JP6769341B2 - Ni-based superalloy - Google Patents
Ni-based superalloy Download PDFInfo
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- JP6769341B2 JP6769341B2 JP2017033971A JP2017033971A JP6769341B2 JP 6769341 B2 JP6769341 B2 JP 6769341B2 JP 2017033971 A JP2017033971 A JP 2017033971A JP 2017033971 A JP2017033971 A JP 2017033971A JP 6769341 B2 JP6769341 B2 JP 6769341B2
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/057—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being less 10%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
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Description
この発明は、タービンホイール等の高温部品の材料に適用して好適なＮｉ基超合金に関する。 The present invention relates to a Ni-based superalloy suitable for use as a material for high temperature parts such as turbine wheels.
例えば、エンジンからの排気を受けて回転するタービンホイールは、高温下（例えば９５０℃程度の高温下）で高速回転するため（例えば毎分の回転数が数十万回）、高温強度特性に優れたものであることが求められる。
このため、タービンホイールの材料として高温強度特性に優れたＮｉ基超合金，特にインコネル７１３Ｃ、ＭＡＲ−Ｍ２４６を代表とするＮｉ基の鋳造合金が主として用いられてきた。
For example, a turbine wheel that rotates by receiving exhaust gas from an engine rotates at high speed at a high temperature (for example, at a high temperature of about 950 ° C.) (for example, the number of revolutions per minute is several hundred thousand times), and therefore has excellent high temperature strength characteristics. It is required to be a product.
For this reason, Ni-based superalloys having excellent high-temperature strength characteristics, particularly Ni-based cast alloys typified by Inconel 713C and MAR-M246, have been mainly used as materials for turbine wheels.
Ｎｉ基超合金における高温強度の強化機構としては、固溶強化と、γ′相（ガンマプライム相）の析出強化が用いられている。強化相として析出するγ′相（金属間化合物のＮｉ3（Ａｌ，Ｔｉ，Ｎｂ）の相）は高温まで安定であるため、鍛造によりタービンホイールを製造することが難しく、通常は主としてＮｉ基の鋳造合金を用いてタービンホイールを鋳造し、且つ鋳造まま（Ａｓ ｃａｓｔ状態）で使用している。 As a mechanism for strengthening high-temperature strength in Ni-based superalloys, solid solution strengthening and precipitation strengthening of the γ'phase (gamma prime phase) are used. Since the γ'phase (the phase of the intermetallic compound Ni 3 (Al, Ti, Nb)) precipitated as the strengthening phase is stable up to high temperatures, it is difficult to manufacture a turbine wheel by forging, and it is usually mainly Ni-based. The turbine wheel is cast using a cast alloy and is used as cast (As cast state).
ところで、タービンホイールのような回転体にあっては、部品の重量が大きくなると慣性重量が大きくなり、例えば、回転の立ち上がりのレスポンスが遅くなるため、軽量であること、即ち低比重であることが求められている。
上述のように強化機構として、固溶強化と、γ′相の析出強化とを用いるＮｉ基の合金にあっては、固溶強化元素の添加量が多いほど高温強度は向上するが、比重が大きくなってしまうため低比重化の要請に応えることが難しい。
また、固溶強化元素の添加量を少なくする一方、γ′相の生成元素の添加量を多くすることで、高温強度を維持しつつ比重を小さくすることも考えられるが、γ′相の析出量を増加させた場合には、鋳込時の凝固過程で鋳造割れが生じやすくなり、製造性が悪化してしまう問題があった。
By the way, in a rotating body such as a turbine wheel, when the weight of a part increases, the inertial weight increases, and for example, the response at the start of rotation becomes slow, so that the weight is light, that is, the specific gravity is low. It has been demanded.
As described above, in a Ni-based alloy that uses solid solution strengthening and precipitation strengthening of the γ'phase as a strengthening mechanism, the higher the amount of the solid solution strengthening element added, the higher the high temperature strength, but the specific gravity increases. It is difficult to meet the demand for lower specific gravity because it becomes large.
Further, it is conceivable to reduce the specific gravity while maintaining the high temperature strength by increasing the addition amount of the γ'phase-forming element while reducing the addition amount of the solid solution strengthening element, but the precipitation of the γ'phase When the amount is increased, there is a problem that casting cracks are likely to occur in the solidification process at the time of casting, and the manufacturability is deteriorated.
