JPH11117019A - Production of heat resistant parts - Google Patents
Production of heat resistant partsInfo
- Publication number
- JPH11117019A JPH11117019A JP29177497A JP29177497A JPH11117019A JP H11117019 A JPH11117019 A JP H11117019A JP 29177497 A JP29177497 A JP 29177497A JP 29177497 A JP29177497 A JP 29177497A JP H11117019 A JPH11117019 A JP H11117019A
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- JP
- Japan
- Prior art keywords
- less
- heat
- working
- resistant
- phase
- 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.)
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- Heat Treatment Of Steel (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、エンジン用ボル
ト、エンジンバルブなどの耐熱部品の製造方法に関す
る。The present invention relates to a method for manufacturing heat-resistant parts such as engine bolts and engine valves.
【０００２】[0002]
【従来の技術】従来、エンジン部品、タービン部品、熱
交換器用部品、加熱炉部品、原子力用部品などの耐熱性
および耐食性などが要求される部品として、オーステナ
イト系耐熱鋼であるＪＩＳ ＳＵＨ６６０（C:≦0.08%
、Si: ≦1.0%、Mn: ≦2.0%、Ni:24.0 〜27.0% 、Cr:1
3.5 〜16.0% 、Mo:1.0〜1.5%、V:0.10〜0.50% 、Al: ≦
0.35% 、Ti:1.90 〜2.35% 、B:0.001 〜0.010%、残部F
e) が使用されている。このＳＵＨ６６０の使用上限温
度は７００℃であり、７００℃を超える使用条件の場合
にはＳＵＨ６６０より高いＮｉの合金鋼が用いられてい
る。この高Ｎｉ合金鋼を用いて使用上限温度８００℃の
耐熱部品を製造する場合、多くが熱間加工により成形
し、続いて固溶化熱処理、時効処理を行う製造工程が採
用されている。2. Description of the Related Art Conventionally, JIS SUH660 (C: austenitic heat-resistant steel) has been used as a component requiring heat resistance and corrosion resistance, such as an engine component, a turbine component, a heat exchanger component, a heating furnace component, and a nuclear component. ≤0.08%
, Si: ≤1.0%, Mn: ≤2.0%, Ni: 24.0-27.0%, Cr: 1
3.5 to 16.0%, Mo: 1.0 to 1.5%, V: 0.10 to 0.50%, Al: ≤
0.35%, Ti: 1.90-2.35%, B: 0.001-0.010%, balance F
e) is used. The upper-limit temperature for use of SUH660 is 700 ° C., and in the case of use conditions exceeding 700 ° C., a Ni alloy steel higher than SUH660 is used. In the case of manufacturing a heat-resistant component having an upper-limit use temperature of 800 ° C. using this high Ni alloy steel, a manufacturing process is often employed in which molding is performed by hot working, followed by solution heat treatment and aging treatment.
【０００３】上記従来の製造工程の熱間加工の代わりに
冷間加工または温間加工をし、続いて加工ひずみを残留
させたまま時効処理を行う工程にすれば、固溶化熱処理
を省略することができ、また成形後の寸法精度も向上す
るため仕上げ加工時における加工代が小さく加工時間も
短くすることができるので、耐熱部品のコストを低減す
ることができるとともに、製造時間を短縮することがで
きる。しかし、加工ひずみを残留させたまま直接時効処
理をすると、時効が促進されて短時間で急激に硬化する
が、長時間高温に曝されると強度の低下が大きく、η相
に変化しやすくなる問題点があった。[0003] If a process of performing cold working or warm working instead of the hot working of the conventional manufacturing process and then performing an aging treatment while leaving working strains is omitted, the solution heat treatment can be omitted. In addition, since the dimensional accuracy after molding is improved, the machining allowance at the time of finishing is small and the machining time can be shortened, so that the cost of heat-resistant parts can be reduced and the manufacturing time can be shortened. it can. However, when the direct aging treatment is performed with the processing strain remaining, aging is accelerated and hardens rapidly in a short time, but when exposed to a high temperature for a long time, the strength is greatly reduced and the η phase is easily changed. There was a problem.
【０００４】[0004]
【発明が解決しようとする課題】本発明は、耐熱鋼の素
材を溶体化処理したのち、冷間加工または温間加工を
し、続いて加工ひずみを残留させたまま時効処理をする
ことができ、且つ８００℃以上の使用雰囲気でも脆化相
のη相が析出することがない耐熱部品の製造方法を提供
することを課題とするものである。SUMMARY OF THE INVENTION According to the present invention, it is possible to perform a cold working or a warm working after a solution treatment of a heat resistant steel material, and then to carry out an aging treatment with a working strain remaining. It is another object of the present invention to provide a method for manufacturing a heat-resistant component in which the η phase of the embrittlement phase does not precipitate even in a use atmosphere of 800 ° C. or more.
