JP2005060821A - beta TYPE TITANIUM ALLOY, AND COMPONENT MADE OF beta TYPE TITANIUM ALLOY - Google Patents
beta TYPE TITANIUM ALLOY, AND COMPONENT MADE OF beta TYPE TITANIUM ALLOY Download PDFInfo
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- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 54
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 45
- 239000000956 alloy Substances 0.000 claims abstract description 45
- 230000032683 aging Effects 0.000 claims abstract description 27
- 238000005242 forging Methods 0.000 claims abstract description 23
- 238000010438 heat treatment Methods 0.000 claims abstract description 23
- 238000005096 rolling process Methods 0.000 claims abstract description 15
- 238000005482 strain hardening Methods 0.000 claims abstract description 14
- 239000000203 mixture Substances 0.000 claims abstract description 12
- 239000010936 titanium Substances 0.000 claims abstract description 11
- 229910052742 iron Inorganic materials 0.000 claims abstract description 8
- 239000013078 crystal Substances 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 239000000463 material Substances 0.000 abstract description 9
- 238000004519 manufacturing process Methods 0.000 abstract description 7
- 238000000034 method Methods 0.000 abstract description 6
- 229910052759 nickel Inorganic materials 0.000 abstract description 2
- 239000000243 solution Substances 0.000 description 17
- 239000011651 chromium Substances 0.000 description 13
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 13
- 230000000694 effects Effects 0.000 description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- 238000010273 cold forging Methods 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
- 229910052758 niobium Inorganic materials 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 239000012224 working solution Substances 0.000 description 2
- 229910001040 Beta-titanium Inorganic materials 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 229910000604 Ferrochrome Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910010380 TiNi Inorganic materials 0.000 description 1
- 230000005856 abnormality Effects 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000003679 aging effect Effects 0.000 description 1
- 239000004566 building material Substances 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 238000003475 lamination Methods 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 229910052715 tantalum Inorganic materials 0.000 description 1
- 238000010313 vacuum arc remelting Methods 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
- 238000004804 winding Methods 0.000 description 1
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Abstract
Description
本発明は、β型チタン合金と、この合金を材料とする部品に関する。本発明により、チタンに比較的安価な合金元素を添加した廉価な合金を材料とし、高い強度を有する部品が提供される。 The present invention relates to a β-type titanium alloy and a part made of this alloy. According to the present invention, there is provided a component having a high strength made of an inexpensive alloy obtained by adding a relatively inexpensive alloy element to titanium.
軽量で高い強度をもつ部品の材料としてはβ型チタン合金が適切であって、これまでに、下記のような組成のものが開発されている。
Ｔｉ−１５Ｖ−３Ａｌ−３Ｃｒ−３Ｓｎ
Ｔｉ−３Ａｌ−８Ｖ−６Ｃｒ−４Ｍｏ−４Ｓｎ
Ｔｉ−１３Ｖ−１１Ｃｒ−３Ａｌ
Ｔｉ−１５Ｍｏ−５Ｚｒ−３Ａｌ
Ｔｉ−２９Ｎｂ−１３Ｔａ−４．６Ｚｒ
A β-type titanium alloy is suitable as a material for lightweight and high-strength parts, and materials having the following compositions have been developed so far.
Ti-15V-3Al-3Cr-3Sn
Ti-3Al-8V-6Cr-4Mo-4Sn
Ti-13V-11Cr-3Al
Ti-15Mo-5Zr-3Al
Ti-29Nb-13Ta-4.6Zr
上記の合金組成には、Ｖ，Ｍｏ，Ｎｂ，Ｔａといった高価な成分が比較的多量に存在し、したがってこれらのチタン合金は高価である。そのような成分を含有しないが、高強度なチタン合金として、Ｃｒ：６〜１３％、Ｆｅ：１〜４％およびＡｌ：３〜７％を含有し、残部がＴｉからなる合金が開示された（特許文献１）。この高強度チタン合金は、加工性にすぐれているというが、実際に製造してみると、結晶粒が不均一になりやすく、それにともなって強度が低いことが少なくない。改善策としては、固溶化処理や時効処理を行なうか、または冷間加工を行なうべきである。 In the above alloy composition, there are relatively large amounts of expensive components such as V, Mo, Nb, and Ta, and therefore these titanium alloys are expensive. An alloy that does not contain such components but contains Cr: 6 to 13%, Fe: 1 to 4%, and Al: 3 to 7% as a high-strength titanium alloy, with the balance being Ti is disclosed. (Patent Document 1). This high-strength titanium alloy is said to be excellent in workability, but when actually manufactured, the crystal grains tend to be non-uniform, and the strength is often low accordingly. As an improvement measure, solution treatment, aging treatment, or cold working should be performed.