以上のように、タービンホイール等の高温部品の材料に用いられる合金にあっては、高温強度特性のほか、比重が小さいこと、鋳造性に優れていることが求められるが、これらの要求を十分に満たすＮｉ基合金は提供されていなかった。 As described above, alloys used as materials for high-temperature parts such as turbine wheels are required to have low specific gravity and excellent castability in addition to high-temperature strength characteristics, but these requirements are sufficient. No Ni-based alloy that meets the requirements has been provided.
尚、本発明に対する先行技術として、下記特許文献１には「ニッケル基合金」についての発明が示され、そこにおいて重量％で、Ｃｏ：１４〜１９％、Ｃｒ：１０〜１５％、Ｃ：０．０５〜０．２％、Ｍｏ：０〜３％、Ｔｉ：０．５〜３．０％で、残部Ｎｉからなる組成を有し、Ｔｉ／Ａｌ比を０．８５以下としたニッケル基合金が開示されている。しかしながらこの特許文献１には、鋳造性を向上させるための具体的な手段についての記載はなく、また、各実施例における成分組成は、いずれも本願発明のものとは異なっている。 As a prior art to the present invention, the following Patent Document 1 shows an invention relating to a "nickel-based alloy", wherein Co: 14 to 19%, Cr: 10 to 15%, C: 0 by weight. .05-0.2%, Mo: 0-3%, Ti: 0.5-3.0%, nickel-based alloy having a composition consisting of the balance Ni and a Ti / Al ratio of 0.85 or less. Is disclosed. However, this Patent Document 1 does not describe a specific means for improving castability, and the component compositions in each of the examples are different from those of the present invention.
本発明は以上のような事情を背景とし、比重が小さく、高温強度特性および鋳造性に優れたＮｉ基超合金を提供することを目的としてなされたものである。 Against the background of the above circumstances, the present invention has been made for the purpose of providing a Ni-based superalloy having a small specific gravity and excellent high-temperature strength characteristics and castability.
而して請求項１に記載のものは、質量％で、Ｃ：０．１〜０．３％、Ｃｒ：８．０〜１２．０％、Ｍｏ：１．０〜５．０％、Ｃｏ：１０〜２０％、Ｔａ：０．０１〜１．５０％、Ｔｉ：２．０〜４．２％、Ａｌ：５．０〜８．０％、Ｖ：０〜１．５％、Ｂ：０．００５〜０．０３０％、Ｚｒ：０．０５〜０．１５％を満たし、更に原子％で、Ｔｉ＋Ａｌ：１６．０〜２０．３％、Ｔｉ／Ａｌ：０．３以下、残部がＮｉ及び不可避的不純物の組成を有することを特徴とする。 The one according to claim 1 is by mass%, C: 0.1 to 0.3%, Cr: 8.0 to 12.0%, Mo: 1.0 to 5.0%, Co. : 10 to 20%, Ta: 0.01 to 1.50%, Ti: 2.0 to 4.2%, Al: 5.0 to 8.0%, V: 0 to 1.5%, B: Satisfying 0.005 to 0.030%, Zr: 0.05 to 0.15%, and further in atomic%, Ti + Al: 16.0 to 20.3%, Ti / Al: 0.3 or less, the balance is Ni. And have a composition of unavoidable impurities.
請求項２のものは、請求項１において、比重が７．９ｇ／ｃｍ3以下であることを特徴とする。 The second aspect of the present invention is characterized in that, in the first aspect, the specific gravity is 7.9 g / cm 3 or less.
請求項３のものは、請求項１，２の何れかにおいて、前記Ｔａが０．３〜０．８質量％であることを特徴とする。 The third aspect is characterized in that, in any one of the first and second aspects, the Ta is 0.3 to 0.8% by mass.