【０００５】[0005]
【課題を解決するための手段】上記課題を解決するた
め、本発明者は、加工ひずみを残留させたまま直接時効
処理しても、その後の８００℃以上の使用雰囲気でη相
が析出しない耐熱鋼製の耐熱部品の製造方法について研
究していたところ、Ｆｅ─Ｎｉ−Ｃｒ系耐熱鋼のＴｉ／
Ａｌの原子比が１．０％を超えるとη相が析出するが、
１．０％以下であるとη相の析出が抑えられ、長時間高
温に曝されても強度の低下が小さいこと、および０．６
％未満であるとγ′相の析出が不十分で強度が確保でき
ないとの知見を得て本発明をなしたものである。Means for Solving the Problems To solve the above problems, the inventor of the present invention has proposed a method for preventing the η phase from precipitating in a subsequent use atmosphere of 800 ° C. or more even if the aging treatment is directly performed while the processing strain remains. While studying the manufacturing method of heat resistant parts made of steel, it was found that Ti /
When the atomic ratio of Al exceeds 1.0%, the η phase precipitates,
When the content is 1.0% or less, precipitation of the η phase is suppressed, and a decrease in strength is small even when exposed to a high temperature for a long time.
%, The present inventors have found that the precipitation of the γ 'phase is insufficient and the strength cannot be secured, and the present invention has been made.
【０００６】すなわち、本発明の耐熱部品の製造方法に
おいては、Ｃ：０．００５〜０．２０％、Ｓｉ：２．０
％以下、Ｍｎ：２．０％以下、Ｎｉ：３０〜４５％、Ｃ
ｒ：１０．０〜２５．０％、Ｎｂ＋Ｔａ：０．２〜１．
５％、Ｔｉ：１．２〜２．５未満％、Ａｌ：０．８〜
２．０％、Ｂ：０．００１〜０．０１％、必要に応じて
Ｍｏ：３．０％以下、Ｗ：３．０％以下、Ｖ：１．０％
以下、Ｃｏ：５．０％以下のうちの１種または２種以上
含有し、さらに必要に応じてＭｇ＋Ｃａ：０．００１〜
０．０１０％、残部Ｆｅおよび不可避的不純物からな
り、Ｔｉ／Ａｌの原子比を０．６〜１．０、必要に応じ
てＴｉ＋Ａｌ＋Ｎｂ＋Ｔａの原子％を４．０〜８．０％
とし、かつＣｏを含有させる場合にはＮｉ＋Ｃｏ：３
０．０〜４５．０％とした耐熱鋼の素材を溶体化処理し
たのち、冷間加工または温間加工により部品を製造し、
加工ひずみを残留したまま時効処理することである。That is, in the method for manufacturing a heat-resistant component of the present invention, C: 0.005 to 0.20%, Si: 2.0
%, Mn: 2.0% or less, Ni: 30 to 45%, C
r: 10.0-25.0%, Nb + Ta: 0.2-1.
5%, Ti: 1.2 to less than 2.5%, Al: 0.8 to
2.0%, B: 0.001 to 0.01%, Mo: 3.0% or less, W: 3.0% or less, V: 1.0% as required
Hereinafter, one or more of Co: 5.0% or less are contained, and Mg + Ca: 0.001 to
0.010%, the balance being Fe and unavoidable impurities. The atomic ratio of Ti / Al is 0.6 to 1.0, and the atomic% of Ti + Al + Nb + Ta is 4.0 to 8.0% as required.
And when Co is contained, Ni + Co: 3
After heat-treating a 0.04-45.0% heat-resistant steel material, manufacture parts by cold working or warm working.
Aging treatment is performed while the processing strain remains.
【０００７】以下本発明を詳細に説明する。先ず本発明
の耐熱鋼の成分組成を上記のように限定した理由を説明
する。 Ｃ：０．００５〜０．２０％ Ｃは、Ｔｉ、Ｎｂ、Ｃｒなどと結合して炭化物を形成す
ることにより合金の高温強度を改善するために含有させ
る元素で、０．００５％未満ではその効果がなく、また
０．２０％を超えると炭化物を多量に析出して加工性、
靭延性および耐食性を劣化するので、その含有範囲を
０．００５〜０．２０％とする。 Ｓｉ：２．０％以下 Ｓｉは、脱酸剤として有用であり、耐酸化性を改善する
元素であるが、２．０％を超えると加工性が低下するの
で、その含有量を２．０％以下とする。Hereinafter, the present invention will be described in detail. First, the reason why the composition of the heat-resistant steel of the present invention is limited as described above will be described. C: 0.005 to 0.20% C is an element contained to improve the high-temperature strength of the alloy by forming carbides by combining with Ti, Nb, Cr and the like. It has no effect, and if it exceeds 0.20%, a large amount of carbides precipitates out, resulting in workability,
Since the toughness and corrosion resistance deteriorate, the content range is set to 0.005 to 0.20%. Si: 2.0% or less Si is useful as a deoxidizing agent and is an element that improves oxidation resistance. However, if it exceeds 2.0%, workability is reduced. % Or less.