出願人も、高強度で価格低廉なチタン合金として、Ｃｒ：２〜１２％、Ｆｅ：８．８％以下、Ｎｉ：７％以下およびＡｌ：６％以下を含み、残部Ｔｉからなるβ型チタン合金を提案した（特許文献２）。この合金は、βトランザス以上の温度に加熱して急冷することにより、高い強度と延性をもたらす均一なβ相が得られる。さらに３５０〜６００℃で時効処理を施すことにより、硬さを高めて耐摩耗性を向上させることができる。しかし、この合金は固溶化状態で硬く、さらに時効反応が早いため、圧延の巻取りで折損する傾向がある。こうした特性は、この合金で部品を量産する場合に、それを困難にする要因である。
本発明の目的は、高価な添加元素を必要とせず、したがって価格が低廉であるが、高い強度を有し、部品の量産が容易なβ型チタン合金を提供することにある。その合金を材料として製造される、高強度な部品を提供することもまた、本発明の目的に含まれる。 An object of the present invention is to provide a β-type titanium alloy which does not require an expensive additive element and is therefore inexpensive, but has high strength and easy mass production of parts. It is also included in the object of the present invention to provide a high-strength part manufactured from the alloy.
本発明のβ型チタン合金は、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。 The β-type titanium alloy of the present invention has an alloy composition containing, in mass%, Cr: 10 to 20% and Fe: 5% or less, with the balance being Ti and inevitable impurities.
本発明のチタン合金の部品のひとつのグループは、上記のβ型チタン合金に、熱間加工、すなわちβトランザス以上であって１１００℃以下の温度で鍛造または圧延を行なって部品形状を与えたものである。 One group of parts of the titanium alloy of the present invention is the above-mentioned β-type titanium alloy, which is hot-worked, that is, forged or rolled at a temperature of not less than β transus and not more than 1100 ° C. to give a part shape It is.
本発明のチタン合金の部品のいまひとつのグループは、上記のβ型チタン合金に、熱間加工、すなわちβトランザス以上であって１１００℃以下の温度で鍛造または圧延を行なったのち、冷間加工を行なって部品形状を与えたものである。 Another group of parts of the titanium alloy according to the present invention includes hot working, that is, forging or rolling at a temperature of not less than β transus and not more than 1100 ° C. The part shape is given in line.
本発明によれば、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必要とすることなく、Ｆｅ，Ｃｒ，Ｎｉといった比較的安価な合金元素を添加しただけで、高強度を発揮するβ型チタン合金を提供することができる。時効速度を遅延化する効果を有するＣｒの添加は、この合金を各種部品に加工する際の製造性を高める。 According to the present invention, a relatively inexpensive alloy element such as Fe, Cr, or Ni is added without requiring an expensive alloy element such as V, Mo, Nb, or Ta as in a conventional β-type titanium alloy. It is possible to provide a β-type titanium alloy that exhibits high strength. The addition of Cr, which has the effect of delaying the aging rate, increases the manufacturability when this alloy is processed into various parts.
本発明に従うチタン合金の部品は、上記ふたつのグループのいずれにおいても高い強度を示すが、とくに冷間加工を施したものは、後述する実施例にみるとおり、すぐれた強度を示す。 The titanium alloy parts according to the present invention show high strength in any of the above two groups, but particularly those subjected to cold working show excellent strength, as seen in the examples described later.
本発明のβ型チタン合金は、上記した基本的な合金成分に加えて、さらに、Ｎｉ：７％以下およびＡｌ：６％以下の一方または両方を含有することができる。 In addition to the basic alloy components described above, the β-type titanium alloy of the present invention can further contain one or both of Ni: 7% or less and Al: 6% or less.