γ′相を強化相とするＮｉ基超合金では、γ′相の生成元素であるＡｌ及びＴｉの添加量を多くすることでγ′相の析出量が多くなること、更にこれとともにγ′相の析出温度が上昇することが知られている。
本発明者らは、Ａｌ＋Ｔｉの総量を高く維持したうえで、γ′相の析出温度を低下させる可能性を追求したところ、ＴｉとＡｌとの比率であるＴｉ／Ａｌ比を小さくすることでγ′相の析出温度が低下すること、更にＴｉ／Ａｌ比を０．３以下とすれば、鋳造の際に延性不足による割れが発生する温度領域でのγ′相の析出を抑制して、鋳造割れを防止することができることを見出した。
In a Ni-based superalloy having a γ'phase as a strengthening phase, the amount of precipitation of the γ'phase increases by increasing the amount of Al and Ti, which are the elements produced by the γ'phase, and the γ'phase is also increased. It is known that the precipitation temperature of aluminum increases.
The present inventors pursued the possibility of lowering the precipitation temperature of the γ'phase while maintaining a high total amount of Al + Ti, and found that by reducing the Ti / Al ratio, which is the ratio of Ti to Al, γ If the precipitation temperature of the'phase is lowered and the Ti / Al ratio is 0.3 or less, the precipitation of the γ'phase is suppressed in the temperature range where cracks occur due to insufficient ductility during casting, and casting is performed. We have found that cracking can be prevented.
本発明は、このような知見に基づいてなされたもので、固溶強化元素の添加量を少とする一方、γ′相を生成する元素であるＴｉ＋Ａｌの総量を１６．０％以上、且つＴｉ／Ａｌ比を０．３以下としたことを特徴としたものである。
本発明では、固溶強化元素の添加量を少とすることで、合金の低比重化を図る一方、γ′相を生成する元素であるＴｉ及びＡｌの添加量を増やすことで高温強度特性の確保を図っている。Ｔｉ及びＡｌの添加量を増やせば鋳造割れが生じやすくなり、鋳造性の悪化を招く虞もあるが、本発明ではＴｉ／Ａｌ比を０．３以下とすることでγ′相の析出温度の上昇を抑制し、凝固過程での鋳造割れの発生を抑えて鋳造性を確保している。
このように本発明のＮｉ基超合金は、比重が小さく、また高温強度特性および鋳造性に優れており、タービンホイール等の高温部品の材料として好適に用いることができる。
The present invention has been made based on such findings, and while the amount of the solid solution strengthening element added is small, the total amount of Ti + Al, which is an element that produces the γ'phase, is 16.0% or more, and Ti. The feature is that the / Al ratio is 0.3 or less.
In the present invention, the addition amount of the solid solution strengthening element is reduced to reduce the specific gravity of the alloy, while the addition amount of Ti and Al, which are elements that generate the γ'phase, is increased to obtain high-temperature strength characteristics. We are trying to secure it. If the amount of Ti and Al added is increased, casting cracks are likely to occur, which may lead to deterioration of castability. However, in the present invention, by setting the Ti / Al ratio to 0.3 or less, the precipitation temperature of the γ'phase is raised. Castability is ensured by suppressing the rise and suppressing the occurrence of casting cracks during the solidification process.
As described above, the Ni-based superalloy of the present invention has a small specific gravity, is excellent in high-temperature strength characteristics and castability, and can be suitably used as a material for high-temperature parts such as turbine wheels.
次に本発明におけるＮｉ基超合金の各成分の限定理由を以下に述べる。
Ｃ：０．１〜０．３％
Ｃは、炭化物を形成することで粒界強度を向上させる。十分な高温強度を得るには０．１％以上の添加を必要とする。但し、過剰な添加は粗大な共晶炭化物を形成し靭延性の低下を引き起こす為、上限を０．３％とする。
Next, the reasons for limiting each component of the Ni-based superalloy in the present invention will be described below.
C: 0.1 to 0.3%
C improves the grain boundary strength by forming carbides. Addition of 0.1% or more is required to obtain sufficient high temperature strength. However, excessive addition forms coarse eutectic carbides and causes a decrease in toughness, so the upper limit is set to 0.3%.
