JPH04210457A - Manufacture of fe-ni base precipitation hardened superalloy - Google Patents
Manufacture of fe-ni base precipitation hardened superalloyInfo
- Publication number
- JPH04210457A JPH04210457A JP40969690A JP40969690A JPH04210457A JP H04210457 A JPH04210457 A JP H04210457A JP 40969690 A JP40969690 A JP 40969690A JP 40969690 A JP40969690 A JP 40969690A JP H04210457 A JPH04210457 A JP H04210457A
- Authority
- JP
- Japan
- Prior art keywords
- aging treatment
- cooling
- treatment
- superalloy
- cooling rate
- 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
- 229910000601 superalloy Inorganic materials 0.000 title claims abstract description 27
- 238000004519 manufacturing process Methods 0.000 title claims description 11
- 238000001556 precipitation Methods 0.000 title abstract description 7
- 238000011282 treatment Methods 0.000 claims abstract description 78
- 238000001816 cooling Methods 0.000 claims abstract description 58
- 230000032683 aging Effects 0.000 claims abstract description 52
- 238000004881 precipitation hardening Methods 0.000 claims abstract description 17
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 claims abstract description 8
- 229910052742 iron Inorganic materials 0.000 claims abstract description 5
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 5
- 229910045601 alloy Inorganic materials 0.000 abstract description 10
- 239000000956 alloy Substances 0.000 abstract description 10
- 239000000243 solution Substances 0.000 description 12
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 10
- 239000010931 gold Substances 0.000 description 10
- 229910052737 gold Inorganic materials 0.000 description 10
- 239000000463 material Substances 0.000 description 9
- 239000002184 metal Substances 0.000 description 8
- 229910052751 metal Inorganic materials 0.000 description 8
- 230000000694 effects Effects 0.000 description 6
- 238000010438 heat treatment Methods 0.000 description 6
- 239000002244 precipitate Substances 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 5
- 229910001026 inconel Inorganic materials 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 239000002344 surface layer Substances 0.000 description 5
- 238000000034 method Methods 0.000 description 4
- 238000007796 conventional method Methods 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 238000010583 slow cooling Methods 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- 150000002739 metals Chemical class 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 230000008646 thermal stress Effects 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 1
- 230000004913 activation Effects 0.000 description 1
- 238000003483 aging Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000007664 blowing Methods 0.000 description 1
- 239000003779 heat-resistant material Substances 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 230000002093 peripheral effect Effects 0.000 description 1
- 238000010248 power generation Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 239000002689 soil Substances 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
Landscapes
- Heat Treatment Of Articles (AREA)
Abstract
Description
［０００１１ [00011
【産業上の利用分野］この発明は、大型部材への応用を
可能としたＦｅ−Ｎｉ基析出硬化型超合金の製造方法に
関するものである。
［０００２］
【従来の技術】従来、Ｆｅ−Ｎｉ基析出硬化型超合金は
、Ｆｅ−Ｎｉベースの超合金を、固溶化処理した後、油
冷または油冷よりも速い冷却速度で急冷し、その後、中
間時効処理を経て時効処理を行っている。上記熱処理で
は、十分な適冷状態と、過飽和固溶体を得るために、固
溶化処理後、極力、急速に冷却することが原則とされて
おり、冷却方法には、冷却速度が大きな油冷や水冷が採
用されている。また、冷却後、時効処理に先立って、中
間時効処理が行われており、この処理によって、比較的
粗大で安定した相（以下「安定相Ｊと称する）を適度に
析出させてクリープ特性の改善を図っている。その後、
時効処理を行って、微細な析出物を析出させ、強度を高
めている
［０００３］上記した従来の熱処理を具体的に説明すれ
ば、例えば、インコネル７０６（商標名）合金では、９
２５〜９８０土１５℃で固溶化処理を行った後、水冷し
、８４５℃で３時間保持する中間時効処理を行う。次い
で、７２０℃で８時間の時効処理を行い、さらに、これ
