ビレットとした。Example 2 The diameter was 40011φ obtained by vacuum arc melting.
So, Ti-6Aj with the component composition shown in Table 3? -6V-
After subjecting the 2Sn alloy ingot to β forging and α+β forging (the working degree of α+β forging is shown in Table 4), the diameter:
A billet for extrusion with a diameter of 160 mm was prepared.
次いで、このビレットを用いて第４表に示す条件で押出
加工を行い、焼鈍を施して継目無鋼管を製造した。Next, this billet was extruded under the conditions shown in Table 4 and annealed to produce seamless steel pipes.
得られた継目無鋼管の機械的性質を調査し、その結果を
第４表に併せて示した。The mechanical properties of the obtained seamless steel pipe were investigated, and the results are also shown in Table 4.
第４表に示される結果からも、本発明の条件通りに製造
、された継目無鋼管は強度、延性及び靭性が共に優れた
値を示すのに対して、製造条件の何れかが本発明の条件
を満たさないものは上記特性の何れかに劣っていること
が明らかである。The results shown in Table 4 also show that the seamless steel pipe manufactured under the conditions of the present invention exhibits excellent values for strength, ductility, and toughness, whereas any of the manufacturing conditions of the present invention It is clear that those that do not satisfy the conditions are inferior in any of the above characteristics.
なお、前記実施例１及び２ではＴｉ−６ＡＩ！−４Ｖ合
金及びＴｉ−６Ａｊ？ −６Ｖ −２Ｓｎ合金について
の説明に終始したが、その他のα＋β型チタン合金、例
えばＴｉ −３Ａ Ｉ −２，５Ｖ合金、 Ｔｉ−６Ａ
ｊ！ −２Ｓｎ−４２ｒ−２Ｍｏ合金或いはＴｉ ６
Ａｊ！ −２Ｓｎ −４２ｒ −６ＭＯ合金等について
も十分に満足できる結果が得られることは言うまでもな
い。In addition, in Examples 1 and 2, Ti-6AI! -4V alloy and Ti-6Aj? -6V -2Sn alloy has been explained, but other α+β type titanium alloys, such as Ti-3A I-2,5V alloy, Ti-6A
j! -2Sn-42r-2Mo alloy or Ti6
Aj! It goes without saying that fully satisfactory results can be obtained with -2Sn -42r -6MO alloys and the like.
く効果の総括〉 以上に説明した如く、この発明によれば、強度。Summary of effects> As explained above, according to the present invention, strength.
延性及び靭性の面でも極めて優れた性能を有するα＋β
型ヂタン合金押出材を製品形状・寸法に係わりなく高能
率で安定製造することができ、航空機機体用材料等とし
て一段と厳しさを増してきた要求性能を十分に満足する
α＋β型チタン合金部材をコスト安く提供することが可
能となるなど、その工業的意義は極めて大きいものであ
る。α+β has extremely excellent performance in terms of ductility and toughness.
It is possible to stably manufacture titanium alloy extruded materials with high efficiency regardless of the product shape and size, and it is possible to produce α+β type titanium alloy parts at a low cost that fully satisfy the increasingly strict performance requirements for materials such as aircraft fuselage materials. Its industrial significance is extremely great, as it can be provided at a low price.
−４−テ；→閤イｍ４つＡＷｒ住１カン浴計明二-4-te; → 4 pieces of AWr living in 1 room and bathing plan Meiji
第１図は、α＋β型チタン合金の加工温度と変形抵抗と
の関係を示すグラフである。FIG. 1 is a graph showing the relationship between processing temperature and deformation resistance of α+β type titanium alloy.
Claims (1)
β組織とされたα＋β型チタン合金ビレットを、β変態
点〜〔β変態点＋１５０℃〕の温度に加熱して押出比１
０以上の押出加工を行うと共に、引き続いて５℃／秒以
上の冷却速度で５００℃以下にまで冷却し、その後７０
０〜８５０℃の温度で０．５〜４時間の焼鈍を行うこと
を特徴とする、α＋β型チタン合金押出材の製造方法。[Claims] 50% or more of processing is performed in the α+β region to create a fine equiaxed α+
An α+β type titanium alloy billet with a β structure is heated to a temperature between the β transformation point and [β transformation point + 150°C], and the extrusion ratio is 1.