Ｃｒ：８．０〜１２．０％
Ｃｒは、表面にＣｒ2Ｏ3からなる緻密な酸化皮膜を形成して耐酸化性，高温耐食性を向上させる。このような特性を発揮させるには８．０％以上含有させることが必要である。
Ｃｒはその含有量が多いほど耐酸化性，高温耐食性に優れるものの、過剰な添加は相安定性を低下させ、延性，靭性が悪化するため、１２．０％を上限とする。より好ましい含有量は９．０〜１０．０％である。
Cr: 8.0-12.0%
Cr forms a dense oxide film made of Cr 2 O 3 on the surface to improve oxidation resistance and high temperature corrosion resistance. In order to exhibit such characteristics, it is necessary to contain 8.0% or more.
The higher the content of Cr, the better the oxidation resistance and high temperature corrosion resistance, but excessive addition lowers the phase stability and deteriorates the ductility and toughness, so the upper limit is 12.0%. A more preferable content is 9.0 to 10.0%.
Ｍｏ：１．０〜５．０％
Ｍｏは、オーステナイト相に固溶して固溶強化により母相を強化する効果がある。このためには、少なくとも１．０％以上含有させる必要がある。より好ましくは３．１％以上である。ただし、過剰な添加は相安定性を低下させ、延性，靭性が悪化するため、５．０％を上限とする。
Mo: 1.0-5.0%
Mo has the effect of solidifying in the austenite phase and strengthening the solid solution to strengthen the matrix phase. For this purpose, it is necessary to contain at least 1.0% or more. More preferably, it is 3.1% or more. However, excessive addition lowers phase stability and deteriorates ductility and toughness, so the upper limit is 5.0%.
Ｃｏ：１０．０〜２０．０％
Ｃｏは、オーステナイト相を固溶強化するとともに、γ′相にも固溶してγ′相をも強化する効果がある。このためには、少なくとも１０．０％以上含有させる必要がある。より好ましくは１２．０％以上である。ただし、Ｃｏは高価な材料であるため多量に添加することはコスト的に不利となるため、２０．０％を上限とする。
Co: 10.0-20.0%
Co has the effect of solid-solving and strengthening the austenite phase and also solid-solving the γ'phase to strengthen the γ'phase. For this purpose, it is necessary to contain at least 10.0% or more. More preferably, it is 12.0% or more. However, since Co is an expensive material, adding a large amount of it is disadvantageous in terms of cost, so the upper limit is 20.0%.
Ｔａ：０．０１〜１．５０％
Ｔａは、Ｃと結合して炭化物を形成するだけでなく、γ′相に固溶してγ′相を強化する効果がある。このためには、少なくとも０．０１％以上含有させる必要がある。ただし、多量の添加は比重が重くなるため上限を１．５０％とする。より好ましい含有量は０．３〜０．８％である。
Ta: 0.01 to 1.50%
Ta not only combines with C to form carbides, but also has the effect of dissolving in the γ'phase to strengthen the γ'phase. For this purpose, it is necessary to contain at least 0.01% or more. However, since the specific gravity becomes heavy when a large amount is added, the upper limit is set to 1.50%. A more preferable content is 0.3 to 0.8%.
Ｔｉ：２．０〜４．２％
Ｔｉは、Ｎｉと結合して強度の向上に有効なγ′相（Ｎｉ3（Ａｌ，Ｔｉ）金属間化合物）を形成して合金を析出強化する。このためには、少なくとも２．０％以上含有させる必要がある。ただし、多量の添加は共晶炭化物を増加させて延性を低下させるため上限を４．２％とする。好ましくは３．０％以下である。
Ti: 2.0-4.2%
Ti combines with Ni to form a γ'phase (Ni 3 (Al, Ti) intermetallic compound) that is effective in improving strength, and precipitates and strengthens the alloy. For this purpose, it is necessary to contain at least 2.0% or more. However, since adding a large amount increases eutectic carbides and reduces ductility, the upper limit is set to 4.2%. It is preferably 3.0% or less.
Ａｌ：５．０〜８．０％
Ａｌは、γ′相（Ｎｉ3Ａｌ金属間化合物）を形成する成分であり、十分な高温強度を得るには５．０％以上含有させる必要がある。ただし過度にＡｌの添加量を増加させるとクリープ強度が低下する為、上限を８．０％とする。より好ましい含有量は６．８〜７．５％である。
Al: 5.0-8.0%
Al is a component that forms a γ'phase (Ni 3 Al intermetallic compound), and needs to be contained in an amount of 5.0% or more in order to obtain sufficient high-temperature strength. However, if the amount of Al added is excessively increased, the creep strength decreases, so the upper limit is set to 8.0%. A more preferable content is 6.8 to 7.5%.