を５０℃／時間の冷却速度で冷却し、引き続き６２０℃
で８時間時効させる２段時効を行っている。なお、イン
コネル７０６では、上記中間時効処理を安定化処理と称
する場合もある（例えばＡＭＳ規格）。上記した工程で
製造されるＦｅ−Ｎｉ基析出硬化型超合金は、高温強度
、クリープ強度が極めて優れており、ジェットエンジン
のタービンブレードなどの超耐熱材に使用されている。
［０００４］[Industrial Field of Application] The present invention relates to a method for producing a Fe--Ni based precipitation hardening superalloy that can be applied to large-sized members. [0002] Conventionally, Fe-Ni-based precipitation hardening superalloys are produced by subjecting Fe-Ni-based superalloys to solution treatment and then rapidly cooling them with oil cooling or at a faster cooling rate than oil cooling. After that, it undergoes an intermediate aging treatment and then an aging treatment. In the above heat treatment, in order to obtain a sufficiently appropriate cooling state and a supersaturated solid solution, the general rule is to cool as rapidly as possible after the solution treatment, and cooling methods include oil cooling and water cooling with a high cooling rate. It has been adopted. In addition, after cooling and prior to aging treatment, intermediate aging treatment is performed, and through this treatment, a relatively coarse and stable phase (hereinafter referred to as "stable phase J") is appropriately precipitated to improve creep characteristics. After that,
Aging treatment is performed to precipitate fine precipitates and increase the strength. [0003] To explain the above-mentioned conventional heat treatment specifically, for example, for Inconel 706 (trade name) alloy, 9
After performing solution treatment at 15° C. for 25 to 980 soil, intermediate aging treatment is performed by cooling with water and holding at 845° C. for 3 hours. Next, aging treatment was performed at 720°C for 8 hours, and this was further cooled at a cooling rate of 50°C/hour, and then aged at 620°C.
A two-stage aging process is performed in which the product is aged for 8 hours. In addition, in Inconel 706, the above-mentioned intermediate aging treatment is sometimes referred to as stabilization treatment (for example, according to the AMS standard). The Fe--Ni-based precipitation hardening superalloy produced by the above-described process has extremely excellent high-temperature strength and creep strength, and is used for super heat-resistant materials such as jet engine turbine blades. [0004]
【発明が解決しようとする課題】ところで、上記した超
合金を、発電用ガスタービンディスクなどの大型部材に
使用すると、上記製造工程の急冷時に、材料の表層部と
内部とで、小型部材では見られないような極めて大きな
冷却速度差が生じてしまう。この冷却速度差によって、
合金には大きな熱応力が生じて、割れが発生しやすくな
る。また、熱処理効果も、冷却速度差によって著しく差
が生じてくるので、機械的性質が、位置によって異なり
非常に不均質になる問題点がある。したがって、従来の
製造方法では、大型の超合金を用いて、析出状態が良好
で、機械的性質が優れた大型製品を得ることは困難であ
った。
［０００５］この発明は、前記課題を解決することを基
本的な目的とし、冷却速度差による不均質さをできるだ
け防止するとともに、析出硬化による十分な強度向上が
確保されるＦｅ−Ｎｉ基析出硬化型超合金を得ることを
目的とするものである。
［０００６］[Problems to be Solved by the Invention] By the way, when the above-mentioned superalloy is used in large components such as gas turbine disks for power generation, during the rapid cooling in the manufacturing process, the surface layer and the interior of the material may deteriorate compared to small components. This results in an extremely large difference in cooling rate that cannot be avoided. Due to this cooling rate difference,
Large thermal stresses occur in the alloy, making it more susceptible to cracking. In addition, the heat treatment effect varies significantly depending on the cooling rate, so there is a problem that the mechanical properties vary depending on the position and are extremely non-uniform. Therefore, with conventional manufacturing methods, it has been difficult to use large-sized superalloys to obtain large-sized products with good precipitation conditions and excellent mechanical properties. [0005] The basic purpose of the present invention is to solve the above-mentioned problems, and the present invention has a Fe-Ni-based precipitation hardening method that prevents heterogeneity due to differences in cooling rates as much as possible and ensures sufficient strength improvement due to precipitation hardening. The purpose is to obtain a type superalloy. [0006]
