JPS63219558A - Heat treatment for ti-6al-4v alloy material - Google Patents
Heat treatment for ti-6al-4v alloy materialInfo
- Publication number
- JPS63219558A JPS63219558A JP5304187A JP5304187A JPS63219558A JP S63219558 A JPS63219558 A JP S63219558A JP 5304187 A JP5304187 A JP 5304187A JP 5304187 A JP5304187 A JP 5304187A JP S63219558 A JPS63219558 A JP S63219558A
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- Prior art keywords
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- treatment
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- 239000000956 alloy Substances 0.000 title claims abstract description 14
- 238000010438 heat treatment Methods 0.000 title claims description 9
- 238000001816 cooling Methods 0.000 claims abstract description 14
- 229910000883 Ti6Al4V Inorganic materials 0.000 claims abstract description 8
- 230000032683 aging Effects 0.000 claims abstract description 8
- 238000000034 method Methods 0.000 claims description 5
- 239000000463 material Substances 0.000 abstract description 24
- 238000005242 forging Methods 0.000 abstract description 2
- 238000005096 rolling process Methods 0.000 abstract description 2
- 230000002706 hydrostatic effect Effects 0.000 abstract 1
- 230000000052 comparative effect Effects 0.000 description 6
- 230000009466 transformation Effects 0.000 description 5
- 238000000137 annealing Methods 0.000 description 4
- 229910000734 martensite Inorganic materials 0.000 description 4
- 238000010583 slow cooling Methods 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- 229910001069 Ti alloy Inorganic materials 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 239000000523 sample Substances 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 229910000756 V alloy Inorganic materials 0.000 description 1
- 239000012141 concentrate Substances 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 230000003628 erosive effect Effects 0.000 description 1
- 238000000462 isostatic pressing Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000005070 sampling Methods 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野］
本発明は、高比強度材料として広く用いられているＴｉ
−６Ａｌ−４Ｖ合金材の特に大型の部材に適した熱処理
方法に関するものである。[Detailed Description of the Invention] [Industrial Application Field] The present invention applies to Ti, which is widely used as a high specific strength material.
The present invention relates to a heat treatment method suitable for particularly large-sized members made of -6Al-4V alloy materials.
［従来の技術］
Ｔｉ−６Ａｌ−４Ｖ合金材はＡｌ１．５０〜６．７５％
（重量基準） 、Ｖ３．５０〜４．５０％、ｌ”ｅＯ，
３０％以下、００．２０％以下、Ｃ０，１０％以下、Ｎ
ｏ、 ０５％以下、ＨＯ，０１５％以下、Ｙ Ｏ，０
０５％以下含むＴｉ合金材で、その高い比強度と優れた
靭性とを利用し、構造用材料として広く用いられている
。近年ではその寸法の大型化した製品の需要が高まり、
大型部材を均一に高強度にする熱処理方法が必要とされ
るようになってきている。[Prior art] Ti-6Al-4V alloy material has Al 1.50 to 6.75%
(weight basis), V3.50-4.50%, l”eO,
30% or less, 0.20% or less, C0.10% or less, N
o, 05% or less, HO, 015% or less, Y O, 0
It is a Ti alloy material containing 0.05% or less of Ti, and is widely used as a structural material due to its high specific strength and excellent toughness. In recent years, demand for products with larger dimensions has increased,
There is an increasing need for a heat treatment method that uniformly increases the strength of large components.
これに対し、一般に高強度を求める場合には、溶体化時
効処理、溶体化過時効処理等がとられるが、これらはマ
ルテンサイト変態を利用しているため、冷却速度が各部
位により異なる大型の部材では強度のばらつきが大きく
なる欠点を有する。On the other hand, when high strength is generally required, solution aging treatment, solution overaging treatment, etc. are used, but since these utilize martensitic transformation, the cooling rate differs depending on each part of the large-sized The disadvantage is that the strength of the members varies widely.
また、均一な強度を得るための焼鈍処理や、二重焼鈍（
ｄｕｐｌｅｘ ａｎｎｅａｌ ）では、高強度が得られ
にくい。同様にβ相からの焼き入れは、伸び、絞りが低
下するという欠点を有する。In addition, annealing treatment and double annealing (
duplex anneal), it is difficult to obtain high strength. Similarly, quenching from the β phase has the disadvantage of decreasing elongation and reduction of area.