Ｖ：０〜１．５％
Ｖは、γ′相に固溶して固溶強化する。ただし、過剰な添加は高温強度を低下させるため１．５％を上限とする。本発明においてはＶを含有しない場合もある。
V: 0-1.5%
V dissolves in the γ'phase to strengthen the solid solution. However, excessive addition reduces the high temperature strength, so the upper limit is 1.5%. In the present invention, V may not be contained.
Ｂ：０．００５〜０．０３０％
Ｂは粒界を強化するため、０．００５％以上添加する。ただし、Ｂの過剰な添加はホウ化物を形成して特性を低下させるため、上限を０．０３０％とする。
B: 0.005 to 0.030%
B is added in an amount of 0.005% or more in order to strengthen the grain boundaries. However, since excessive addition of B forms boride and deteriorates the properties, the upper limit is set to 0.030%.
Ｚｒ：０．０５〜０．１５％
ＺｒもＢと同様に粒界強化によりクリープ強度を向上させるため、０．０５％以上添加する。ただし、過剰に添加すると延性が低下するため、上限を０．１５％とする。
Zr: 0.05 to 0.15%
Similar to B, Zr is added in an amount of 0.05% or more in order to improve the creep strength by strengthening the grain boundaries. However, if it is added in excess, the ductility will decrease, so the upper limit is set to 0.15%.
Ｔｉ＋Ａｌ：１６．０〜２０．３％
Ｔｉ／Ａｌ：０．３以下
上記したところから明らかなように、Ｔｉ＋Ａｌの総量はγ′相の量を示す指標であり、高温強度特性を向上させるためには原子％で１６％以上含有させる必要がある。ただし、過剰に添加すると延性が低下するため、上限を２０．３％とする。
Ｔｉ／Ａｌ比は、γ′相の析出温度にとって重要な因子であり、本発明ではＴｉ／Ａｌ比を０．３以下とする。Ｔｉ＋Ａｌの総量が１６％以上あり、且つＴｉ／Ａｌ比が０．３を超えた場合には、γ′相の析出温度が上昇し鋳造工程における凝固過程で延性不足による割れが発生し易くなる。
Ti + Al: 16.0 to 20.3%
Ti / Al: 0.3 or less As is clear from the above, the total amount of Ti + Al is an index indicating the amount of the γ'phase, and it is necessary to contain 16% or more in atomic% in order to improve the high temperature strength characteristics. There is. However, if it is added excessively, the ductility will decrease, so the upper limit is set to 20.3%.
The Ti / Al ratio is an important factor for the precipitation temperature of the γ'phase, and in the present invention, the Ti / Al ratio is set to 0.3 or less. When the total amount of Ti + Al is 16% or more and the Ti / Al ratio exceeds 0.3, the precipitation temperature of the γ'phase rises and cracks due to insufficient ductility are likely to occur in the solidification process in the casting process.
以上のような本発明によれば、比重が小さく、高温強度特性および鋳造性に優れたＮｉ基超合金を提供することができる。 According to the present invention as described above, it is possible to provide a Ni-based superalloy having a small specific gravity and excellent high-temperature strength characteristics and castability.
次に本発明の実施例を以下に説明する。
先ず表１に示す化学成分の合金を真空溶解炉にて溶解し、５０ｋｇのインゴットに鋳造した。その後、インゴットから機械加工により試験片を作製し、試験片を用いて、比重、０．２％耐力、伸び、クリープ強度を評価した。また、表１に示す化学成分の合金を用いて、タービンホイールを作製し鋳造性を評価した。
Next, examples of the present invention will be described below.
First, the alloys of the chemical components shown in Table 1 were melted in a vacuum melting furnace and cast into a 50 kg ingot. Then, a test piece was prepared from the ingot by machining, and the specific gravity, 0.2% proof stress, elongation, and creep strength were evaluated using the test piece. In addition, a turbine wheel was produced using the alloy of the chemical components shown in Table 1 and the castability was evaluated.