Extrusion processing of 0 or more is performed, followed by cooling to 500 °C or less at a cooling rate of 5 °C / sec or more, and then 70 °C
A method for producing an α+β type titanium alloy extruded material, characterized by performing annealing at a temperature of 0 to 850°C for 0.5 to 4 hours.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5526487A JPS63223155A (en) | 1987-03-12 | 1987-03-12 | Production of alpha+beta type titanium alloy extruded material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5526487A JPS63223155A (en) | 1987-03-12 | 1987-03-12 | Production of alpha+beta type titanium alloy extruded material |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS63223155A true JPS63223155A (en) | 1988-09-16 |
Family
ID=12993740
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5526487A Pending JPS63223155A (en) | 1987-03-12 | 1987-03-12 | Production of alpha+beta type titanium alloy extruded material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63223155A (en) |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5244517A (en) * | 1990-03-20 | 1993-09-14 | Daido Tokushuko Kabushiki Kaisha | Manufacturing titanium alloy component by beta forming |
| US6139659A (en) * | 1996-03-15 | 2000-10-31 | Honda Giken Kogyo Kabushiki Kaisha | Titanium alloy made brake rotor and its manufacturing method |
| EP1273674A1 (en) * | 2001-07-06 | 2003-01-08 | General Electric Company | Heat treatment of titanium-alloy article having martensitic structure |
| JP2009299124A (en) * | 2008-06-12 | 2009-12-24 | Kobe Steel Ltd | Titanium alloy billet having excellent defect detectability in ultrasonic crack inspection test |
| WO2010125253A1 (en) * | 2009-04-30 | 2010-11-04 | Cefival | Method for producing elongate products made of titanium |
| CN102327974A (en) * | 2011-06-23 | 2012-01-25 | 苏州旭创精密模具有限公司 | Electric control cabinet material bridge mould with primary back pressure workstation |
| JP2012052219A (en) * | 2010-08-03 | 2012-03-15 | Kobe Steel Ltd | α-β TITANIUM ALLOY EXTRUDED MATERIAL EXCELLENT IN FATIGUE STRENGTH, AND METHOD FOR PRODUCING THE α-β TITANIUM ALLOY EXTRUDED MATERIAL |
| JP6176425B1 (en) * | 2016-12-22 | 2017-08-09 | 新日鐵住金株式会社 | α + β type titanium alloy extrusion |
| JP2018053320A (en) * | 2016-09-29 | 2018-04-05 | 新日鐵住金株式会社 | α+β TYPE TITANIUM ALLOY HOT EXTRUSION SHAPE MATERIAL AND MANUFACTURING METHOD THEREFOR |
| JP2019167584A (en) * | 2018-03-23 | 2019-10-03 | 日本製鉄株式会社 | α + β TYPE TITANIUM ALLOY EXTRUSION SHAPE |
-
1987
- 1987-03-12 JP JP5526487A patent/JPS63223155A/en active Pending
Cited By (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5244517A (en) * | 1990-03-20 | 1993-09-14 | Daido Tokushuko Kabushiki Kaisha | Manufacturing titanium alloy component by beta forming |
| US6139659A (en) * | 1996-03-15 | 2000-10-31 | Honda Giken Kogyo Kabushiki Kaisha | Titanium alloy made brake rotor and its manufacturing method |
| EP1273674A1 (en) * | 2001-07-06 | 2003-01-08 | General Electric Company | Heat treatment of titanium-alloy article having martensitic structure |
| US6814820B2 (en) | 2001-07-06 | 2004-11-09 | General Electric Company | Heat treatment of titanium-alloy article having martensitic structure |
| JP2009299124A (en) * | 2008-06-12 | 2009-12-24 | Kobe Steel Ltd | Titanium alloy billet having excellent defect detectability in ultrasonic crack inspection test |
| FR2944983A1 (en) * | 2009-04-30 | 2010-11-05 | Cefival | PROCESS AND INSTALLATION FOR MANUFACTURING TITANIUM EXTENSION PRODUCTS |
| WO2010125253A1 (en) * | 2009-04-30 | 2010-11-04 | Cefival | Method for producing elongate products made of titanium |
| CN102438764A (en) * | 2009-04-30 | 2012-05-02 | 塞菲瓦尔公司 | Method for producing elongate products made of titanium |
| JP2012052219A (en) * | 2010-08-03 | 2012-03-15 | Kobe Steel Ltd | α-β TITANIUM ALLOY EXTRUDED MATERIAL EXCELLENT IN FATIGUE STRENGTH, AND METHOD FOR PRODUCING THE α-β TITANIUM ALLOY EXTRUDED MATERIAL |
| CN102327974A (en) * | 2011-06-23 | 2012-01-25 | 苏州旭创精密模具有限公司 | Electric control cabinet material bridge mould with primary back pressure workstation |
| JP2018053320A (en) * | 2016-09-29 | 2018-04-05 | 新日鐵住金株式会社 | α+β TYPE TITANIUM ALLOY HOT EXTRUSION SHAPE MATERIAL AND MANUFACTURING METHOD THEREFOR |
| JP6176425B1 (en) * | 2016-12-22 | 2017-08-09 | 新日鐵住金株式会社 | α + β type titanium alloy extrusion |
| WO2018116444A1 (en) | 2016-12-22 | 2018-06-28 | 新日鐵住金株式会社 | α+β TITANIUM ALLOY EXTRUDED MATERIAL |
| US11473173B2 (en) | 2016-12-22 | 2022-10-18 | Nippon Steel Corporation | α+βtitanium alloy extruded shape |
| JP2019167584A (en) * | 2018-03-23 | 2019-10-03 | 日本製鉄株式会社 | α + β TYPE TITANIUM ALLOY EXTRUSION SHAPE |
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