又、Ｔｉ−６Ａｌ−４Ｖ合金は、冷間での成形性が乏し
く熱間で加工されることが多い。この熱間での加工の目
的は、目的の形状にすることと、機械的性質の向上であ
る。Furthermore, the Ti-6Al-4V alloy has poor cold formability and is often hot-processed. The purpose of this hot processing is to form a desired shape and to improve mechanical properties.
［発明が解決しようとする問題点］
しかしながら、Ｔ ｉ −６Ａ １ ４ Ｖ 合金ハ
、熱間での加工硬化能は小ざく、変形が表面にかたより
がちである。このため、大型部材では、通常の焼鈍、例
えばＡ Ｍ ３４９２０に定める７０５〜７６０℃の焼
鈍では、中心部は加工があまり加わっていないため、所
望の機械的性質の向上が１ｑられず、表面近傍で強度が
高く、中心部で強度が低い、不均一な強度分布をもつ。[Problems to be Solved by the Invention] However, the T i -6A 14 V alloy C has a small hot work hardening ability, and deformation tends to be concentrated on the surface. For this reason, with normal annealing for large parts, such as annealing at 705 to 760°C specified in A M 34920, the center part is not processed much, so the desired mechanical properties cannot be improved by 1q, and the areas near the surface are It has an uneven intensity distribution with high intensity in the center and low intensity in the center.
この強度の不均一性は、応力が負荷された場合には、応
力集中を生じる原因となり、耐用期間の短縮につながる
。This non-uniformity in strength causes stress concentration when stress is applied, leading to a shortened service life.
本発明では、Ｔｉ−６Ａｌ−４Ｖ合金大型部材の機械的
性質の均質化を目的とする。The present invention aims to homogenize the mechanical properties of a large Ti-6Al-4V alloy member.
また、上記不均一性をさけるために、β変態点近傍より
徐冷することも考えられるが、このような熱処理では高
強度が得られない。そこで、発明ではさらに高強度を得
ることも目的とする。Further, in order to avoid the above-mentioned non-uniformity, it is possible to perform slow cooling from near the β transformation point, but high strength cannot be obtained with such heat treatment. Therefore, the invention aims to obtain even higher strength.
［問題点を解決するための手段］
本発明は、Ｔｉ−６Ａｌ−４Ｖ合金材をα＋β域または
β域で加工した後、８８０℃以上１０５０℃以下で１０
分以上８時間以内保持し、その後６００ ℃以上８８０
℃未満の範囲の温度まで連続的に徐冷し、その温度で１
０分以上８時間以内保持した後、空冷もしくはそれ以上
の冷却速度で冷却し、さらに４５０℃以上６５０℃以下
の温度域で１時間以上１０時間以内の時効処理を加える
ことを特徴とするＴｉ−６Ａｌ−４Ｖ合金材の熱処理方
法である。[Means for Solving the Problems] The present invention provides a method for processing a Ti-6Al-4V alloy material in the α+β region or β region, and then processing the material at a temperature of 880°C or higher and 1050°C or lower for 10°C.
Hold for at least 8 hours, then at 600°C or more at 880°C.
Continuously slow cooling to a temperature in the range below ℃, and at that temperature 1
After holding for 0 minutes to 8 hours, the Ti- This is a method for heat treatment of 6Al-4V alloy material.
本発明の前記Ｔｉ−６Ａｌ−４Ｖ合金材はＡ Ｉ ５．
５０〜６．７５％（重量基準、以下同様）、■３．５０
〜４．５０％、Ｆｅｏ、３０％以下、００．２％以下、
Ｃ０，１０％以下、Ｎｏ、０５％以下、ｌ−１０，０１
５％以下、Ｙ Ｏ，００５％以下を含むＴｉ合金材に適
用されるものである。The Ti-6Al-4V alloy material of the present invention is A I5.
50-6.75% (weight basis, same below), ■3.50
~4.50%, Feo, 30% or less, 00.2% or less,
C0, 10% or less, No, 05% or less, l-10,01
It is applied to Ti alloy materials containing 5% or less and 0.005% or less.