【０００８】Ｍｎ：２．０％以下 Ｍｎは、Ｓｉと同様に脱酸剤として含有させる元素であ
るが、２．０％を超えると加工性および高温酸化性を損
なうだけでなく、靭性を害するη相の析出を助長するの
で、その含有量を２．０％以下とする。 Ｎｉ：３０．０〜４５．０％ Ｎｉは、合金のマトリックスであるオーステナイト組織
を形成する元素であり、合金の耐熱性および耐食性を向
上し、また強化相であるγ′相を析出させる上で必要な
元素で、３０．０％未満では８００℃以上の高温強度が
得られず、また４５．０％を超えるとコストが高くなる
ので、その含有範囲を３０．０〜４５．０％とする。 Ｃｒ：１０．０〜２５．０％ Ｃｒは、合金の高温酸化および腐食を改善するために含
有させる元素で、１０％未満ではこのような効果を得る
ことができず、２５．０％を超えるとオーステナイト相
が不安定となり、脆化相であるσ相（ＦｅＣｒ）が析出
して合金の靭性を低下するので、その含有範囲を１０．
０〜２５．０％とする。なお、好ましい範囲は１２〜２
０％である。Mn: 2.0% or less Mn is an element to be contained as a deoxidizer like Si, but if it exceeds 2.0%, not only impairs workability and high-temperature oxidizability, but also impairs toughness. Since the precipitation of the η phase is promoted, the content is set to 2.0% or less. Ni: 30.0-45.0% Ni is an element forming an austenitic structure which is a matrix of the alloy, and improves the heat resistance and corrosion resistance of the alloy, and is used for precipitating a γ 'phase which is a strengthening phase. If it is a necessary element, if it is less than 30.0%, a high-temperature strength of 800 ° C. or more cannot be obtained, and if it exceeds 45.0%, the cost will be high. . Cr: 10.0-25.0% Cr is an element contained for improving high-temperature oxidation and corrosion of the alloy. If the content is less than 10%, such an effect cannot be obtained, and the content exceeds 25.0%. And the austenite phase become unstable, and the σ phase (FeCr), which is an embrittlement phase, precipitates and lowers the toughness of the alloy.
0 to 25.0%. The preferred range is 12 to 2
0%.
【０００９】Ｎｂ＋Ｔａ：０．２〜１．５％ ＮｂおよびＴａは、いずれもＮｉとともに重要な析出相
である金属間化合物のγ′相（γプライム相）であるＮ
ｉ3 （Ａｌ，Ｔｉ，Ｎｂ，Ｔａ）を形成し、そのγ′相
の析出によって合金の高温強度を効果的に高くすること
ができる元素で、この効果を得るために０．２％以上含
有させる必要があるが、１．５％を超えるとラーバス相
（Ｆｅ2 Ｎｂ）が多量に析出して高温強度および靭性を
低下するので、その含有範囲を ０．２〜１．５％とす
る。 Ｔｉ：１．２〜２．５未満％ Ｔｉは、Ａｌ，Ｎｂ，ＴａとともにＮｉと結合して高温
強度を向上させるのに有効なγ′相を形成する元素で、
その含有量が１．２％未満であるとγ′の固溶温度が低
下し、２．５％以上になるとη相（Ｎｉ3 Ｔｉ）が析出
して高温強度および靭性を低下するので、その含有範囲
を１．２〜２．５未満％とする。Nb + Ta: 0.2-1.5% Nb and Ta are both N and γ ′ phase (γ prime phase) of an intermetallic compound which is an important precipitation phase together with Ni.
An element that forms i 3 (Al, Ti, Nb, Ta) and can effectively increase the high-temperature strength of the alloy by the precipitation of its γ ′ phase. To obtain this effect, the content is 0.2% or more. However, if the content exceeds 1.5%, a large amount of the Lavas phase (Fe 2 Nb) precipitates to lower the high-temperature strength and toughness, so the content range is set to 0.2 to 1.5%. Ti: 1.2 to less than 2.5% Ti is an element that combines with Ni, Al, Nb, and Ta to form a γ ′ phase that is effective for improving high-temperature strength.
If the content is less than 1.2%, the solid solution temperature of γ 'is lowered, and if it is 2.5% or more, η phase (Ni 3 Ti) is precipitated to lower the high-temperature strength and toughness. The content range is set to 1.2 to less than 2.5%.
