JP3084764B2 - Method for manufacturing Ni-based superalloy member - Google Patents
Method for manufacturing Ni-based superalloy memberInfo
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- JP3084764B2 JP3084764B2 JP03043696A JP4369691A JP3084764B2 JP 3084764 B2 JP3084764 B2 JP 3084764B2 JP 03043696 A JP03043696 A JP 03043696A JP 4369691 A JP4369691 A JP 4369691A JP 3084764 B2 JP3084764 B2 JP 3084764B2
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- based superalloy
- alloy
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Description
【０００１】[0001]
【産業上の利用分野】本発明は、高温における強度，靭
性もしくは耐熱性や耐食性などに優れていることが要求
される素材，部品ないしは製品、例えば航空機エンジン
のタービン部材や原子炉容器内の締結ボルト等の耐熱も
しくは耐食部材として利用するのに適したＮｉ基超合金
部材を製造するのに利用されるＮｉ基超合金部材の製造
方法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a material, part or product required to have excellent strength, toughness, heat resistance and corrosion resistance at high temperatures, for example, fastening in a turbine member of an aircraft engine or a reactor vessel. The present invention relates to a method for manufacturing a Ni-based superalloy member used for manufacturing a Ni-based superalloy member suitable for use as a heat-resistant or corrosion-resistant member such as a bolt.
【０００２】[0002]
【従来の技術】近年、ジェットエンジンやガスタービン
などの動力機関においては、その高性能化および高効率
化などのために、タービン各部の高温化が不可欠となっ
ており、このような高温化に耐えうるタービン部材の開
発が求められるようになっている。2. Description of the Related Art In recent years, in power engines such as jet engines and gas turbines, it has become indispensable to raise the temperature of each part of the turbine in order to achieve higher performance and higher efficiency. The development of a durable turbine member has been required.
【０００３】この種のタービン部材に要求される特性
は、高温での遠心力に耐えうる優れたクリープ破断強
度，疲労強度ならびに靭性，高温燃焼ガス雰囲気に対す
る耐熱性や耐食性などである。The characteristics required of this kind of turbine member are excellent creep rupture strength, fatigue strength and toughness capable of withstanding centrifugal force at high temperatures, heat resistance to high-temperature combustion gas atmosphere, corrosion resistance and the like.
【０００４】このような用途に適する材料としては、従
来より、Ｎｉ基超合金が多く採用されており、溶製した
Ｎｉ基超合金の溶湯を鋳造して製造するようにしてい
た。[0004] As a material suitable for such an application, a Ni-based superalloy has been conventionally employed in many cases, and is produced by casting a molten Ni-based superalloy.
【０００５】[0005]
【発明が解決しようとする課題】しかしながら、従来の
Ｎｉ基超合金部材の鋳造による製造に際しては、Ｎｉ基
超合金溶湯の凝固条件を格別コントロールすることなし
に鋳造を行っていたため、鋳造組織には、凝固偏析によ
って、（Ｆｅ，Ｃｒ，Ｎｉ）2 （Ｍｏ，Ｔｉ，Ｎｂ）で
あらわされる六方晶の金属間化合物であるＬａｖｅｓ
（ラーベス）相がデンドライト境界に形成されることが
あり、このようなＬａｖｅｓ相が形成されたときにはＮ
ｉ基超合金部材の延性等が低下することがあるという問
題点があり、このような問題点を解決することが課題と
して存在していた。However, in the production of a conventional Ni-base superalloy member by casting, the casting is performed without particularly controlling the solidification conditions of the molten Ni-base superalloy. Laves, a hexagonal intermetallic compound represented by (Fe, Cr, Ni) 2 (Mo, Ti, Nb) by solidification segregation
(Laves) phase may be formed at the dendrite boundary, and when such a Laves phase is formed, N
There is a problem that the ductility and the like of the i-based superalloy member may be reduced, and solving such a problem has been a problem.
【０００６】[0006]
【発明の目的】本発明は、上記した従来の課題を解決す
るためになされたもので、鋳造により製造されたＮｉ基
超合金部材（素材，部品，製品等）の延性等の低下を防
止し、延性等のより一層の向上をはかることが可能であ
るＮｉ基超合金部材を製造できるようにすることを目的
としている。SUMMARY OF THE INVENTION The present invention has been made to solve the above-mentioned conventional problems, and it is intended to prevent a decrease in ductility and the like of a Ni-based superalloy member (material, part, product, etc.) manufactured by casting. It is an object of the present invention to manufacture a Ni-based superalloy member capable of further improving ductility and the like.