上記α＋β域またはβ域での加工は、例えば圧延、鍛造
、静水圧プレス等によって行い、その侵の熱処理により
、材料は全体にわたりα相の等軸化及び再結晶をおこし
、加工の前履歴の影響がなくなり、均一な状態となる。Processing in the above α+β region or β region is performed, for example, by rolling, forging, isostatic pressing, etc., and the erosive heat treatment causes equiaxed and recrystallized α phase throughout the material, which changes the previous history of processing. The effect disappears and the state becomes uniform.
８８０℃未満の温度では、十分なα相の等軸化及び再結
晶が行われない。なお、かつこの間にＡＩ、Ｏ等のα安
定化型元素はα相へ、Ｖ、Ｆｅ等のβ安定化型元素はβ
相へと濃縮されていく。At temperatures below 880° C., sufficient equiaxing and recrystallization of the α phase does not occur. Additionally, during this period, α-stabilized elements such as AI and O enter the α phase, and β-stabilized elements such as V and Fe enter the β phase.
Concentrates into phases.
温度の上限を１０５０℃としたのは、これ以上の温度で
はα相が消失し、上記のα安定化型元素、β安定化型元
素の濃縮が行われないためでおる。The reason why the upper limit of the temperature is set to 1050° C. is that at a temperature higher than this, the α phase disappears and the above-mentioned α-stabilized elements and β-stabilized elements are not concentrated.
時間を１０分以上としたのは、これより短い時間では、
材料に均一な温度分布を与えられないためであり、８時
間以内としたのは、経済的な効率を考慮したためである
。The reason for setting the time to 10 minutes or more is that if the time is shorter than this,
This is because a uniform temperature distribution cannot be given to the material, and the reason why the heating time is set within 8 hours is because economical efficiency is considered.
本発明では、上記高温での保持にひきつづき、６００℃
以上８８０℃未満の範囲の温度まで徐冷するが、その徐
冷の速度は０．２℃／ Ｓｅｃ以下が適当である。そし
てその温度で１０分以上８時間以内保持する。In the present invention, in addition to holding at the above-mentioned high temperature,
It is slowly cooled to a temperature in the range below 880°C, and the slow cooling rate is suitably 0.2°C/Sec or less. Then, hold at that temperature for 10 minutes or more and 8 hours or less.
前記第１の保持温度から上記第２の保持温度までの徐冷
は、α相、β相の平衡的な変態を促し、なおかつ、β相
のβ安定化型元素による安定化も促進する。冷却速度が
速いときは、拡散が変態に追いつかないため、β相の安
定化が十分性われない。Slow cooling from the first holding temperature to the second holding temperature promotes equilibrium transformation of the α phase and β phase, and also promotes stabilization of the β phase by the β stabilizing element. When the cooling rate is high, diffusion cannot keep up with transformation, and the β phase is not sufficiently stabilized.
第２の保持温度は、そこからの冷却により、マルテンサ
イト変態をおこさず、残留β相を多く残させることを目
的として選ばれている。平衡状態ではこれらの温度はＭ
ｆ点より上に位置しているため、マルテンサイトを生じ
るはずであるが、β相にはβ安定化型元素が濃縮されて
いるため、本発明の場合はマルテンサイトは生じない。The second holding temperature is selected for the purpose of not causing martensitic transformation and leaving a large amount of residual β phase by cooling from there. At equilibrium these temperatures are M
Since it is located above the f point, martensite should be produced, but since β-stabilizing elements are concentrated in the β phase, martensite is not produced in the case of the present invention.
ただし、６００℃未満の温度ではβ相が安定化しすぎて
おり、この後の時効処理によってα相を析出させないた
め、本発明には含めない。However, at temperatures below 600° C., the β phase becomes too stable and the α phase is not precipitated by the subsequent aging treatment, so it is not included in the present invention.
この後、空冷もしくはそれ以上の冷却速度で冷却するが
、具体的には０．１５℃／ Ｓｅｃ以上の冷却速度で３
００℃以下の温度まで冷却する。これより遅い速度で冷
却した場合には、α相の成長により、β相は失くなって
しまい、残留β相は存在しない。After that, it is cooled by air or at a cooling rate higher than that, but specifically, at a cooling rate of 0.15°C/Sec or higher.