【００１０】Ａｌ：０．８〜２．０％ Ａｌは、Ｎｉと結合してγ′相を形成する最も重要な元
素で、０．８％未満であるとγ′相の析出が不十分で高
温強度が確保できず、２．０％を超えると合金の熱間加
工性が低下するので、その含有範囲を０．８〜２．０％
とする。好ましい範囲は１．２〜１．６未満％である。 Ｂ：０．００１〜０．０１％ Ｂは、結晶粒界に偏析して粒界を強化する元素で、この
効果を得るために０．００１％以上含有させる必要があ
るが、０．０１％を超えると熱間加工性を損なうので、
その含有範囲を０．００１〜０．０１％とする。 Ｍｏ：３．０％以下、Ｗ：３．０％以下、Ｖ：１．０％
以下 Ｍｏ、Ｗ、Ｖは、固溶強化により高温強度を向上させる
元素で、ＭｏおよびＷについては３％を超えて、Ｖは１
％を超えて含有しても効果の向上が少なく、またコスト
の上昇および加工性を低下するので、その含有量をＭｏ
を３．０％以下、Ｗを３．０％以下、Ｖを１．０％以下
とする。Al: 0.8-2.0% Al is the most important element that combines with Ni to form a γ ′ phase. If it is less than 0.8%, the precipitation of the γ ′ phase is insufficient. High temperature strength cannot be secured, and if it exceeds 2.0%, the hot workability of the alloy decreases, so the content range is 0.8 to 2.0%.
And A preferred range is from 1.2 to less than 1.6%. B: 0.001 to 0.01% B is an element that segregates at crystal grain boundaries and strengthens the grain boundaries. To obtain this effect, it is necessary to contain 0.001% or more, but 0.01%. If it exceeds, the hot workability is impaired,
The content range is 0.001 to 0.01%. Mo: 3.0% or less, W: 3.0% or less, V: 1.0%
Mo, W, and V are elements that improve high-temperature strength by solid solution strengthening. Mo and W exceed 3%, and V is 1
%, The effect is little improved, the cost is increased and the processability is reduced.
Is 3.0% or less, W is 3.0% or less, and V is 1.0% or less.
【００１１】Ｃｏ：５．０％以下 Ｎｉ＋Ｃｏ：３０．０〜４５．０％ Ｃｏは、Ｎｉとほぼ同じような作用がある元素で、Ｎｉ
を一部置換する形で合金に含有させることができる。す
なわちＮｉ＋Ｃｏ：３０．０〜４５．０％の条件を満た
す範囲でＣｏを含有させることができる。しかしＣｏは
Ｎｉに比較して高価な元素であるので、上限を５．０％
とする。 Ｍｇ＋Ｃａ：０．００１〜０．０１０％ ＭｇおよびＣａは、溶解時に脱酸および脱硫元素として
添加する元素で、熱間加工性を改善する効果がある。こ
の効果が現れるのは０．００１％からであり、０．０１
０％を超えて含有させるとかえって熱間加工性を低下す
るので、その含有範囲を０．００１〜０．０１０％とす
る。Co: 5.0% or less Ni + Co: 30.0-45.0% Co is an element having almost the same effect as Ni.
Can be contained in the alloy in such a way that it is partially substituted. That is, Co can be contained in a range satisfying the condition of Ni + Co: 30.0 to 45.0%. However, since Co is an expensive element compared to Ni, the upper limit is 5.0%.
And Mg + Ca: 0.001 to 0.010% Mg and Ca are elements added as deoxidizing and desulfurizing elements during dissolution, and have an effect of improving hot workability. This effect appears from 0.001% and 0.01%.
If the content exceeds 0%, the hot workability is rather deteriorated. Therefore, the content range is 0.001 to 0.010%.
【００１２】Ｔｉ／Ａｌの原子比：０．６〜１．０ Ｔｉ／Ａｌの原子比が０．６％未満であるとγ′相の析
出が不十分で強度が確保できず、また１．０％を超える
と脆化相のη相が析出し、長時間高温に曝されると強度
が低下するので、その範囲を０．６〜１．０とする。 Ｔｉ＋Ａｌ＋Ｎｂ＋Ｔａの原子％が４．０〜８．０％ Ｔｉ、Ａｌ、Ｎｂ、Ｔａは、何れもγ′相の構成元素
で、十分なＮｉ量が存在する場合、γ′相の析出量はこ
れらの元素の含有量の総和に比例する。そして合金の高
温強度はγ′相の析出量に比例する。本発明において合
金の７００℃以上での高温強度を十分発現させる上で
４．０原子％以上含有させる必要がある。一方、その総
和が８．０原子％を超えると強度は上昇するものの熱間
加工性は低下する。そこでこれらの元素の含有量の総和
を４．０〜８．０％とする。好ましくは５．０〜６．５
％である。 Ｐ，Ｓ，Ｏ，Ｎ これらの元素は、何れも不可避的不純物で、これらのう
ちＰおよびＳは熱間加工性を低下させ、またＯおよびＮ
は酸化物または窒化物を形成し、機械的性質を劣化する
ので、Ｐは０．０２％以下、Ｓ，ＯおよびＮは０．０１
％以下にするのが好ましい。Atomic ratio of Ti / Al: 0.6 to 1.0 When the atomic ratio of Ti / Al is less than 0.6%, the precipitation of the γ 'phase is insufficient and the strength cannot be secured. If it exceeds 0%, the embrittlement phase η phase will precipitate, and if it is exposed to a high temperature for a long time, the strength will decrease, so the range is set to 0.6 to 1.0. The atomic percentage of Ti + Al + Nb + Ta is 4.0 to 8.0%. Ti, Al, Nb, and Ta are all constituent elements of the γ ′ phase, and when there is a sufficient amount of Ni, the precipitation amount of the γ ′ phase is It is proportional to the sum of the element contents. The high temperature strength of the alloy is proportional to the amount of the γ 'phase precipitated. In the present invention, it is necessary to contain 4.0 atomic% or more in order to sufficiently develop the high-temperature strength of the alloy at 700 ° C. or more. On the other hand, if the total exceeds 8.0 atomic%, the strength increases but the hot workability decreases. Therefore, the sum of the contents of these elements is set to 4.0 to 8.0%. Preferably 5.0 to 6.5
%. P, S, O, N These elements are all unavoidable impurities, of which P and S decrease hot workability, and O and N
Forms oxides or nitrides and deteriorates mechanical properties, so that P is 0.02% or less, and S, O and N are 0.01% or less.