［比重測定］
ＪｌＳ Ｚ ８８０７に準拠して比重測定を実施し、以下の基準に従い評価した。
Ａ：比重が７．９ｇ／ｃｍ3以下
Ｂ：比重が７．９ｇ／ｃｍ3超、８．０ｇ／ｃｍ3以下
Ｃ：比重が８．０ｇ／ｃｍ3超
[Specific gravity measurement]
Specific gravity measurements were performed according to JlS Z 8807 and evaluated according to the following criteria.
A: Specific gravity is 7.9 g / cm 3 or less B: Specific gravity is more than 7.9 g / cm 3 and 8.0 g / cm 3 or less C: Specific gravity is more than 8.0 g / cm 3
［高温引張試験］
ＪｌＳ Ｇ ０５６７に準拠し平行部径８ｍｍ、標点距離４０ｍｍの試験片を作製し、試験温度１０５０℃で引張試験を行った。この試験では１０５０℃での０．２％耐力、伸びの測定を行った。
０．２％耐力については、以下の基準に従い評価した。
Ａ：０．２％耐力が２００ＭＰａ以上
Ｂ：０．２％耐力が１５０ＭＰａ以上、２００ＭＰａ未満
Ｃ：０．２％耐力が１５０ＭＰａ未満
また伸びについては、以下の基準に従い評価した。
Ａ：伸びが１５％以上
Ｂ：伸びが１０％以上、１５％未満
Ｃ：伸びが１０％未満
[High temperature tensile test]
A test piece having a parallel portion diameter of 8 mm and a gauge point distance of 40 mm was prepared according to JlS G 0567, and a tensile test was performed at a test temperature of 1050 ° C. In this test, 0.2% proof stress and elongation at 1050 ° C were measured.
The 0.2% proof stress was evaluated according to the following criteria.
A: 0.2% proof stress is 200 MPa or more B: 0.2% proof stress is 150 MPa or more and less than 200 MPa C: 0.2% proof stress is less than 150 MPa The elongation was evaluated according to the following criteria.
A: Elongation is 15% or more B: Elongation is 10% or more and less than 15% C: Elongation is less than 10%
［クリープ破断試験］
ＪｌＳ Ｚ ２２７１に準拠した試験片を作製し、試験温度１０００℃で負荷応力１８０ＭＰａを掛け破断に到る寿命を測定し、以下の基準に従い評価した。試験片は平行部がΦ６．４ｍｍである。
Ａ：破断寿命が２５ｈ以上
Ｂ：破断寿命が１５ｈ以上、２５ｈ未満
Ｃ：破断寿命が１５ｈ未満
[Creep rupture test]
A test piece conforming to JlS Z 2271 was prepared, a load stress of 180 MPa was applied at a test temperature of 1000 ° C., the life until fracture was measured, and the test piece was evaluated according to the following criteria. The parallel part of the test piece is Φ6.4 mm.
A: Breaking life is 25h or more B: Breaking life is 15h or more and less than 25h C: Breaking life is less than 15h
［鋳造性評価］
表１に示す化学成分の合金を用いて、同一形状、同一サイズのタービンホイールをそれぞれ同一条件にて減圧鋳造し、同一の合金組成で作製された１００個のタービンホイールについて、羽先における割れ発生の有無を目視にて確認し、以下の基準に従い評価した。
Ａ：割れ発生無し
Ｂ：割れが認められたタービンホイールの発生率３０％未満
Ｃ：割れが認められたタービンホイールの発生率３０％以上
これらの結果が表２に示してある。
[Evaluation of castability]
Using the alloys of the chemical components shown in Table 1, turbine wheels of the same shape and size were cast under the same conditions under the same conditions, and cracks occurred at the tips of 100 turbine wheels manufactured with the same alloy composition. The presence or absence of the above was visually confirmed and evaluated according to the following criteria.
A: No cracking B: Turbine wheel occurrence rate with cracks less than 30% C: Turbine wheel occurrence rate with cracks 30% or more These results are shown in Table 2.