【０００７】[0007]
【課題を解決するための手段】本発明に係わるＮｉ基超
合金部材の製造方法は、Ｎｉ基超合金部材を鋳造により
製造するに際し、Ｎｉ基超合金溶湯の凝固速度Ｒｃｍ／
ｈと、凝固界面の温度勾配Ｇ℃／ｃｍとの関係が、Ｇ／
Ｒ≧０．５℃・ｈ／ｃｍ2 を満足する状態で鋳造を行う
構成としたことを特徴としており、実施態様において
は、Ｎｉ基超合金溶湯の凝固速度Ｒｃｍ／ｈと、凝固界
面の温度勾配Ｇ℃／ｃｍとの関係が、Ｇ／Ｒ≧１．０℃
・ｈ／ｃｍ2 を満足する状態で鋳造を行う構成としたこ
とを特徴としており、同じく実施態様においては、Ｎｉ
基超合金が単結晶用合金である構成としたり、あるいは
等軸晶用合金ないしは一方向凝固柱状晶用合金である構
成としたことを特徴としており、同じく実施態様におい
ては、Ｎｉ基超合金が、 Ｃｒ：１１〜２３重量％、 Ｔｉ：０．５〜４．０重量％、 を必須元素として含み、 Ｃｏ：２０重量％以下、 Ｗ：６重量以下％およびＭｏ：１０重量％以下のうちの
１種または２種、 Ｎｂ：１．０〜６．５重量％、 Ｔａ：２．０重量％以下、 Ａｌ：０．２〜４．０重量％、 Ｆｅ：３７重量％以下、 を選択元素として含み、残部Ｎｉおよび不純物よりなる
構成としたり、あるいは単結晶化の場合を考慮して粒界
強化元素等の規定を緩めて、 Ｃ：０．１５重量％以下、 Ｂ：０．０１重量％以下、 Ｚｒ：０．３０％重量％以下、 に規制した構成としたことを特徴としており、上記した
Ｎｉ基超合金部材の製造方法に係わる発明の構成を前述
した従来の課題を解決するための手段としている。According to the method of manufacturing a Ni-based superalloy member according to the present invention, a solidification rate of a molten Ni-based superalloy Rcm /
h and the temperature gradient of the solidification interface G ° C./cm is G /
It is characterized in that casting is performed in a state of satisfying R ≧ 0.5 ° C. · h / cm 2. In an embodiment, the solidification rate Rcm / h of the molten Ni-base superalloy and the temperature of the solidification interface The relationship with the gradient G ° C./cm is G / R ≧ 1.0 ° C.
H / cm 2 , casting is performed in a state satisfying h / cm 2.
The base superalloy may be configured to be a single crystal alloy, or may be configured to be an equiaxed crystal alloy or a unidirectionally solidified columnar crystal alloy.In the same embodiment, the Ni-based superalloy is , Cr: 11 to 23% by weight, Ti: 0.5 to 4.0% by weight, as essential elements, Co: 20% by weight or less, W: 6% by weight or less, and Mo: 10% by weight or less One or two kinds, Nb: 1.0 to 6.5% by weight, Ta: 2.0% by weight or less, Al: 0.2 to 4.0% by weight, Fe: 37% by weight or less, as selected elements C: 0.15% by weight or less, B: 0.01% by weight or less , Zr: 0.30% by weight or less. It is characterized by, and a means for solving the conventional problems described above and the configuration of the invention relating to a manufacturing method of a Ni-based super alloy member mentioned above.
【０００８】本発明に係わるＮｉ基超合金部材の製造方
法では、Ｎｉ基超合金溶湯の凝固速度Ｒｃｍ／ｈと、凝
固界面の温度勾配Ｇ℃／ｃｍとの関係が、Ｇ／Ｒ≧０．
５℃・ｈ／ｃｍ2 、より望ましくはＧ／Ｒ≧１．０℃・
ｈ／ｃｍ2 を満足する状態にして鋳造を行うようにして
いるが、この理由は、上記Ｇ／Ｒの値が０．５℃・ｈｃ
ｍ2 よりも小さいと、鋳造組織において、凝固偏析によ
って、（Ｆｅ，Ｃｒ，Ｎｉ）2 （Ｍｏ，Ｔｉ，Ｎｂ）で
あらわされる六方晶の金属間化合物であるＬａｖｅｓ
（ラーベス）相がデンドライト境界に形成される可能性
が大きくなり、この結果、Ｌａｖｅｓ相の形成により延
性等の低下などという不具合が生じるようになるためで
ある。In the method for manufacturing a Ni-base superalloy member according to the present invention, the relationship between the solidification rate Rcm / h of the molten Ni-base superalloy and the temperature gradient G ° C / cm at the solidification interface is G / R ≧ 0.