% Is preferred.
【００１３】次に、本発明の素材の製造方法、加工およ
び熱処理について説明する。本発明の耐熱部品の製造方
法は、上記成分組成の耐熱鋼の素材を溶体化処理したの
ち、冷間加工または温間加工により製品の部品を製造
し、加工ひずみを残留したまま時効処理することである
が、上記耐熱鋼の素材は、高周波誘導炉、真空溶解溶解
後エレクトロスラグ再溶解、大気溶解後真空エレクトロ
スラグ再溶解などによって溶解および精製後、鋳造して
製造されたインゴットを必要に応じてソーキングした
後、熱間鍛造や熱間圧延などの加工工程を通して製造さ
れるものである。さらに、本発明の耐熱部品の製造方法
の溶体化処理は、９５０〜１１５０℃で、素材の大きさ
にもよるが通常１０分〜４時間加熱後油冷または水冷す
ることである。Next, the method for manufacturing the material of the present invention, processing and heat treatment will be described. The method for producing a heat-resistant part of the present invention comprises, after solution-treating a heat-resistant steel material having the above-mentioned component composition, producing a product part by cold working or warm working, and subjecting the product to an aging treatment while processing strain remains. However, the above heat-resistant steel material is melted and refined in a high-frequency induction furnace, vacuum melting and melting of electroslag after melting, air melting and melting of vacuum electroslag after melting, etc. After being soaked, it is manufactured through a working process such as hot forging or hot rolling. Further, the solution treatment in the method for producing a heat-resistant component of the present invention is to perform oil cooling or water cooling after heating at 950 to 1150 ° C., usually for 10 minutes to 4 hours, depending on the size of the material.
【００１４】また、本発明の冷間加工または温間加工
は、製品の部品を製造するためのもので、加工率が小さ
いと時効の促進が小さく十分の強度が得られないので、
本発明の耐熱鋼においては３０％以上にすることが好ま
しい。また、本発明の時効処理は、６００〜８００℃
で、製品の大きさ、部品の種類および用途にもよるが通
常０．１〜２０時間加熱して行う。本発明の製造方法で
製造される耐熱部品は、ボルト、ナット、エンジンバル
ブ、板、ワイヤーなどのエンジン部品、タービン部品、
熱交換器用部品、加熱炉部品、原子力用部品などであ
る。The cold working or warm working of the present invention is for producing parts of a product. If the working ratio is small, the aging is not accelerated sufficiently and sufficient strength cannot be obtained.
In the heat-resistant steel of the present invention, the content is preferably 30% or more. The aging treatment of the present invention is performed at 600 to 800 ° C.
The heating is usually carried out for 0.1 to 20 hours, depending on the size of the product, the type of parts and the use. Heat-resistant parts manufactured by the manufacturing method of the present invention include engine parts such as bolts, nuts, engine valves, plates, and wires, turbine parts,
Parts for heat exchangers, parts for heating furnaces, parts for nuclear power, etc.
【００１５】[0015]
【発明の実施の形態】以下本発明を実施例により説明す
る。下記表１に示した成分組成の材料５０ｋｇを高周波
誘導炉で溶解および精製し、鋳造してインゴットを得
た。そしてこのインゴットを１１００℃で１６時間ソー
キングした後、引き続いて１１００〜９００℃の温度範
囲で鍛造、圧延して直径２５ｍｍの丸棒（本発明の素
材）とした。その丸棒を９７５℃で３０分間加熱後油冷
の条件で溶体化処理をし、その熱処理をした丸棒から直
径２４．０ｍｍ、高さ４５．０ｍｍの試験片を切り出し
た。そしてそれらの試験片を用いて、室温において絞り
６５％の前方押出し加工を行い、それらの試験片に７５
０℃×４時間、さらに長時間使用を想定して８００℃×
１００時間の時効処理をした。DESCRIPTION OF THE PREFERRED EMBODIMENTS The present invention will be described below with reference to embodiments. 50 kg of a material having a component composition shown in Table 1 below was melted and purified in a high-frequency induction furnace, and cast to obtain an ingot. The ingot was soaked at 1100 ° C. for 16 hours, and subsequently forged and rolled in a temperature range of 1100 to 900 ° C. to obtain a round bar having a diameter of 25 mm (material of the present invention). The round bar was heated at 975 ° C. for 30 minutes and then subjected to a solution treatment under oil-cooling conditions. A test piece having a diameter of 24.0 mm and a height of 45.0 mm was cut out from the heat-treated round bar. Then, using these test pieces, a front extrusion process of drawing 65% was performed at room temperature.