比較例１は、本発明の組成と比べて固溶強化元素であるＣｏ及びＴａが非添加である。また、γ′相生成元素であるＴｉ量が本発明の下限値より少ない一方、本発明では非添加のＮｂが添加されている。この比較例１は、十分な高温強度特性が得られず、０．２％耐力、クリープ強度の評価が「Ｃ」であった。更に、比重の評価が「Ｂ」で後述する実施例に比べ劣っている。 In Comparative Example 1, Co and Ta, which are solid solution strengthening elements, are not added as compared with the composition of the present invention. Further, while the amount of Ti, which is a γ'phase-forming element, is less than the lower limit of the present invention, Nb, which is not added, is added in the present invention. In this Comparative Example 1, sufficient high-temperature strength characteristics could not be obtained, and the evaluation of 0.2% proof stress and creep strength was "C". Further, the evaluation of specific gravity is "B", which is inferior to that of the examples described later.
比較例２は、Ｔｉ量及びＴｉ＋Ａｌの総量が本発明の下限値を下回っている一方、本発明において非添加の重元素Ｗが添加されている。このため比較例２においては、０．２％耐力、伸び、クリープ強度の評価は「Ａ」と良好であるものの、比重の評価が「Ｃ」であった。 In Comparative Example 2, the amount of Ti and the total amount of Ti + Al are below the lower limit of the present invention, while the non-added heavy element W is added in the present invention. Therefore, in Comparative Example 2, the evaluation of 0.2% proof stress, elongation, and creep strength was as good as “A”, but the evaluation of specific gravity was “C”.
比較例３は、Ｔｉ量及びＴｉ＋Ａｌの総量が本発明の下限値を下回っている一方、本発明において非添加の重元素Ｈｆ及びＷが添加されている。またＴａ量も本発明の上限値１．５％を上回っている。このため比較例３においては、０．２％耐力、伸び、クリープ強度の評価は「Ａ」と良好であるものの、比重の評価が「Ｃ」であった。 In Comparative Example 3, the amount of Ti and the total amount of Ti + Al are below the lower limit of the present invention, while the non-added heavy elements Hf and W are added in the present invention. The amount of Ta also exceeds the upper limit of 1.5% of the present invention. Therefore, in Comparative Example 3, the evaluation of 0.2% proof stress, elongation, and creep strength was as good as “A”, but the evaluation of specific gravity was “C”.
比較例４は、Ｔｉ＋Ａｌの総量が本発明の規定範囲内である一方で、Ｔｉ／Ａｌ比が本発明の上限値０．３を上回っている。このため比較例４についてはγ′相の析出温度が、他の例よりも高くなっており、鋳造性評価において凝固割れ（鋳造割れ）の発生が認められ評価が「Ｃ」であった。また、γ′相の析出温度が高いことから高温時の延性が低く熱間伸びの評価も「Ｃ」であった。 In Comparative Example 4, the total amount of Ti + Al is within the specified range of the present invention, while the Ti / Al ratio exceeds the upper limit of 0.3 of the present invention. Therefore, in Comparative Example 4, the precipitation temperature of the γ'phase was higher than in the other examples, and solidification cracks (casting cracks) were observed in the castability evaluation, and the evaluation was “C”. Further, since the precipitation temperature of the γ'phase was high, the ductility at high temperature was low and the evaluation of hot elongation was also “C”.
比較例５は、Ａｌ量及びＴｉ＋Ａｌの総量が本発明の下限値を下回っている。このため十分な高温強度特性が得られず、０．２％耐力、クリープ強度の評価は「Ｃ」であった。また、この比較例５は、Ｔｉ＋Ａｌの総量自体は少ないが、比較例４と同様にＴｉ／Ａｌ比が本発明の上限値０．３を上回っているため、鋳造割れの発生が認められ鋳造性の評価が「Ｂ」であった。 In Comparative Example 5, the total amount of Al and Ti + Al is below the lower limit of the present invention. Therefore, sufficient high-temperature strength characteristics could not be obtained, and the evaluation of 0.2% proof stress and creep strength was "C". Further, in Comparative Example 5, although the total amount of Ti + Al itself is small, the Ti / Al ratio exceeds the upper limit value of 0.3 of the present invention as in Comparative Example 4, so that casting cracks are observed and castability is observed. The evaluation of was "B".