【課題を解決するための手段１上記課題を解決するため
、本願発明は、ＦｅおよびＮｉをベース成分とする超合
金を、固溶化処理した後、中間時効処理し、その後、時
効処理を行うＦｅ−Ｎｉ基析出硬化型超合金の製造方法
において、前記固溶化処理後の冷却を、空冷または空冷
よりも遅い冷却速度で行うとともに、前記中間時効処理
の処理時間を短縮し、または、中間時効処理を省略し、
その後、時効処理を行うことを特徴とする。
［０００７］ここで、本願発明が応用される超合金は、
ＦｅとＮｉをベース成分とし、その他必要な成分が添加
されたものであり、その後、本願発明の製造工程で析出
硬化によって、強度が高められるものである。ただし、
本願発明としては、上記超合金のＦｅ 、Ｎｉの含有量
や、他の成分の種別、含有量が特に限定されるものでは
ない。他の成分の一例としてしては、Ｃｒ、ＡＩ、Ｔｉ
、Ｎｂが適当量添加され、Ｓ、Ｐなどが不可避的に含ま
れるものが考えられる。その代表例としては、インコネ
ル７０６（商標名）合金を挙げることができる。
［０００８］そして、超合金は、析出物などを固溶させ
るように、固溶化処理がなされるが、その温度や１時間
は、超合金の組成や、形状などによって定められる。固
溶化処理後の冷却は、冷却速度が小さな空冷や、徐冷に
よって行われる。徐冷としては、炉冷が代表的であるが
、炉内冷却に限定されるものではなく、要は、十分に遅
い冷却速度で冷却する方法であればよい。但し、その速
度は、少なくとも、冷却によって合金を適冷でき、後工
程の時効処理によって、析出物が得られるものでなけれ
ばならない。なお、上記空冷においても、そのガスの選
択や、静置、送風、撹拌などの冷却方法も限定されるも
のではなく、適宜選択することができる。
［０００９］そして、中間時効処理は、固溶化処理を、
油冷または油冷よりも速い冷却速度で冷却した場合に必
要とされる中間時効処理時間よりも、短い時間で行うか
、あるいは、その処理を省略する。なお、中間時効処理
温度は、変更することを要しない。中間時効処理の有無
や、処理時間の短罐量は、超合金の組成や、固溶化処理
後の冷却速度などに従って、決定される。中間時効処理
後の時効処理は、従来と同様の温度、時間などに従って
行うことができる。また、所望により、処理時間を短縮
して行うことも可能であり、過時効を防ぐために、時効
処理時間の短縮が必須とされる場合もある。
［００１０］
【作用】すなわち、本願発明によれば、固溶化処理後の
冷却を、空冷よりも遅い冷却速度で行うので、製品粗材
の位置の違いによる冷却速度差が小さくなり、焼き割れ
の発生や、熱処理効果が不均質になるのを回避できる。
しかもＦｅ−Ｎｉベースの超合金は、焼入れ性が大きい
ので、上記した冷却によっても適冷状態が得られ、後述
する析出硬化作用が確保される。
［００１１３さらに、冷却速度を小さくしたことによっ
て、中間時効処理に達するまでの時間が長くなり、しか
も、この超合金では、析出相生成に対する活性化エネル
ギが小さいことが推測されるので、上記冷却中に、中間
時効で予定される安定相析出の潜伏期に入り、あるいは
、安定相の析出が開始していることが考えられる。なお
、中間時効処理を、従来と同程度の時間で処理した場合
には、安定相の析出が過度に行われることになり、過時
効になったり、時効硬化をもたらすＮｂ 、 Ｔｉ 、
Ａｌなどを消費して、最終的な時効処理時の析出を不
十分なものとして強度不足を招くのではないかと考えら
れる。
したがって、中間時効処理の処理時間を短縮または、省
略することによって、安定相が最適な状態で析出してい
るものと考えられる。適切な中間時効処理をおこなった
後に行う時効処理では、微細な析出物が析出する。また
、所望によって、過時効を防ぐように、時効時間を短縮
して行えば、良好な析出相が得らね、均質で、強度の優
れた超合金か得られる。
［００１２］[Means for Solving the Problems 1] In order to solve the above problems, the present invention provides a solution treatment for a superalloy containing Fe and Ni as base components, an intermediate aging treatment, and then an aging treatment. - In the method for producing a Ni-based precipitation hardening superalloy, the cooling after the solution treatment is performed with air cooling or a cooling rate slower than air cooling, and the treatment time of the intermediate aging treatment is shortened, or the intermediate aging treatment is performed. omit,
After that, it is characterized by performing an aging treatment. [0007] Here, the superalloy to which the present invention is applied is:
It has Fe and Ni as base components and other necessary components are added thereto, and is then subjected to precipitation hardening in the manufacturing process of the present invention to increase its strength. however,
In the present invention, the contents of Fe and Ni in the superalloy, as well as the types and contents of other components, are not particularly limited. Examples of other components include Cr, AI, Ti
, Nb may be added in appropriate amounts, and S, P, etc. may be unavoidably included. A typical example thereof is Inconel 706 (trade name) alloy. [0008] The superalloy is then subjected to solution treatment to dissolve precipitates and the like, and the temperature and time are determined depending on the composition, shape, etc. of the superalloy. Cooling after the solution treatment is performed by air cooling with a low cooling rate or slow cooling. A typical example of slow cooling is furnace cooling, but it is not limited to in-furnace cooling, and any method may be used as long as it cools at a sufficiently slow cooling rate. However, the speed must be such that at least the alloy can be appropriately cooled by cooling, and a precipitate can be obtained by the post-process aging treatment. In addition, in the above-mentioned air cooling, the selection of the gas and the cooling method such as standing still, blowing air, and stirring are not limited, and can be appropriately selected. [0009]The intermediate aging treatment includes solution treatment,