0 ° C x 4 hours, 800 ° C x for longer use
The aging treatment was performed for 100 hours.
【００１６】その後この時効処理をした試験片より硬さ
試験および引張り試験用の試験片を切り出して室温で硬
さ試験および８００℃で引張り試験を行った。その結果
を下記表２の本発明方法の欄に記載した。また同時に従
来の製造方法で製造した試験片、すなわち上記前方押出
し加工をした後に固溶化熱処理（９７５℃で３０分間加
熱後油冷）をし、その後７５０℃×４時間で時効処理を
し、さらに長時間使用を想定して８００℃×１００時間
の時効処理をした試験片も用意して同様な試験を行っ
た。その結果を下記表２の従来方法の欄に記載した。な
お、引張り試験は、ＪＩＳ ４号試験片を用いて８００
℃で行った。Thereafter, test specimens for a hardness test and a tensile test were cut out from the aged test specimens and subjected to a hardness test at room temperature and a tensile test at 800 ° C. The results are shown in the column of the method of the present invention in Table 2 below. At the same time, a test piece manufactured by a conventional manufacturing method, that is, a solution heat treatment (heating at 975 ° C. for 30 minutes followed by oil cooling) after the above-mentioned forward extrusion, followed by an aging treatment at 750 ° C. × 4 hours, A similar test was performed by preparing a test piece that had been subjected to an aging treatment at 800 ° C. for 100 hours for long-term use. The results are shown in the column of the conventional method in Table 2 below. The tensile test was performed using a JIS No. 4 test piece at 800
C. was performed.
【００１７】[0017]
【表１】 [Table 1]
【００１８】[0018]
【表２】 [Table 2]
【００１９】これらの結果より、本発明の耐熱鋼の素材
を冷間加工後直接時効処理したものは、本発明の耐熱鋼
の素材を従来方法の冷間加工後に固溶化熱処理し、その
後時効処理したものより室温硬さが約１８〜３１％高く
なっており、また８００℃の引張強さが約３３〜４０％
高くなっている。さらに、本発明の耐熱鋼を冷間加工後
直接時効処理したものは、比較鋼のＴｉ／Ａｌの原子％
比が１．０を超えたものを冷間加工後直接時効処理した
ものより室温硬さが約１６〜４０％も高くなっており、
また８００℃の引張強さが約１９〜５４％も高くなって
いる。According to these results, the heat-resistant steel material of the present invention obtained by subjecting the material of the heat-resistant steel of the present invention to direct aging after cold working is subjected to a solution heat treatment after cold working of the heat-resistant steel material of the present invention, followed by aging treatment. The room temperature hardness is about 18 to 31% higher than that of the cured product, and the tensile strength at 800 ° C. is about 33 to 40%.
Is getting higher. Further, the heat-resistant steel of the present invention which was subjected to direct aging treatment after cold working was the atomic% of Ti / Al of the comparative steel.
The room temperature hardness is about 16 to 40% higher than that in which the ratio exceeds 1.0 and that subjected to direct aging after cold working.
Further, the tensile strength at 800 ° C. is as high as about 19 to 54%.
【００２０】また、本発明の耐熱鋼を冷間加工後直接時
効処理したものは、全てミクロ組織が正常であったが、
比較鋼を冷間加工後直接時効処理したもののＴｉ／Ａｌ
の原子％比が大きいものは、時効が進み過ぎたため脆化
相であるη相が析出し、またＴｉ／Ａｌの原子％比が小
さいものは、ミクロ組織が正常であるがγ′相の析出が
十分でないため本発明鋼より強度が低い。また、本発明
の耐熱鋼を冷間加工後直接時効処理したものは、比較鋼
のＴｉ／Ａｌの原子％比が１．０を超えたものを従来方
法で処理したものより室温硬さが１例を除いて高くなっ
ており、また８００℃の引張強さが約１０〜３８％高く
なっている。The microstructures of all of the heat-resisting steels of the present invention subjected to direct aging after cold working had normal microstructures.
Ti / Al after cold working and direct aging treatment of comparative steel
When the atomic% ratio of Ti is large, the aging phase is excessively advanced, and the η phase, which is an embrittlement phase, precipitates. When the atomic% ratio of Ti / Al is small, the microstructure is normal but the γ 'phase is precipitated. Is not enough, the strength is lower than that of the steel of the present invention. Further, the heat-resistant steel of the present invention, which had been subjected to direct aging treatment after cold working, had a room temperature hardness of 1 compared with that of a comparative steel having a Ti / Al atomic ratio of more than 1.0, which was treated by the conventional method. It is high except for the examples, and the tensile strength at 800 ° C. is about 10-38% higher.