本発明のβ型チタン合金の合金組成は、前掲の特許文献２の高強度β型チタン合金と対比したとき、Ｃｒ量が高く、Ｆｅ量が低減されたものといえる。本発明の合金においてＦｅおよびＣｒは、（Ｎｉを添加する場合はＮｉも）、合金を強度の高いβ相とするために添加する。しかし、Ｆｅ含有量を増加させて強度を高めたβチタン合金は硬く、製造性が低い。この欠点を補うため、Ｃｒ量を増加させた。以下、合金組成の限定理由を説明する。 It can be said that the alloy composition of the β-type titanium alloy of the present invention has a high Cr content and a reduced Fe content when compared with the high-strength β-type titanium alloy of Patent Document 2 described above. In the alloy of the present invention, Fe and Cr (when Ni is added, Ni is also added) to make the alloy have a high-strength β phase. However, β-titanium alloys having increased strength by increasing the Fe content are hard and have low productivity. In order to compensate for this defect, the Cr content was increased. Hereinafter, the reasons for limiting the alloy composition will be described.
Ｃｒ：１０〜２０％
Ｃｒは、Ｔｉをβ相化するとともに、時効速度を遅くする効果を有する、比較的安価な元素である。本発明のβ型チタン合金を構成する必須の元素として、上記の範囲内で添加する。１０％未満では時効反応を遅くする効果が低い。好ましいのは、１３％またはそれを超える量である。２０％を超えて添加しても、効果が飽和するし、合金の比重が高くなって、本来チタン合金がもつ、軽量という利点が失われる。
Cr: 10-20%
Cr is a relatively inexpensive element that has the effect of slowing the aging rate while turning Ti into β-phase. As an essential element constituting the β-type titanium alloy of the present invention, it is added within the above range. If it is less than 10%, the effect of slowing the aging reaction is low. Preferred is an amount of 13% or more. Even if added over 20%, the effect is saturated, the specific gravity of the alloy becomes high, and the advantage of light weight inherent to the titanium alloy is lost.
Ｆｅ：５％以下
Ｆｅも、上記のようにＴｉをβ相化する元素である。Ｆｅ量の増大によって強度は上昇するが、硬さが増して加工性を損なうため、両者のバランスをとって上限を５％とした。
Fe: 5% or less Fe is also an element that makes Ti into β phase as described above. Although the strength increases as the amount of Fe increases, the hardness increases and the workability is impaired. Therefore, the upper limit is set to 5% by balancing the two.
Ｎｉ：７％以下
Ｎｉは、β相を安定化する元素のうちで、比較的安価なものであるから、本発明の合金においては、Ｃｒの一部を置換する形で添加することができる。しかし、Ｎｉを過剰に含有すると、熱処理の際に金属間化合物ＴｉＮｉ2が生成しやすくなり、これが脆化を引き起こして強度が低下する。そこで７％という上限を設けた。
Ni: 7% or less Ni is an element that stabilizes the β phase and is relatively inexpensive. Therefore, in the alloy of the present invention, Ni can be added in a form of replacing a part of Cr. However, when Ni is contained excessively, the intermetallic compound TiNi 2 is easily generated during the heat treatment, which causes embrittlement and decreases strength. Therefore, an upper limit of 7% was set.
Ａｌ：６％以下
Ａｌは、合金の時効処理で生じるα相を強化するために添加する。過剰に添加すると、金属間化合物Ｔｉ3Ａｌが析出して合金が脆くなるので、含有率の上限を６％とした。
Al: 6% or less Al is added to reinforce the α phase generated by the aging treatment of the alloy. If added excessively, the intermetallic compound Ti 3 Al precipitates and the alloy becomes brittle, so the upper limit of the content was made 6%.