The intermediate aging treatment is performed in a shorter time than that required in the case of oil cooling or cooling at a faster cooling rate than oil cooling, or the treatment is omitted. Note that the intermediate aging treatment temperature does not need to be changed. The presence or absence of intermediate aging treatment and the short amount of treatment time are determined according to the composition of the superalloy, the cooling rate after solution treatment, etc. The aging treatment after the intermediate aging treatment can be performed according to the same temperature, time, etc. as in the conventional method. Further, if desired, it is possible to shorten the aging treatment time, and in some cases, it is essential to shorten the aging treatment time in order to prevent overaging. [0010] [Operation] That is, according to the present invention, cooling after solution treatment is performed at a slower cooling rate than air cooling, so the difference in cooling rate due to the difference in the position of the product rough material is reduced, and quench cracking is reduced. generation and non-uniform heat treatment effects can be avoided. Moreover, since the Fe--Ni-based superalloy has high hardenability, an appropriate cooling state can be obtained even by the above-mentioned cooling, and the precipitation hardening effect described below can be ensured. [00113 Furthermore, by reducing the cooling rate, it takes longer to reach the intermediate aging treatment, and in addition, in this superalloy, it is assumed that the activation energy for precipitate phase formation is small. It is conceivable that the steel has entered the latent period of stable phase precipitation scheduled for intermediate aging, or that stable phase precipitation has started. In addition, if the intermediate aging treatment is performed for a time comparable to that of the conventional method, stable phase precipitation will occur excessively, resulting in overaging or age hardening of Nb, Ti,
It is thought that Al and the like are consumed, resulting in insufficient precipitation during the final aging treatment, resulting in insufficient strength. Therefore, it is considered that the stable phase is precipitated in an optimal state by shortening or omitting the treatment time of the intermediate aging treatment. In the aging treatment performed after a suitable intermediate aging treatment, fine precipitates precipitate. Furthermore, if desired, if the aging time is shortened to prevent overaging, a good precipitated phase will not be obtained, but a homogeneous superalloy with excellent strength will be obtained. [0012]
【実施例】以下に、この発明の実施例を、本発明の範囲
外の比較例と比較しつつ、説明する。表１に示す合金組
成（含有量；重量％）からなるインコネル７０６合金を
溶製、鍛造して、第１図に示す径６４０ｍｍ、厚さ２４
０羽のディスク材４を用意し、供試合金Ａ、 Ｂとした
。なお、合金Ｎｏ、欄で、 「規格」と記載しである各
含有量の数値は、インコネル７０６合金の規格値を示す
ものである。
［００１３］[Examples] Examples of the present invention will be explained below while comparing them with comparative examples outside the scope of the present invention. Inconel 706 alloy having the alloy composition (content; weight %) shown in Table 1 was melted and forged to a diameter of 640 mm and a thickness of 24 mm as shown in Figure 1.