【００２１】[0021]
【発明の効果】本発明の耐熱製品の製造方法は、上記構
成にしたことにより、固溶化熱処理をすることなく直接
時効をすることができるとともに、冷間加工または温間
加工により成形することにより寸法精度が向上するため
仕上げ加工時における加工代が小さく加工時間も短くな
るので、低コストで、かつ長時間８００℃以上に曝され
ても強度が低下しない耐熱部品を製造することができる
という優れた効果を奏する。According to the method for manufacturing a heat-resistant product of the present invention, the aging can be directly performed without performing the solution heat treatment by the above-described structure, and the heat-resistant product can be formed by cold working or warm working. Since the dimensional accuracy is improved, the machining allowance at the time of finish machining is small and the machining time is also short, so that it is possible to manufacture a heat-resistant component that is low in cost and does not decrease in strength even when exposed to 800 ° C. or more for a long time. It has the effect.
Claims (6)
〜０．２０％、Ｓｉ：２．０％以下、Ｍｎ：２．０％以
下、Ｎｉ：３０．０〜４５．０％、Ｃｒ：１０．０〜２
５．０％、Ｎｂ＋Ｔａ：０．２〜１．５％、Ｔｉ：１．
２〜２．５未満％、Ａｌ：０．８〜２．０％、Ｂ：０．
００１〜０．０１％、残部Ｆｅおよび不可避的不純物か
らなり、Ｔｉ／Ａｌの原子比が０．６〜１．０である耐
熱鋼の素材を溶体化処理したのち、冷間加工または温間
加工により部品を製造し、加工ひずみを残留したまま時
効処理することを特徴とする耐熱部品の製造方法。C: 0.005% by weight (the same applies hereinafter)
0.20%, Si: 2.0% or less, Mn: 2.0% or less, Ni: 30.0 to 45.0%, Cr: 10.0 to 2
5.0%, Nb + Ta: 0.2-1.5%, Ti: 1.
2 to less than 2.5%, Al: 0.8 to 2.0%, B: 0.
001-0.01%, balance Fe and unavoidable impurities, heat treatment steel material having Ti / Al atomic ratio of 0.6-1.0, and then cold working or warm working A method for producing a heat-resistant component, comprising: producing a component by aging treatment while retaining processing strain.
２．０％以下、Ｍｎ：２．０％以下、Ｎｉ：３０．０〜
４５．０％、Ｃｒ：１０．０〜２５．０％、Ｎｂ＋Ｔ
ａ：０．２〜１．５％、Ｔｉ：１．２〜２．５未満％、
Ａｌ：０．８〜２．０％、Ｂ：０．００１〜０．０１
％、およびＭｏ：３．０％以下、Ｗ：３．０％以下、
Ｖ：１．０％以下の１種または２種以上、残部Ｆｅおよ
び不可避的不純物からなり、Ｔｉ／Ａｌの原子比が０．
６〜１．０である耐熱鋼の素材を溶体化処理したのち、
冷間加工または温間加工により部品を製造し、加工ひず
みを残留したまま時効処理することを特徴とする耐熱部
品の製造方法。2. C: 0.005 to 0.20%, Si:
2.0% or less, Mn: 2.0% or less, Ni: 30.0 to
45.0%, Cr: 10.0 to 25.0%, Nb + T
a: 0.2 to 1.5%, Ti: 1.2 to less than 2.5%,
Al: 0.8 to 2.0%, B: 0.001 to 0.01
%, And Mo: 3.0% or less, W: 3.0% or less,
V: One or more of 1.0% or less, the balance being Fe and unavoidable impurities, and an atomic ratio of Ti / Al of 0.1%.
After heat-treating a heat-resistant steel material of 6 to 1.0,
A method for producing a heat-resistant component, comprising: producing a component by cold working or warm working; and performing aging treatment while maintaining processing strain.