5 ° C. · h / cm 2 , more preferably G / R ≧ 1.0 ° C.
h / cm 2 is satisfied, the casting is performed because the value of G / R is 0.5 ° C. · hc
If it is smaller than m 2 , in the cast structure, Laves which is a hexagonal intermetallic compound represented by (Fe, Cr, Ni) 2 (Mo, Ti, Nb) due to solidification segregation.
This is because the possibility that a (Laves) phase is formed at the dendrite boundary increases, and as a result, problems such as a decrease in ductility due to the formation of the Laves phase occur.
【０００９】また、本発明に係わるＮｉ基超合金部材の
製造方法においては、Ｎｉ基超合金が単結晶用合金であ
るようにすることも必要に応じて望ましく、あるいは従
来より多用されている等軸晶用合金や一方向凝固柱状晶
用合金であるようにすることもできる。In the method of manufacturing a Ni-based superalloy member according to the present invention, it is desirable if necessary that the Ni-based superalloy is an alloy for a single crystal. It may be an alloy for axial crystals or an alloy for directionally solidified columnar crystals.
【００１０】このような前者に示した単結晶用Ｎｉ基超
合金よりなる単結晶体は、従来の普通鋳造等軸晶合金や
一方向凝固柱状晶合金と異なり、粒界がないために融点
直下で溶体化処理することが可能であり、凝固偏析を完
全に除去したγ相（不規則面心立方格子よりなるマトリ
ックス合金相），γ´相（Ｌ１2 型規則格子よりなる金
属間化合物相）ならびにγ´´相（ＤＯ22型規則格子よ
りなる金属間化合物相）からなる均質組織を得ることが
できるものとなっているので、高温でのクリープ破断強
度や疲労強度を低下させることなく耐熱性や耐食性をよ
り一層向上させることが可能である点で有利なものとな
る。Unlike the conventional ordinary cast equiaxed alloy and the unidirectionally solidified columnar alloy, the single crystal of the former Ni-base superalloy for a single crystal as described above does not have a grain boundary. Γ phase (matrix alloy phase composed of irregular face-centered cubic lattice) and γ ′ phase (intermetallic compound phase composed of L12 2- type ordered lattice) And a homogeneous structure composed of a γ ″ phase (intermetallic compound phase composed of DO 22 type superlattice) can be obtained, so that heat resistance can be maintained without lowering creep rupture strength or fatigue strength at high temperatures. And corrosion resistance can be further improved.
【００１１】本発明に係わるＮｉ基超合金部材の製造方
法において適用されるＮｉ基超合金としては、例えば、
Ｎｉマトリックス中にＣｒ，Ｃｏ，Ｍｏ，Ｗ，Ｎｂ，Ｔ
ａ，Ｔｉ，Ａｌ等を含有させたものがあり、商品名とし
ては、Ｉｎｃｏｌｏｙ，Ｉｎｃｏｎｅｌ，Ｍ２５２，Ｎ
ｉｍｏｎｉｃ，Ｐｙｒｏｍｅｔ，Ｒｅｆｒａｃｔｏｒ
ｙ，Ｒｅｎｅ，Ｕｄｉｍｅｔ，Ｕｎｉｔｅｍｐ，Ｗａｓ
ｐａｌｏｙなどと称されるものがある。The Ni-base superalloy applied in the method for manufacturing a Ni-base superalloy member according to the present invention includes, for example,
Cr, Co, Mo, W, Nb, T in Ni matrix
a, Ti, Al, etc., and the trade names are Incoloy, Inconel, M252, N
imonic, Pyromet, Refractor
y, Rene, Udimet, Unitemp, Was
There is one called "paloy".
【００１２】そして、具体的な合金組成例としては、次
に例示する化学成分組成を有するものが用いられる。As specific examples of alloy compositions, those having the following chemical component compositions are used.
【００１３】Ｃｒ：１１〜２３重量％ Ｃｒは合金の高温における耐熱性や耐食性を改善するの
に有効な元素であり、このような効果を得るためには１
１重量％以上とすることが望ましい。そして、Ｃｒ含有
量の増加に伴ってその効果は大きくなるが、多くなりす
ぎると固溶強化元素の固溶限を下げるとともに、脆化相
であるＴＣＰ相が析出して高温強度を害することがある
ため、２３重量％以下とすることが望ましい。Cr: 11 to 23% by weight Cr is an element effective for improving the heat resistance and corrosion resistance of the alloy at high temperatures.