Disk material 4 containing 0 birds was prepared and used as test gold A and B. In addition, in the Alloy No. column, the numerical value of each content described as "standard" indicates the standard value of Inconel 706 alloy. [0013]
【表１】
［００１４］そして、供試合金Ａ、 Ｂに対し、それぞ
れ、９８０℃で３時間の固溶化処理を行い、その後、供
試合金Ａは水冷して、本願とは、冷却速度が異なる比較
例とした。また、供試合金Ｂは空冷した。なお、供試合
金の位置の違いによる冷却速度差を知るため、ディスク
材４の角部表層位置１．中心表層位置２．深部位置３の
各位置で冷却速度を測定した。その結果は表２に示すと
おりである。角部表層位置１は、表面および周面からそ
れぞれ４０ｍｎｔの距離の角部にあり、中心表層位置２
は、中心軸にあって、表面から４０Ｍの深さにあり、深
部位置３は、同じく中心軸にあって、表面から１２０ｍ
ｍの深さの最深部にある。
［００１５１表２の結果から、水冷した供試合金Ａでは
、位置の違いによる冷却速度差が非常に大きくて、熱処
理効果にも差異が生ずることが予測された。また、大き
な熱応力が生じているものと考えられ、さらに大型材で
は、割れが発生するおそれが大きい。これに対し、供試
合金Ｂは、位置の違いによる冷却速度差は、極めて小さ
かった。
［００１６］[Table 1] [0014] Test metals A and B were each subjected to solid solution treatment at 980°C for 3 hours, and then test metal A was water-cooled. This is a different comparative example. In addition, the test gold B was air-cooled. In addition, in order to know the cooling rate difference due to the difference in the position of the sample metal, the corner surface layer position 1 of the disk material 4 was determined. Center surface position 2. The cooling rate was measured at each deep position 3. The results are shown in Table 2. Corner surface layer position 1 is located at a corner at a distance of 40 mnt from the surface and peripheral surface, respectively, and center surface layer position 2
is located on the central axis at a depth of 40 m from the surface, and deep position 3 is located on the central axis and at a depth of 120 m from the surface.
It is located at the deepest part at a depth of m. [00151 From the results in Table 2, it was predicted that in water-cooled sample metal A, the difference in cooling rate due to the difference in position was very large, and that there would be a difference in the heat treatment effect. In addition, it is thought that large thermal stress is generated, and there is a high possibility that cracks will occur in large-sized materials. On the other hand, in sample gold B, the difference in cooling rate due to the difference in position was extremely small. [0016]
【表２】
［００１７］冷却した各供試合金は、引き続き、第３表
に示す中間時効処理を行った。すなわち、供試合金Ａに
は、従来と同様の温度、時間でその処理を行った。また
、供試合金Ｂは、３個を用意し、その１つを従来と同様
の温度、時間で中間時効処理を行って、供試合金Ｂ１と
した。他の１つは、処理温度を従来と同様とし、処理時
間を従来の３時間から、１２時間に変更して中間時効処
理を行った実施例であり、供試合金Ｂ２とした。また、
最後の１つは、中間時効処理を省略した実施例であり、
供試合金Ｂ３とした。
［００１８］[Table 2] [0017] Each of the cooled test specimens was subsequently subjected to the intermediate aging treatment shown in Table 3. That is, sample gold A was treated at the same temperature and time as conventional treatments. In addition, three samples of sample gold B were prepared, and one of them was subjected to an intermediate aging treatment at the same temperature and time as in the past to obtain sample gold B1. The other example is an example in which an intermediate aging treatment was carried out by keeping the treatment temperature the same as before and changing the treatment time from the conventional 3 hours to 12 hours, and it was designated as sample gold B2. Also,
The last one is an example in which intermediate aging treatment is omitted,
The match gold was set as B3. [0018]
【表３】
［００１９］さらに、各供試合金を、表３に示す条件で
時効処理を行った。時効処理は、従来と同様の方法（同
一温度、時間）で行った。得られた析出硬化型超合金の
機械的性質を評価するため、各供試合金の位置１および
位置３より試験材を採取し、それぞれ引張試験（室温右
よび６５０℃）と、高温でのクリープ破断試験とを行っ
た。その結果は表４に示すとおりである。
［００２０３表４から明らかなように、冷却を水冷で行
った比較例の供試合金Ａは、位置１と位置３で、機械的
性質が大きく異なっていた。これを一つの用途例として
、ＡＭＳ規格値５７０３Ｂと照合すると、位置１では、
高温強度は十分に規格値を満足しているものの、位置３
では、規格値を下回っており、機械的性質の不均質さが
際立っていた。
［００２１１一方、固溶化処理後の冷却を空冷に代え、
中間時効処理は、従来と同じ処理時間で行った比較例の
供試合金Ｂ１は、機械的性質の不均質さは除かれたが、