Cool to a temperature below 00°C. If the cooling rate is slower than this, the β phase will be lost due to the growth of the α phase, and no residual β phase will exist.
上記の熱処理にひきつづき、４５０℃以上６５０℃以下
の温度域にて、１時間以上、１０時間以内の時効処理を
加える。これにより残留β相からはα相が析出し、強度
を向上させる。Following the above heat treatment, an aging treatment is applied at a temperature range of 450° C. or higher and 650° C. or lower for 1 hour or more and 10 hours or less. As a result, the α phase precipitates from the residual β phase, improving the strength.
［実施例］ 以下に実施例を示す。[Example] Examples are shown below.
実施例１
直径２４０ｍｍ（７）Ｔ ｉ −６Ａ Ｉ −４Ｖ合金
α＋β域鍛造材を供試材とした。これを９５０℃で１．
５時間保持後、１時間ないし１時間３０分かけてａ ｏ
ｏ’ｃ又は７００℃まで冷却し、その温度で１時間保持
した後水冷を行った。これに引き続き５００℃又は６０
０℃で４時間の時効処理を施した。Example 1 A forged material in the α+β region of a Ti-6A I-4V alloy having a diameter of 240 mm (7) was used as a test material. This was heated to 950℃ for 1.
After holding for 5 hours, ao for 1 hour to 1 hour 30 minutes.
The mixture was cooled to 700° C., maintained at that temperature for 1 hour, and then cooled with water. Following this, 500℃ or 60℃
Aging treatment was performed at 0°C for 4 hours.
実施例２
実施例１におけるのと同じ供試材を用い、これを９２０
℃で１．５時間保持後、１時間ないし１時間３０分かけ
て８００℃又は７００℃まで冷却し、その温度で１時間
保持した後水冷を行った。これに引き続き５００℃又は
６００℃で４時間の時効処理を施した。Example 2 Using the same test material as in Example 1, it was
After being held at 1.5 hours at 0.degree. C., it was cooled to 800.degree. C. or 700.degree. C. over 1 hour to 1 hour and 30 minutes, kept at that temperature for 1 hour, and then cooled with water. Subsequently, aging treatment was performed at 500°C or 600°C for 4 hours.
かかる素材から図に示す位置から試験片を採取し、機械
的性質の試験をした。A test piece was taken from the material at the position shown in the figure and tested for mechanical properties.
試験結果の１例として９２０℃より８００℃まで冷却し
、ここより水冷したものを６００℃で時効したものの試
験結果を表１に示す。As an example of the test results, Table 1 shows the test results of a sample that was cooled from 920°C to 800°C, water-cooled from there, and then aged at 600°C.
表１
比較例１
実施例１と同じ供試材を用い、７００℃で４時間熱処理
後空冷した。この素材の機械的性質の試験結果を表２に
示す。Table 1 Comparative Example 1 Using the same test material as in Example 1, it was heat treated at 700° C. for 4 hours and then air cooled. Table 2 shows the test results for the mechanical properties of this material.
表２
比較例２
実施例１と同じ供試材を用い、１１００℃で２時間熱処
理後空冷した。この素材の機械的性質の試験結果を表３
に示す。Table 2 Comparative Example 2 The same test material as in Example 1 was heat treated at 1100° C. for 2 hours and then cooled in air. Table 3 shows the test results of the mechanical properties of this material.
Shown below.
表３
比較例３
実施例１と同じ供試材を用い、９２０℃で１．５時間熱
処理後至温まで徐冷し、ついで６００℃で４時間時効処
理した。この素材の機械的性質の試験結果を表４に示す
。Table 3 Comparative Example 3 Using the same test material as in Example 1, it was heat treated at 920°C for 1.5 hours, slowly cooled to the lowest temperature, and then aged at 600°C for 4 hours. Table 4 shows the test results for the mechanical properties of this material.