本発明のβ型チタン合金を材料として前記したような部品を製造する方法のひとつのグループは、前記したように、チタン合金に対し、βトランザス以上であって１１００℃以下の温度で鍛造または圧延を行なって部品形状を与え、ただちに急冷することにより、均一なβ相を形成させることである。それにより、高い強度を有する部品を製造することができる。βトランザスは、７５０℃前後の温度であって、チタン合金の組成によって多少変動する。この温度を下回る加工温度は、割れを招くことがある。しかし高温に過ぎると加工中に結晶粒が粗大化するから、１１００℃までの温度での加工を行なうべきである。 As described above, one group of methods for manufacturing the above-described component using the β-type titanium alloy of the present invention as a material is forging or rolling the titanium alloy at a temperature of not less than β transus and not more than 1100 ° C. To form a uniform β phase by giving a part shape and immediately cooling rapidly. Thereby, parts having high strength can be manufactured. β transus is a temperature around 750 ° C. and varies somewhat depending on the composition of the titanium alloy. Processing temperatures below this temperature can lead to cracking. However, if the temperature is too high, the crystal grains become coarse during processing, so processing at temperatures up to 1100 ° C. should be performed.
上記の鍛造または圧延に続いて、固溶化熱処理を施すことが好ましい。それにより、チタン合金のβ相が再結晶化されて、すぐれた強度と延性が得られる。固溶化は、加工後のチタン合金を、βトランザス以上であって１０００℃以下の温度に加熱する操作により実施することができる。 Subsequent to the forging or rolling described above, a solution heat treatment is preferably performed. Thereby, the β phase of the titanium alloy is recrystallized, and excellent strength and ductility are obtained. The solution treatment can be performed by an operation of heating the processed titanium alloy to a temperature not lower than β transus and not higher than 1000 ° C.
鍛造または圧延に続いて、時効処理を施すことも好ましい。時効処理は、３５０〜６００℃、好ましくは４００〜５５０℃で実施することができる。前述のように、本発明のβ型チタン合金は時効反応があまり早くないから、そのコントロールは容易である。時効処理によって、この合金の部品の強度はさらに高まる。時効処理は、固溶化熱処理の前に行なってもよいし、後に行なってもよいし、前後両方に行ってもよい。 It is also preferable to perform an aging treatment after forging or rolling. The aging treatment can be carried out at 350 to 600 ° C., preferably 400 to 550 ° C. As described above, the β-type titanium alloy of the present invention does not have a fast aging reaction, so that the control is easy. Aging treatment further increases the strength of the alloy parts. The aging treatment may be performed before the solution heat treatment, may be performed after the heat treatment, or may be performed both before and after.
本発明のβ型チタン合金を材料として、前記したような部品を製造する方法のいまひとつのグループは、β型チタン合金に、βトランザス以上であって１１００℃以下の温度で鍛造または圧延を行なったのち、冷間加工を行なって部品形状を与えるものである。冷間加工は、より高い強度と硬さとを与える。 Another group of methods for manufacturing the above-described parts using the β-type titanium alloy of the present invention as a material was forging or rolling the β-type titanium alloy at a temperature of β transus or higher and 1100 ° C. or lower. After that, cold working is performed to give a part shape. Cold working gives higher strength and hardness.
部品形状を冷間加工により与える場合も、熱間加工によった場合と同様、固溶化熱処理を施すことが好ましい。この場合の固溶化熱処理も、前記したところと同様に、チタン合金を、βトランザス以上であって１１００℃以下の温度に加熱するという操作で実施でき、固溶化により、β相が再結晶化して、均一な組織が得られる。固溶化熱処理と冷間加工とは、どちらを先にしてもよい。 When the part shape is given by cold working, it is preferable to perform solution heat treatment as in the case of hot working. The solution heat treatment in this case can also be performed by an operation of heating the titanium alloy to a temperature of not less than β transus and not more than 1100 ° C., as described above, and the β phase is recrystallized by solution treatment. A uniform structure can be obtained. Either the solution heat treatment or the cold work may be performed first.
同じく部品形状を冷間加工により与える場合も、それに続いて時効処理を施すことが好ましい。この場合の時効処理も、前記したところと同じく、３５０〜６００℃、好ましくは４００〜５５０℃で実施することができ、時効効果によって、この合金の部品の強度はさらに高まる。上記の固溶化熱処理と時効処理とは、併用することが好ましい。 Similarly, when the part shape is given by cold working, it is preferable to perform an aging treatment subsequently. The aging treatment in this case can be carried out at 350 to 600 ° C., preferably 400 to 550 ° C., as described above, and the strength of the alloy component is further increased by the aging effect. The solution heat treatment and the aging treatment are preferably used in combination.