It is desirable that the content be 1% by weight or more. The effect increases with an increase in the Cr content. However, if the Cr content is too high, the solid solubility limit of the solid solution strengthening element is lowered, and a TCP phase, which is an embrittlement phase, may precipitate and impair the high-temperature strength. Therefore, it is desirable that the content be 23% by weight or less.
【００１４】Ｃｏ：２０重量％以下 ＣｏはＮｉ基超合金部材の耐熱性や耐食性を向上させる
のに有効な元素であるので、２０重量％以下の範囲で含
有させることも望ましい。Co: 20% by weight or less Co is an element effective for improving the heat resistance and corrosion resistance of the Ni-base superalloy member, and therefore, it is desirable to contain Co in a range of 20% by weight or less.
【００１５】Ｗ：６重量％以下およびＭｏ：１０重量％
以下のうちの１種または２種 Ｗ，Ｍｏはマトリックスであるγ相に主として固溶し、
固溶強化によりクリープ強度および疲労強度を高めるの
に有効な元素である。そして、このような効果を十分に
得る必要があるときにはＷは１．０重量％以上，Ｍｏは
２．５重量％以上とすることが望ましい。しかし、Ｗ，
Ｍｏは部材の高温における耐食性を低下させたり、針状
のα−（Ｗ，Ｍｏ）が析出してクリープ強度，疲労強度
および靭性を低下させたりすることがあるため、Ｗは６
重量％以下、Ｍｏは１０重量％以下とすることが望まし
い。W: 6% by weight or less and Mo: 10% by weight
One or two of the following W and Mo are mainly dissolved in the matrix γ phase,
It is an effective element for increasing creep strength and fatigue strength by solid solution strengthening. When it is necessary to sufficiently obtain such an effect, it is preferable that W is 1.0% by weight or more and Mo is 2.5% by weight or more. But W,
Mo may reduce the corrosion resistance of the member at high temperatures, or may cause needle-like α- (W, Mo) to precipitate to lower the creep strength, fatigue strength and toughness.
% By weight and Mo by 10% by weight or less.
【００１６】Ｎｂ：１．０〜６．５重量％ Ｔａ：２．０重量％以下 Ｎｂ，Ｔａは、γ´相およびγ相´´に［Ｎｉ3 （Ａ
ｌ，Ｎｂ，Ｔａ）］の形で固溶して固溶強化することに
より、クリープ強度や疲労強度を向上させるが、このよ
うな効果を得る必要があるときにはＮｂ量を１．０重量
％以上とすることが望ましい。しかし、多すぎるとクリ
ープ強度，疲労強度を低下させる傾向となるのでＮｂは
６．５重量％以下、Ｔａは２．０重量％以下とすること
が望ましい。Nb: 1.0 to 6.5% by weight Ta: 2.0% by weight or less Nb, Ta is formed by adding [Ni 3 (A
l, Nb, Ta)] to improve the creep strength and fatigue strength by forming a solid solution and strengthening the solid solution. However, when it is necessary to obtain such an effect, the Nb content is increased to 1.0% by weight or more. It is desirable that However, if the content is too large, the creep strength and the fatigue strength tend to be reduced. Therefore, Nb is desirably 6.5% by weight or less and Ta is desirably 2.0% by weight or less.
【００１７】Ｔｉ：０．５〜４．０重量％ Ｔｉはγ´相およびγ´´相に［Ｎｉ3 （Ａｌ，Ｔ
ｉ）］の形で固溶することにより固溶強化するほか、合
金の高温における耐食性を改善する効果があるので０．
５重量％以上含有させることも望ましい。しかし、多量
に添加すると、耐食性が劣化する傾向となるため、４．
０重量％以下とすることが望ましい。Ti: 0.5 to 4.0% by weight Ti contains [Ni 3 (Al, T) in the γ ′ phase and the γ ″ phase.
i)] has the effect of improving the corrosion resistance of the alloy at high temperatures in addition to solid solution strengthening by dissolving in the form of 0).
It is also desirable to contain 5% by weight or more. However, if added in a large amount, the corrosion resistance tends to deteriorate.
It is desirably 0% by weight or less.