比較例６，７は、Ｔｉ＋Ａｌの総量が比較例５に比べれば多いものの、未だ本発明の下限値１６％を下回っている。加えてＴａが非添加であるため、クリープ強度の評価は「Ｃ」であった。 In Comparative Examples 6 and 7, although the total amount of Ti + Al is larger than that in Comparative Example 5, it is still below the lower limit of 16% of the present invention. In addition, since Ta was not added, the creep strength was evaluated as "C".
比較例８は、前述の比較例６，７と異なり、Ｔａが本発明の成分範囲となるように添加されたものであるが、Ｔｉ＋Ａｌの総量が本発明の下限値１６％を下回っている。このためクリープ強度は比較例６，７より改善されるも「Ｂ」であった。この比較例８は、クリープ強度のほか、０．２％耐力、伸び、鋳造性の評価も「Ｂ」であり、後述の実施例に比べて全体としての特性が劣っている。 In Comparative Example 8, unlike Comparative Examples 6 and 7 described above, Ta was added so as to be within the component range of the present invention, but the total amount of Ti + Al was less than the lower limit of 16% of the present invention. Therefore, the creep strength was "B" although it was improved from Comparative Examples 6 and 7. In Comparative Example 8, in addition to creep strength, 0.2% proof stress, elongation, and castability were also evaluated as “B”, and the overall characteristics were inferior to those of Examples described later.
一方、各元素が本発明の成分範囲を満たす実施例１〜１４は、比重の評価が何れも「Ａ」と良好であった。また０．２％耐力、伸び、クリープ強度の評価は、全て「Ａ」又は一項目のみ「Ｂ」と良好であった。また、何れの実施例も鋳造性に問題はなく評価は「Ａ」であった。このように実施例の合金は、比重が小さく（何れも７．９ｇ／ｃｍ3以下）、１０００℃近傍の高温域で高い高温強度特性を有し、且つ鋳造性を兼ね備えている。特に各元素が、より好ましい範囲を満たす実施例１，２，５，１０，１４においては、何れの評価項目も「Ａ」となっており、バランスに優れた合金が得られている。 On the other hand, in Examples 1 to 14 in which each element satisfies the component range of the present invention, the evaluation of specific gravity was as good as "A". The evaluations of 0.2% proof stress, elongation, and creep strength were all good as "A" or only one item was "B". In addition, there was no problem in castability in any of the examples, and the evaluation was "A". As described above, the alloys of the examples have a small specific gravity (7.9 g / cm 3 or less in each case), have high high-temperature strength characteristics in a high-temperature region near 1000 ° C., and have castability. In particular, in Examples 1, 2, 5, 10, and 14 in which each element satisfies a more preferable range, all the evaluation items are "A", and an alloy having an excellent balance is obtained.
Claims (3)
Ｃ：０．１〜０．３％
Ｃｒ：８．０〜１２．０％
Ｍｏ：１．０〜５．０％
Ｃｏ：１０．０〜２０．０％
Ｔａ：０．０１〜１．５０％
Ｔｉ：２．０〜４．２％
Ａｌ：５．０〜８．０％
Ｖ：０〜１．５％
Ｂ：０．００５〜０．０３０％
Ｚｒ：０．０５〜０．１５％
を満たし、更に原子％で
Ｔｉ＋Ａｌ：１６．０〜２０．３％
Ｔｉ／Ａｌ：０．３以下
残部がＮｉ及び不可避的不純物の組成を有することを特徴とするＮｉ基超合金。 By mass% C: 0.1 to 0.3%
Cr: 8.0-12.0%
Mo: 1.0-5.0%
Co: 10.0-20.0%
Ta: 0.01 to 1.50%
Ti: 2.0-4.2%
Al: 5.0-8.0%
V: 0-1.5%
B: 0.005 to 0.030%
Zr: 0.05 to 0.15%
Ti + Al: 16.0 to 20.3% in atomic%
Ti / Al: 0.3 or less A Ni-based superalloy characterized in that the balance has a composition of Ni and unavoidable impurities.
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| US15/900,460 US10385426B2 (en) | 2017-02-24 | 2018-02-20 | Ni-based superalloy |
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