このように、本発明のチタン合金から部品を製造する方法には、つぎのようなさまざまな工程が可能である。
・鍛造または圧延
・鍛造または圧延−固溶化熱処理
・鍛造または圧延−時効処理
・鍛造または圧延−固溶化熱処理−時効処理
・鍛造または圧延−冷間加工
・鍛造または圧延−冷間加工−時効処理
・鍛造または圧延−固溶化熱処理−冷間加工
・鍛造または圧延−冷間加工−固溶化熱処理
・鍛造または圧延−固溶化熱処理−冷間加工
・鍛造または圧延−固溶化熱処理−冷間加工−時効処理
・鍛造または圧延−冷間加工−固溶化熱処理−時効処理
Thus, the following various processes are possible for the method of manufacturing a part from the titanium alloy of the present invention.
-Forging or rolling-Forging or rolling-solution heat treatment-Forging or rolling-aging treatment-Forging or rolling-solution heat treatment-aging treatment-Forging or rolling-cold work-Forging or rolling-cold work-aging treatment- Forging or rolling-Solution heat treatment-Cold working / forging or rolling-Cold working-Solution heat treatment / Forging or rolling-Solution heat treatment-Cold working / forging or rolling-Solution heat treatment-Cold working-Aging treatment・ Forging or rolling-cold working-solution heat treatment-aging treatment
本発明のチタン合金は溶接性にすぐれ、共材を使用して溶接した場合にも、溶接部の外観や硬さに異常はみられない。 The titanium alloy of the present invention is excellent in weldability, and there is no abnormality in the appearance and hardness of the welded part even when welding is performed using a common material.
スポンジチタン（純度９９．８％）、純鉄（純度９９．９％）、純クロム（純度９９．３％）、低炭素フェロクロム２号、純Ｎｉ（純度９９．９％）およびＳＵＳ３０４鋼屑を原料とし、プラズマ積層凝固炉を用いて種々の合金組成のチタン合金を溶製して、直径１９０mm、長さ７００mmのインゴットを得た。それらを真空アーク再溶解炉（ＶＡＲ）を用いて二次溶解し、直径２４０mm、長さ５００mmのインゴットにした。それぞれの合金組成を、表1に示す。発明合金１〜９は本発明に従った合金組成を有するものであり、比較合金Ａ〜Ｃは、Ｃｒが不足であるか、またはＦｅ量が過大な合金組成のものである。 Sponge titanium (purity 99.8%), pure iron (purity 99.9%), pure chromium (purity 99.3%), low carbon ferrochrome No. 2, pure Ni (purity 99.9%) and SUS304 steel scrap Titanium alloys having various alloy compositions were melted as raw materials using a plasma lamination solidification furnace to obtain ingots having a diameter of 190 mm and a length of 700 mm. They were secondarily melted using a vacuum arc remelting furnace (VAR) to form an ingot having a diameter of 240 mm and a length of 500 mm. Table 1 shows the respective alloy compositions. Inventive alloys 1 to 9 have an alloy composition according to the present invention, and comparative alloys A to C have an alloy composition in which Cr is insufficient or the amount of Fe is excessive.
上記のチタン合金のインゴットを９５０℃に加熱し、熱間鍛造を行なって直径２０mmの丸棒とした。別に、直径８５mmの鍛造材を８５０℃で熱間圧延し、直径１２．５mmの線材とし、コイルに巻き取った。上記の丸棒に対し、表２に示す固溶化熱処理を施したものを、サンプルとした。各サンプルから、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６．２５mm、標点距離２５mm）を用意した。引張試験は、インストロン型引張試験機を用い、クロスヘッド速度５×１０-5m/sとして引張強さを測定した。引張強さを、硬さとともに表２に示す。表２にみるとおり、比較合金はコイルの巻取り過程で折損が発生しているのに対し、発明合金は硬すぎず、製造性が良好である。
The titanium alloy ingot was heated to 950 ° C. and hot forged into a round bar having a diameter of 20 mm. Separately, a forged material having a diameter of 85 mm was hot-rolled at 850 ° C. to obtain a wire material having a diameter of 12.5 mm, which was wound around a coil. A sample obtained by subjecting the above round bar to solution heat treatment shown in Table 2 was used as a sample. From each sample, a No. 3 tensile test piece (diameter 6.25 mm, gauge distance 25 mm) defined by ASTM E8 was prepared by machining. In the tensile test, an tensile strength was measured using an Instron type tensile tester at a crosshead speed of 5 × 10 −5 m / s. Table 2 shows the tensile strength together with the hardness. As seen in Table 2, the comparative alloy is broken during the winding process of the coil, whereas the inventive alloy is not too hard and the manufacturability is good.