【００１８】Ａｌ：０．２〜４．０重量％ Ａｌは析出強化相であるγ´相［Ｎｉ3 Ａｌ］の構成元
素であり、Ａｌ添加による効果を得る必要があるときに
は０．２〜４．０重量％の範囲とすることが望ましい。Al: 0.2 to 4.0% by weight Al is a constituent element of the γ 'phase [Ni 3 Al] which is a precipitation strengthening phase. It is desirably in the range of 0.0% by weight.
【００１９】Ｆｅ：３７重量％以下 ＦｅはＮｉの代替元素として添加しうる元素であり、３
７重量％まではＮｉ基超合金の特性を大きく劣化させる
ことなしに含有させることが可能である。Fe: 37% by weight or less Fe is an element that can be added as an alternative element to Ni.
Up to 7% by weight can be contained without significantly deteriorating the properties of the Ni-based superalloy.
【００２０】Ｃ：０．１５重量％以下 Ｂ：０．０１重量％以下 Ｚｒ：０．３０重量％以下 これらの元素は従来の普通鋳造等軸晶合金および一方向
凝固柱状晶合金において粒界強化元素として用いられる
元素であるが、単結晶化した場合にはこれらの粒界強化
元素は必要なく、むしろ次に示すように有害元素となる
ため、適宜規制することも望ましい。C: 0.15% by weight or less B: 0.01% by weight or less Zr: 0.30% by weight or less These elements are used to strengthen grain boundaries in conventional ordinary cast equiaxed alloys and directionally solidified columnar alloys. It is an element used as an element. However, in the case of single crystallization, these grain boundary strengthening elements are not necessary, but rather become harmful elements as shown below, and therefore it is desirable to appropriately regulate them.
【００２１】Ｃは炭化物（ＴｉＣ，ＮｂＣ，ＴａＣ等）
を形成し、塊状に析出する。この炭化物は、合金の融点
に比べて溶融温度が低く、合金の融点直下で行う溶体化
処理では局部溶融を起こすため、容体化処理温度を上げ
ることができず、単結晶の容体化温度範囲を狭くするの
で、単結晶化する場合にはＣを０．１５重量％以下とす
ることも望ましい。C is a carbide (TiC, NbC, TaC, etc.)
Are formed and precipitate in a lump. The melting temperature of this carbide is lower than the melting point of the alloy, and the solution treatment performed immediately below the melting point of the alloy causes local melting. In order to make it narrow, it is also desirable to make C 0.15% by weight or less in the case of single crystallization.
【００２２】Ｂはホウ化物［（Ｃｒ，Ｎｉ，Ｔｉ，Ｍ
ｏ）3 Ｂ2］を形成し、合金の粒界に析出する。ホウ化
物も炭化物と同様に合金の融点に比べ低融点であり、単
結晶の溶体化処理温度を低下させ、溶体化処理温度範囲
を狭くするので、単結晶化する場合にはＢを０．０１重
量％以下とすることも望ましい。B is a boride [(Cr, Ni, Ti, M
o) 3 B 2 ] is formed and precipitates at the grain boundaries of the alloy. Borides, like carbides, also have a lower melting point than the alloy and lower the solution treatment temperature of the single crystal and narrow the solution treatment temperature range. It is also desirable that the content be not more than weight%.
【００２３】Ｚｒは合金の固相線温度を下げ、凝固温度
範囲を広くするため、単結晶化に対し有害であるので、
単結晶化する場合にはＺｒを０．３０重量％以下とする
ことも望ましい。Zr is harmful to single crystallization because it lowers the solidus temperature of the alloy and widens the solidification temperature range.
In the case of single crystallization, it is also desirable to make Zr 0.30% by weight or less.