２．０％以下、Ｍｎ：２．０％以下、Ｎｉ：３０．０〜
４５．０％、Ｃｒ：１０．０〜２５．０％、Ｎｂ＋Ｔ
ａ：０．２〜１．５％、Ｔｉ：１．２〜２．５未満％、
Ａｌ：０．８〜２．０％、Ｂ：０．００１〜０．０１
％、およびＭｏ：３．０％以下、Ｗ：３．０％以下、
Ｖ：１．０％以下のうちの１種または２種以上、Ｃｏ：
５．０％以下、残部Ｆｅおよび不可避的不純物からな
り、Ｔｉ／Ａｌの原子比が０．６〜１．０、で、かつＮ
ｉ＋Ｃｏ：３０．０〜４５．０％であることを特徴とす
る耐熱鋼の素材を溶体化処理したのち、冷間加工または
温間加工により部品を製造し、加工ひずみを残留したま
ま時効処理することを特徴とする耐熱部品の製造方法。3. C: 0.005 to 0.20%, Si:
2.0% or less, Mn: 2.0% or less, Ni: 30.0 to
45.0%, Cr: 10.0 to 25.0%, Nb + T
a: 0.2 to 1.5%, Ti: 1.2 to less than 2.5%,
Al: 0.8 to 2.0%, B: 0.001 to 0.01
%, And Mo: 3.0% or less, W: 3.0% or less,
V: one or more of 1.0% or less, Co:
5.0% or less, the balance being Fe and unavoidable impurities, the atomic ratio of Ti / Al is 0.6 to 1.0, and N
After heat-treating a heat-resistant steel material characterized by i + Co: 30.0 to 45.0%, a component is manufactured by cold working or warm working, and then subjected to aging treatment while maintaining working strain. A method for producing a heat-resistant component, comprising:
０．０１０％含有するものであることを特徴とする請求
項１ないし請求項３のいずれか１項記載の耐熱部品の製
造方法。4. The heat-resistant steel contains Mg + Ca in an amount of 0.001 to 0.001.
The method for producing a heat-resistant component according to any one of claims 1 to 3, wherein the content is 0.010%.
原子％が４．０〜８．０％であることを特徴とする請求
項１ないし請求項４のいずれか１項記載の耐熱部品の製
造方法。5. The method for manufacturing a heat-resistant component according to claim 1, wherein the heat-resistant steel has an atomic percentage of Ti + Al + Nb + Ta of 4.0 to 8.0%.
３０％以上であることを特徴とする請求項１ないし請求
項５のいずれか１項記載の耐熱部品の製造方法。6. The method for manufacturing a heat-resistant component according to claim 1, wherein the degree of cold working or warm working is 30% or more.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP29177497A JPH11117019A (en) | 1997-10-09 | 1997-10-09 | Production of heat resistant parts |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP29177497A JPH11117019A (en) | 1997-10-09 | 1997-10-09 | Production of heat resistant parts |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH11117019A true JPH11117019A (en) | 1999-04-27 |
Family
ID=17773257
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP29177497A Pending JPH11117019A (en) | 1997-10-09 | 1997-10-09 | Production of heat resistant parts |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH11117019A (en) |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2002016661A3 (en) * | 2000-08-24 | 2002-06-06 | Inco Alloys Int | Low cost, corrosion and heat resistant alloy for diesel engine valves |
| JP2009542919A (en) * | 2006-07-07 | 2009-12-03 | イートン コーポレーション | Abrasion resistant heat resistant alloy |
| EP2806047A1 (en) * | 2013-05-21 | 2014-11-26 | Daido Steel Co.,Ltd. | Precipitation hardened FE-NI alloy |
| JP2015030873A (en) * | 2013-08-01 | 2015-02-16 | 株式会社東芝 | Austenitic heat resistant steel and turbine component |
| JP2015183256A (en) * | 2014-03-25 | 2015-10-22 | 株式会社東芝 | Austenitic heat resistant steel and turbine component |
| CN108431258A (en) * | 2015-12-18 | 2018-08-21 | 博格华纳公司 | Include the wastegate component of novel alloy |
| CN110465667A (en) * | 2019-09-25 | 2019-11-19 | 广西科技大学 | A kind of turbocharger vanes and preparation method thereof |
-
1997
- 1997-10-09 JP JP29177497A patent/JPH11117019A/en active Pending
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2002016661A3 (en) * | 2000-08-24 | 2002-06-06 | Inco Alloys Int | Low cost, corrosion and heat resistant alloy for diesel engine valves |
| JP2009542919A (en) * | 2006-07-07 | 2009-12-03 | イートン コーポレーション | Abrasion resistant heat resistant alloy |
| EP2806047A1 (en) * | 2013-05-21 | 2014-11-26 | Daido Steel Co.,Ltd. | Precipitation hardened FE-NI alloy |
| JP2015030873A (en) * | 2013-08-01 | 2015-02-16 | 株式会社東芝 | Austenitic heat resistant steel and turbine component |
| JP2015183256A (en) * | 2014-03-25 | 2015-10-22 | 株式会社東芝 | Austenitic heat resistant steel and turbine component |
| CN108431258A (en) * | 2015-12-18 | 2018-08-21 | 博格华纳公司 | Include the wastegate component of novel alloy |
| JP2019505662A (en) * | 2015-12-18 | 2019-02-28 | ボーグワーナー インコーポレーテッド | Wastegate parts containing new alloys |
| US11306376B2 (en) | 2015-12-18 | 2022-04-19 | Borgwarner Inc. | Wastegate component comprising a novel alloy |
| CN110465667A (en) * | 2019-09-25 | 2019-11-19 | 广西科技大学 | A kind of turbocharger vanes and preparation method thereof |
| CN110465667B (en) * | 2019-09-25 | 2022-04-22 | 广西科技大学 | Turbocharger blade and preparation method thereof |
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