さらに、上記サンプルに５００℃×８時間の時効処理を施したものから試験片をつくり、引張試験をした。その結果は表３に示すとおりであって、いっそうの強度向上が認められた。 Further, a test piece was prepared from the sample subjected to aging treatment at 500 ° C. for 8 hours, and a tensile test was performed. The results are as shown in Table 3, and a further improvement in strength was observed.
実施例１で製造した発明合金１〜９の直径２０mmの丸棒に対し、さまざまな加工率で冷間加工を行なって、加工後の引張強さおよび硬さを測定した。その結果を、表４に実施例３−１〜３−９として示す。比較のため、発明合金１〜９のサンプルについて、冷間加工を行なわなかった場合の引張強さと硬さとを測定して、比較例３−１〜３−９として、表４に併記した。冷間加工後の引張強さおよび硬さは熱間圧延後の製品をしのぎ、時効処理を施した場合とほぼ同等であることが、表４のデータを表２および表３のデータと対比することにより理解される。 The 20 mm diameter round bars of the inventive alloys 1 to 9 produced in Example 1 were cold worked at various working rates, and the tensile strength and hardness after working were measured. The results are shown in Table 4 as Examples 3-1 to 3-9. For comparison, the samples of Invention Alloys 1-9 were measured for tensile strength and hardness when not cold worked, and are shown in Table 4 as Comparative Examples 3-1 to 3-9. Contrast the data in Table 4 with the data in Table 2 and Table 3 that the tensile strength and hardness after cold working are almost the same as when the product after hot rolling is overtaken and subjected to aging treatment. Is understood.
実施例１で製造した発明合金１〜９の直径２０mmの丸棒に対し、加工率５０％の冷間加工を行ない、ついで実施例１と同じ条件（５００℃×８時間）の時効処理を施した。時効処理後の引張強さおよび硬さを測定した結果を、表５に示す。
The 20 mm diameter round bars of Inventive Alloys 1-9 manufactured in Example 1 were cold worked at a processing rate of 50%, and then subjected to aging treatment under the same conditions (500 ° C. × 8 hours) as in Example 1. did. Table 5 shows the results of measuring the tensile strength and hardness after aging treatment.
実施例１で製造した発明合金１〜９の直径２０mmの丸棒に対し、加工率５０％の冷間加工を行ない、ついで実施例１と同じ条件（９００℃×１時間→空冷）の固溶化熱処理を施した。固溶化熱処理後の引張強さおよび硬さを測定した結果を、表６に示す。 The 20 mm diameter round bars of Inventive Alloys 1 to 9 manufactured in Example 1 were cold worked at a processing rate of 50%, and then solid solutiond under the same conditions as in Example 1 (900 ° C. × 1 hour → air cooling). Heat treatment was applied. Table 6 shows the results of measuring the tensile strength and hardness after the solution heat treatment.
実施例１で製造した発明合金１〜９の直径２０mmの丸棒に対し、実施例１と同じ条件（９００℃×１時間→空冷）の固溶化熱処理を施したのち、加工率５０％の冷間加工を行ない、ついで実施例１と同じ条件（５００℃×８時間）の時効処理を施した。時効処理後の引張強さおよび硬さを測定した結果を、表７に示す。
The 20 mm diameter round bars of inventive alloys 1 to 9 manufactured in Example 1 were subjected to a solution heat treatment under the same conditions as in Example 1 (900 ° C. × 1 hour → air cooling), and then cooled at a processing rate of 50%. Then, an aging treatment was performed under the same conditions as in Example 1 (500 ° C. × 8 hours). Table 7 shows the results of measurement of tensile strength and hardness after aging treatment.