【００２４】本発明に係わるＮｉ基超合金部材の製造方
法は、上記したＮｉ基超合金が適用されうるものであ
り、例えば、Ｉｎｃｏｎｅｌ系合金に適用する場合に、
Ｉｎｃｏｎｅｌ７１８をベースにしかつ単結晶化の場合
を考慮して粒界強化元素等の規定を緩めた合金を考慮し
たときには、Ｃｒ：１５．０〜２３．０重量％、Ｍｏ：
２．５〜３．５重量％、Ｎｂ：４．５〜５．５重量％、
Ｔｉ：０．５〜１．５重量％、Ａｌ：０．２〜０．９重
量％、Ｆｅ：１３．０〜２５．０重量％、Ｔａ：１．０
重量％以下、Ｚｒ：０．３重量％以下、Ｃ：０．１５重
量％以下、Ｂ：０．０１重量％以下、残部Ｎｉおよび不
純物よりなるＮｉ基超合金を用いることができる。The method of manufacturing a Ni-based superalloy member according to the present invention can be applied to the above-mentioned Ni-based superalloy. For example, when applied to an Inconel-based alloy,
When considering an alloy based on Inconel 718 and loosening the definition of the grain boundary strengthening element in consideration of the case of single crystallization, Cr: 15.0 to 23.0% by weight, Mo:
2.5 to 3.5% by weight, Nb: 4.5 to 5.5% by weight,
Ti: 0.5 to 1.5% by weight, Al: 0.2 to 0.9% by weight, Fe: 13.0 to 25.0% by weight, Ta: 1.0
It is possible to use a Ni-based superalloy consisting of not more than 0.3% by weight, not more than 0.3% by weight of Zr, not more than 0.15% by weight of C, not more than 0.01% by weight of B, and the balance of Ni and impurities.
【００２５】[0025]
【発明の作用】本発明に係わるＮｉ基超合金部材の製造
方法によれば、Ｎｉ基超合金部材を鋳造により製造する
に際し、Ｎｉ基超合金溶湯の凝固速度Ｒｃｍ／ｈと、凝
固界面の温度勾配Ｇ℃／ｃｍとの関係が、Ｇ／Ｒ≧０．
５℃・ｈ／ｃｍ2 を満足する状態で鋳造を行う構成と
し、凝固界面の温度勾配Ｇに対して合金溶湯の凝固速度
Ｒが大きくなり過ぎないようにしたから、鋳造後の組織
において凝固偏析により延性低下等の原因となる有害な
Ｌａｖｅｓ相がデンドライト境界に形成されがたくなく
なるので、Ｎｉ基超合金部材の延性等がより一層向上し
たものとなる。According to the method for producing a Ni-base superalloy member according to the present invention, when the Ni-base superalloy member is produced by casting, the solidification rate Rcm / h of the molten Ni-base superalloy and the temperature of the solidification interface are determined. The relationship with the gradient G ° C./cm is G / R ≧ 0.
Casting is performed in a state satisfying 5 ° C. · h / cm 2, and the solidification rate R of the molten alloy is not excessively increased with respect to the temperature gradient G at the solidification interface. As a result, a harmful Laves phase which causes a decrease in ductility is hardly formed at the boundary of the dendrite, so that the Ni-based superalloy member is further improved in ductility and the like.
【００２６】[0026]
【実施例】この実施例では、真空誘導溶解によって表１
に示す化学成分組成のＮｉ基超合金を用意した。EXAMPLES In this example, Table 1 was obtained by vacuum induction melting.
A Ni-base superalloy having the chemical composition shown in Table 1 was prepared.
【００２７】[0027]
【表１】 [Table 1]
【００２８】次に、上記Ｎｉ基超合金素材を切り出して
直径２０ｍｍの単結晶用鋳型に入れ、真空誘導溶解を行
った後、鋳造に際して一方向凝固させて単結晶体を製作
したが、この鋳造に際して、凝固速度Ｒｃｍ／ｈと、凝
固界面の温度勾配Ｇ℃／ｃｍとの関係で表わされる凝固
条件をコントロールした。Next, the above-mentioned Ni-base superalloy material was cut out, put into a single-crystal mold having a diameter of 20 mm, subjected to vacuum induction melting, and then unidirectionally solidified during casting to produce a single-crystal body. At this time, the solidification conditions represented by the relationship between the solidification rate Rcm / h and the temperature gradient G ° C / cm at the solidification interface were controlled.
【００２９】この結果、凝固条件とＬａｖｅｓ相との関
係は、図１に示すごとくであった。As a result, the relationship between the coagulation conditions and the Laves phase was as shown in FIG.
【００３０】図１に示すように、Ｇ／Ｒの値が小さくな
るとＬａｖｅｓ相の生成量が増加する傾向にあることが
認められ、Ｇ／Ｒ≧０．５°Ｃ・ｈ／ｃｍ2 とすること
によって、Ｌａｖｅｓ相が２体積％以下となり、従来の
凝固条件をコントロールしない場合に比べて延性をおよ
そ２０％向上させることができることが認められた。As shown in FIG. 1, when the value of G / R becomes small, it is recognized that the generation amount of the Laves phase tends to increase, so that G / R ≧ 0.5 ° C.h / cm 2 . As a result, it was recognized that the Laves phase became 2% by volume or less, and the ductility could be improved by about 20% as compared with the case where the conventional solidification conditions were not controlled.