強度が不足しており、位置１．３ともに、高温強度は前
記ＡＭＳ規格値を下回っていた。
［ｏ ｏ ２２］次に、本願発明の実施例である供試合
金８２、Ｂ３は、機械的性質の不均質さが除かれるとと
もに、高温強度も十分に向上しており、位置１，３とも
に、同程度の高温強度を有し、前記ＡＭＳ規格値を満足
していた。なお、上記実施例では、中間時効処理時間を
短縮した供試合金Ｂ２と、中間時効処理を省略した供試
合金Ｂ３とは、はぼ同じ機械的性質が得られたが、合金
の組成や、形状寸法などによって、両者間に差異が生ず
ることも考えられるので、最適な機械的特性を得るため
には、組成および形状寸法に応じてその都度、中間時効
処理の有無と、処理時間の短縮量とを適宜決定する。
［００２３］[Table 3] [0019] Furthermore, each sample gold was subjected to aging treatment under the conditions shown in Table 3. The aging treatment was performed in the same manner as the conventional method (same temperature and time). In order to evaluate the mechanical properties of the resulting precipitation hardening superalloy, test materials were taken from position 1 and position 3 of each specimen, and subjected to tensile tests (at room temperature and 650°C) and creep tests at high temperatures. A breaking test was conducted. The results are shown in Table 4. [00203 As is clear from Table 4, the mechanical properties of the sample metal A of the comparative example, which was cooled by water cooling, were significantly different between positions 1 and 3. Taking this as an application example, when comparing it with the AMS standard value 5703B, at position 1,
Although the high temperature strength fully satisfies the standard value,
The results were below the standard values, and the heterogeneity of mechanical properties was noticeable. [00211 On the other hand, cooling after solution treatment is replaced with air cooling,
The intermediate aging treatment was performed for the same treatment time as the conventional one, and the specimen B1 of the comparative example had the non-uniformity of mechanical properties removed, but
The strength was insufficient, and the high temperature strength at both positions 1 and 3 was below the AMS standard value. [o o 22] Next, sample gold 82, B3, which is an example of the present invention, has non-uniformity in mechanical properties removed and high-temperature strength is sufficiently improved, and both positions 1 and 3 are , had comparable high-temperature strength and satisfied the AMS standard values. In addition, in the above-mentioned example, almost the same mechanical properties were obtained for the sample metal B2 in which the intermediate aging treatment time was shortened and the sample metal B3 in which the intermediate aging treatment was omitted, but the alloy composition, Differences may occur between the two depending on the shape and dimensions, so in order to obtain the optimal mechanical properties, it is necessary to determine whether intermediate aging treatment is performed and the amount of reduction in treatment time depending on the composition and shape. shall be determined as appropriate. [0023]
【表４】 ［００２４］[Table 4] [0024]
【発明の効果】以上説明したように、本願発明のＦｅＮ
ｉ基析出硬化型超合金の製造方法によれば、固溶化処理
後の冷却速度を遅くするとともに、中間時効処理を雑種
化、または省略することにより、熱処理効果の不均質さ
や、境き割れを回避することができる。また、本願発明
の製造方法によれば、小型部材はもとより、大型部材に
おいても、均質で、十分な析出硬化が達成され、従来の
製造方法によるよりも、高温強度およびクリープ特性の
優れたＦｅ−Ｎｉ基析出硬化型超合金を得ることができ
る。[Effects of the Invention] As explained above, the FeN of the present invention
According to the method for producing i-base precipitation hardening superalloys, the cooling rate after solution treatment is slowed down, and intermediate aging treatment is hybridized or omitted, thereby reducing the heterogeneity of the heat treatment effect and boundary cracking. can be avoided. Furthermore, according to the manufacturing method of the present invention, homogeneous and sufficient precipitation hardening can be achieved not only in small parts but also in large parts, and Fe- A Ni-based precipitation hardening superalloy can be obtained.