本発明のβ型チタン合金は、強度および靭延性にすぐれ、かつ低コストであるから、自動車エンジン用のコンロッド、バルブおよびスプリング、航空機エンジン用のブレードおよびディスクのように、軽量で高強度を要求される各種の機械部品の材料として好適に使用される。本発明のβ型チタン合金はまた、釣り具やゴルフクラブヘッドなどのレジャー用品、めがねフレーム、アタッシェケースなどの生活用品に使用されるほか、パソコン、デジタルカメラ、携帯電話などのＯＡ機器、車椅子などの医療福祉機器の構造部材、さらには、ビル、橋、道路などの建築材料として有用である。 Since the β-type titanium alloy of the present invention has excellent strength and toughness and is low in cost, it requires light weight and high strength such as connecting rods, valves and springs for automobile engines, blades and disks for aircraft engines. It is suitably used as a material for various machine parts. The β-type titanium alloy of the present invention is also used for leisure goods such as fishing gear and golf club heads, daily goods such as eyeglass frames and attache cases, OA equipment such as personal computers, digital cameras and mobile phones, and wheelchairs. It is useful as a structural member for medical welfare equipment, and further as a building material for buildings, bridges, roads and the like.
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| JP2006308027A (en) * | 2005-04-28 | 2006-11-09 | Yamaha Motor Co Ltd | Connecting rod, manufacturing method thereof, internal combustion engine, automobile |
| WO2008050892A1 (en) | 2006-10-26 | 2008-05-02 | Nippon Steel Corporation | Beta titanium alloy |
| GB2457998A (en) * | 2007-12-19 | 2009-09-09 | Gen Electric | A method of working titanium alloys |
| JP2009270163A (en) * | 2008-05-08 | 2009-11-19 | Daido Steel Co Ltd | Titanium alloy |
| JP2010279581A (en) * | 2009-06-05 | 2010-12-16 | Japan Lifeline Co Ltd | Guide wire |
| CN102400013A (en) * | 2010-09-09 | 2012-04-04 | 北京正安广泰新材料科技有限公司 | Low-cost beta titanium alloy |
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| JP2006308027A (en) * | 2005-04-28 | 2006-11-09 | Yamaha Motor Co Ltd | Connecting rod, manufacturing method thereof, internal combustion engine, automobile |
| DE102007031508B4 (en) | 2006-07-27 | 2019-03-28 | Denso Corporation | Engine and wiper device containing the engine |
| US9816158B2 (en) | 2006-10-26 | 2017-11-14 | Nippon Steel & Sumitomo Metal Corporation | β-type titanium alloy |
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| WO2008050892A1 (en) | 2006-10-26 | 2008-05-02 | Nippon Steel Corporation | Beta titanium alloy |
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| JP2009270163A (en) * | 2008-05-08 | 2009-11-19 | Daido Steel Co Ltd | Titanium alloy |
| JP2010279581A (en) * | 2009-06-05 | 2010-12-16 | Japan Lifeline Co Ltd | Guide wire |
| CN102400013A (en) * | 2010-09-09 | 2012-04-04 | 北京正安广泰新材料科技有限公司 | Low-cost beta titanium alloy |
| CN111647835A (en) * | 2020-06-01 | 2020-09-11 | 南京理工大学 | Method for improving mechanical heat treatment of beta-type titanium alloy |
| KR102434519B1 (en) * | 2021-12-29 | 2022-08-22 | 한국재료연구원 | Method of manufacturing high strength titanium alloy using ferrochrome and high strength titanium alloy |
| WO2023128356A1 (en) * | 2021-12-29 | 2023-07-06 | 한국재료연구원 | Method for manufacturing high-strength titanium alloy by using ferrochrome, and high-strength titanium alloy |
| CN115386819A (en) * | 2022-08-09 | 2022-11-25 | 中国第二重型机械集团德阳万航模锻有限责任公司 | Aging temperature-punching control method for ultrahigh-strength titanium alloy |
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