【００３１】また、本発明に係わるＮｉ基超合金部材の
製造方法は、単結晶化させる場合だけでなく、等軸晶や
一方向凝固柱状晶組織とする場合にも上記Ｇ／Ｒの鋳造
条件とすることによって延性の向上を実現できることが
認められた。The method of manufacturing a Ni-based superalloy member according to the present invention is applicable not only to the case of single crystallization but also to the case of forming an equiaxed crystal or a directionally solidified columnar crystal structure. It has been recognized that the improvement in ductility can be realized by doing so.
【００３２】[0032]
【発明の効果】本発明に係わるＮｉ基超合金部材の製造
方法では、Ｎｉ基超合金部材を鋳造により製造するに際
し、Ｎｉ基超合金溶湯の凝固速度Ｒｃｍ／ｈと、凝固界
面の温度勾配Ｇ℃／ｃｍとの関係が、Ｇ／Ｒ≧０．５℃
・ｈ／ｃｍ2 を満足する状態で鋳造を行うようにしたか
ら、Ｎｉ基超合金部材（素材，部品，製品等）の延性等
をより一層向上させたものとすることが可能であるとい
う著しく優れた効果がもたらされる。According to the method for manufacturing a Ni-based superalloy member according to the present invention, when the Ni-based superalloy member is manufactured by casting, the solidification speed Rcm / h of the molten Ni-based superalloy and the temperature gradient G at the solidification interface are obtained. G / R ≧ 0.5 ° C.
・ Since casting is performed in a state where h / cm 2 is satisfied, the ductility of Ni-base superalloy members (materials, parts, products, etc.) can be further improved. Excellent effect is brought.
【図１】Ｎｉ基超合金溶湯の凝固速度Ｒ（ｃｍ／ｈ）と
凝固界面の温度勾配Ｇ（°Ｃ／ｃｍ）との比であるＧ／
Ｒ（°Ｃ・ｈ／ｃｍ2 ）とＬａｖｅｓ相の形成量との関
係を調べた結果を例示するグラフである。FIG. 1 shows a ratio G /, which is a ratio between a solidification rate R (cm / h) of a molten Ni-base superalloy and a temperature gradient G (° C./cm) at a solidification interface.
4 is a graph illustrating the result of examining the relationship between R (° C. h / cm 2 ) and the amount of formation of a Laves phase.
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 平２−301538（ＪＰ，Ａ) 特開 昭62−247043（ＪＰ，Ａ) 特開 平１−188645（ＪＰ，Ａ) 特開 昭64−62446（ＪＰ，Ａ) 特開 昭62−170445（ＪＰ，Ａ) 特開 昭53−89820（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C22C 19/05 B22D 21/00 B22D 27/04 ──────────────────────────────────────────────────続 き Continuation of the front page (56) References JP-A-2-301538 (JP, A) JP-A-62-270443 (JP, A) JP-A-1-188645 (JP, A) JP-A 64-64 62446 (JP, A) JP-A-62-170445 (JP, A) JP-A-53-89820 (JP, A) (58) Fields investigated (Int. Cl. 7 , DB name) C22C 19/05 B22D 21 / 00 B22D 27/04
Claims (5)
に際し、Ｎｉ基超合金溶湯の凝固速度Ｒｃｍ／ｈと、凝
固界面の温度勾配Ｇ℃／ｃｍとの関係が、Ｇ／Ｒ≧０．
５℃・ｈ／ｃｍ2 を満足する状態で鋳造を行うことを特
徴とするＮｉ基超合金部材の製造方法。When producing a Ni-base superalloy member by casting, the relationship between the solidification rate Rcm / h of the molten Ni-base superalloy and the temperature gradient G ° C / cm at the solidification interface is G / R ≧ 0.
A method for producing a Ni-based superalloy member, wherein casting is performed under a condition of 5 ° C. · h / cm 2 .
と、凝固界面の温度勾配Ｇ℃／ｃｍとの関係が、Ｇ／Ｒ
≧１．０℃・ｈ／ｃｍ2 を満足する状態で鋳造を行う請
求項１に記載のＮｉ基超合金部材の製造方法。2. Solidification rate Rcm / h of molten Ni-base superalloy
And the temperature gradient G ° C / cm at the solidification interface is G / R
The method for producing a Ni-based superalloy member according to claim 1, wherein the casting is performed in a state satisfying ≧ 1.0 ° C · h / cm 2 .