【図１】本発明実施例と、比較例に用いる供試合金のデ
ィスク材の平面図である。FIG. 1 is a plan view of disc materials of test metals used in examples of the present invention and comparative examples.
【図２】同じくディスク材の縦断面図である。FIG. 2 is a longitudinal cross-sectional view of the disk material.
１ 角部表層位置 ２ 中心表層位置 ３ 深部位置 ４ ディスク材 1 Corner surface position 2 Center surface layer position 3 Deep position 4 Disc material
Claims (2)
を、固溶化処理した後、中間時効処理し、その後、時効
処理を行うＦｅ−Ｎｉ基析出硬化型超合金の製造方法に
おいて、前記固溶化処理後の冷却を、空冷または空冷よ
りも遅い冷却速度で行うとともに、前記中間時効処理の
処理時間を短縮し、または、中間時効処理を省略し、そ
の後、時効処理を行うことを特徴とするＦｅ−Ｎｉ基析
出硬化型超合金の製造方法1. A method for producing a Fe-Ni-based precipitation hardening superalloy, in which a superalloy containing Fe and Ni as base components is subjected to solution treatment, intermediate aging treatment, and then aging treatment. Cooling after solution treatment is performed by air cooling or at a cooling rate slower than air cooling, and the treatment time of the intermediate aging treatment is shortened, or the intermediate aging treatment is omitted, and then the aging treatment is performed. Method for producing Fe-Ni based precipitation hardening superalloy
とする請求項１記載のＦｅ−Ｎｉ基析出硬化型超合金の
製造方法2. The method for producing a Fe-Ni-based precipitation hardening superalloy according to claim 1, characterized in that the aging treatment time is shortened.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP40969690A JPH04210457A (en) | 1990-12-11 | 1990-12-11 | Manufacture of fe-ni base precipitation hardened superalloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP40969690A JPH04210457A (en) | 1990-12-11 | 1990-12-11 | Manufacture of fe-ni base precipitation hardened superalloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH04210457A true JPH04210457A (en) | 1992-07-31 |
Family
ID=18518998
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP40969690A Pending JPH04210457A (en) | 1990-12-11 | 1990-12-11 | Manufacture of fe-ni base precipitation hardened superalloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH04210457A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0774530A1 (en) * | 1995-11-17 | 1997-05-21 | Asea Brown Boveri Ag | Process for producing a heat resistant part from an iron-nickel superalloy |
| FR2768156A1 (en) * | 1997-09-05 | 1999-03-12 | Korea Atomic Energy Res | Tempering a nickel based alloy to improve corrosion resistance |
| JP2009299187A (en) * | 2008-06-16 | 2009-12-24 | Korea Inst Of Machinery & Materials | Heat treatment method for forming wavy grain boundary in nickel-based alloy, and alloy treated with the same |
-
1990
- 1990-12-11 JP JP40969690A patent/JPH04210457A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0774530A1 (en) * | 1995-11-17 | 1997-05-21 | Asea Brown Boveri Ag | Process for producing a heat resistant part from an iron-nickel superalloy |
| FR2768156A1 (en) * | 1997-09-05 | 1999-03-12 | Korea Atomic Energy Res | Tempering a nickel based alloy to improve corrosion resistance |
| JP2009299187A (en) * | 2008-06-16 | 2009-12-24 | Korea Inst Of Machinery & Materials | Heat treatment method for forming wavy grain boundary in nickel-based alloy, and alloy treated with the same |
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