表４
比較例４
実施例１と同じ供試材を用い、９５５℃で１．５時間熱
処理後、水冷し、ついで５５０℃で６時間時効処理した
。この素材の機械的性質の試験結果を表５に示す。Table 4 Comparative Example 4 Using the same test material as in Example 1, it was heat treated at 955°C for 1.5 hours, cooled with water, and then aged at 550°C for 6 hours. Table 5 shows the test results for the mechanical properties of this material.
表５
前記実施例並びに比較例における機械的性質のばらつき
を含めた評価方法として、ＮＩＬ−ＨＯ２に−５では、
Ａｆａでの評価を推薦している。これは 。Table 5 As an evaluation method including variations in mechanical properties in the above examples and comparative examples, for NIL-HO2-5,
We recommend evaluation with Afa. this is .
次式で表わされる値である。This value is expressed by the following formula.
Ａ値＝平均値−に×標準偏差
ここで、に値はデータの数と求める信頼度により決まる
数値で、データ数１５．９９％信頼度の場合は３．５２
である。A value = average value - × standard deviation Here, the value is determined by the number of data and the desired reliability, and in the case of 15.99% reliability for the number of data, it is 3.52
It is.
これによりデータを整理した結果を表６に示す。Table 6 shows the results of organizing the data.
表６
［発明の効果］
上記表６から明らかなとおり、本発明のものは比較例の
ものに較べ、強度に信頼性を考慮に入れると、優れた強
度が１ｑられている。これはばらつきの少ない高強度材
が得られることを示している。Table 6 [Effects of the Invention] As is clear from Table 6 above, the product of the present invention has superior strength by 1q compared to the comparative example when reliability is taken into account. This indicates that a high-strength material with little variation can be obtained.
図は供試材の寸法と試験片の採取位置を示す説明図であ
る。The figure is an explanatory diagram showing the dimensions of the sample material and the sampling position of the test piece.
Claims (1)
した後、８８０℃以上１０５０℃以下で１０分以上８時
間以内保持し、その後６００℃以上８８０℃未満の範囲
の温度まで連続的に徐冷し、その温度で１０分以上８時
間以内保持した後、空冷もしくはそれ以上の冷却速度で
冷却し、さらに４５０℃以上６５０℃以下の温度域で１
時間以上１０時間以内の時効処理を加えることを特徴と
するＴｉ−６Ａｌ−４Ｖ合金材の熱処理方法。After processing the Ti-6Al-4V alloy material in the α+β region or β region, it is held at 880°C or more and 1050°C or less for 10 minutes or more and 8 hours, and then continuously reduced to a temperature in the range of 600°C or more and less than 880°C. After cooling and holding at that temperature for 10 minutes or more and less than 8 hours, cool with air cooling or a faster cooling rate, and then cool in a temperature range of 450°C or more and 650°C or less.
1. A method for heat treatment of Ti-6Al-4V alloy material, characterized by applying an aging treatment for more than 10 hours and less than 10 hours.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5304187A JPS63219558A (en) | 1987-03-10 | 1987-03-10 | Heat treatment for ti-6al-4v alloy material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5304187A JPS63219558A (en) | 1987-03-10 | 1987-03-10 | Heat treatment for ti-6al-4v alloy material |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS63219558A true JPS63219558A (en) | 1988-09-13 |
Family
ID=12931801
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5304187A Pending JPS63219558A (en) | 1987-03-10 | 1987-03-10 | Heat treatment for ti-6al-4v alloy material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63219558A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0683242A1 (en) * | 1994-03-23 | 1995-11-22 | Nkk Corporation | Method for making titanium alloy products |
| KR100473809B1 (en) * | 2002-11-22 | 2005-03-08 | 학교법인 포항공과대학교 | Method for manufacturing (α+ β)titanium alloys with improved mechanical and dynamic fracture properties |
-
1987
- 1987-03-10 JP JP5304187A patent/JPS63219558A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0683242A1 (en) * | 1994-03-23 | 1995-11-22 | Nkk Corporation | Method for making titanium alloy products |
| US5516375A (en) * | 1994-03-23 | 1996-05-14 | Nkk Corporation | Method for making titanium alloy products |
| KR100473809B1 (en) * | 2002-11-22 | 2005-03-08 | 학교법인 포항공과대학교 | Method for manufacturing (α+ β)titanium alloys with improved mechanical and dynamic fracture properties |
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