項１または２に記載のＮｉ基超合金部材の製造方法。3. The method for producing a Ni-based superalloy member according to claim 1, wherein the Ni-based superalloy is an alloy for a single crystal.
１種または２種、 Ｎｂ：１．０〜６．５重量％、 Ｔａ：２．０重量％以下、 Ａｌ：０．２〜４．０重量％、 Ｆｅ：３７重量％以下、を選択元素として含み、残部Ｎ
ｉおよび不純物よりなる請求項１，２または３に記載の
Ｎｉ基超合金部材の製造方法。4. An Ni-based superalloy containing Cr: 11 to 23% by weight, Ti: 0.5 to 4.0% by weight as essential elements, Co: 20% by weight or less, W: 6% by weight or less And Mo: one or two of 10% by weight or less, Nb: 1.0 to 6.5% by weight, Ta: 2.0% by weight or less, Al: 0.2 to 4.0% by weight, Fe : 37% by weight or less as the selected element, and the balance N
The method for producing a Ni-based superalloy member according to claim 1, 2 or 3, comprising i and impurities.
法。5. The Ni-based superalloy member according to claim 4, wherein in the impurities, C: 0.15% by weight or less, B: 0.01% by weight or less, Zr: 0.30% by weight or less. Manufacturing method.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP03043696A JP3084764B2 (en) | 1991-03-08 | 1991-03-08 | Method for manufacturing Ni-based superalloy member |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP03043696A JP3084764B2 (en) | 1991-03-08 | 1991-03-08 | Method for manufacturing Ni-based superalloy member |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH04280938A JPH04280938A (en) | 1992-10-06 |
| JP3084764B2 true JP3084764B2 (en) | 2000-09-04 |
Family
ID=12670996
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP03043696A Expired - Fee Related JP3084764B2 (en) | 1991-03-08 | 1991-03-08 | Method for manufacturing Ni-based superalloy member |
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| Country | Link |
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Families Citing this family (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP3209902B2 (en) * | 1995-11-06 | 2001-09-17 | キャノン・マスキーガン・コーポレーション | High temperature corrosion resistant single crystal nickel-based superalloys |
| CN1059473C (en) * | 1997-05-28 | 2000-12-13 | 冶金工业部钢铁研究总院 | High temperature alloy for heating furnace |
| US6364000B2 (en) * | 1997-09-23 | 2002-04-02 | Howmet Research Corporation | Reinforced ceramic shell mold and method of making same |
| JP4154480B2 (en) * | 2002-08-08 | 2008-09-24 | 独立行政法人産業技術総合研究所 | Heat-resistant magnesium alloy and method for producing the same |
| US7156932B2 (en) * | 2003-10-06 | 2007-01-02 | Ati Properties, Inc. | Nickel-base alloys and methods of heat treating nickel-base alloys |
| US8512485B2 (en) * | 2011-01-03 | 2013-08-20 | General Electric Company | Alloy |
| JP5478601B2 (en) | 2011-12-22 | 2014-04-23 | 株式会社日立製作所 | Ni-based forged alloy and gas turbine using the same |
| CN102994809B (en) * | 2012-12-04 | 2015-04-15 | 西安热工研究院有限公司 | High-strength and corrosion-resistant nickel-iron-chromium-based high-temperature alloy and preparation method for same |
| US20150107072A1 (en) * | 2013-10-22 | 2015-04-23 | Kazim Ozbaysal | Fatigue resistant turbine through bolt |
| US10563293B2 (en) | 2015-12-07 | 2020-02-18 | Ati Properties Llc | Methods for processing nickel-base alloys |
| CN106399801A (en) * | 2016-09-18 | 2017-02-15 | 华能国际电力股份有限公司 | High-strength wear-resisting high-temperature alloy |
| CN106244856A (en) * | 2016-09-18 | 2016-12-21 | 华能国际电力股份有限公司 | A kind of Fe Ni matrix high temperature alloy |
| CN106636842A (en) * | 2016-09-18 | 2017-05-10 | 华能国际电力股份有限公司 | Precipitation strengthening high-carbon austenitic heat-resistance steel and preparation method thereof |
| CN113308635B (en) * | 2021-05-19 | 2021-11-30 | 北京科技大学 | Low-thermal-neutron absorption cross section entropy alloy with nanometer precipitated phase and preparation method |
-
1991
- 1991-03-08 JP JP03043696A patent/JP3084764B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH04280938A (en) | 1992-10-06 |
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