JPS5839760A - Heat resistant ni alloy - Google Patents
Heat resistant ni alloyInfo
- Publication number
- JPS5839760A JPS5839760A JP13784181A JP13784181A JPS5839760A JP S5839760 A JPS5839760 A JP S5839760A JP 13784181 A JP13784181 A JP 13784181A JP 13784181 A JP13784181 A JP 13784181A JP S5839760 A JPS5839760 A JP S5839760A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- creep rupture
- phase
- rupture strength
- amount
- 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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- Turbine Rotor Nozzle Sealing (AREA)
Abstract
Description
【発明の詳細な説明】
本発明はクリープ破断強度が優れたＮｉ基耐熱合金に関
する。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a Ni-based heat-resistant alloy with excellent creep rupture strength.
ジェットエンジンや発電設備などに用いられるＪスター
ビンの出力、熱効率を上げるには、燃焼ガス温度を上昇
させるのが最も有効である。The most effective way to increase the output and thermal efficiency of J-turbines used in jet engines and power generation equipment is to increase the combustion gas temperature.
そのためには、クリープ破断強度の大きい動翼材が必要
である。For this purpose, a moving blade material with high creep rupture strength is required.
現在、発電用大獄ガスタービンの動翼材にはｌＮ−７３
８ＬＣ（インーコ社製、組成後記）が使用されており、
またジェットエンジンの動員材にはＭａｒＭ２００ （
マーチンマリエタ社製、組成後記）が優れたものとして
使用され、またＭａｒＭ２４７（マーチンマリエタ社製
、組成後記）の実用化が検討されている。Currently, lN-73 is used as the rotor blade material for the Daigoku gas turbine for power generation.
8LC (manufactured by Inco, composition listed below) is used,
In addition, MarM200 (
MarM247 (manufactured by Martin Murrieta, composition described below) is used as an excellent one, and the practical use of MarM247 (manufactured by Martin Murrieta, composition described later) is being considered.
しかし、これらの合金はクリープ破断強度が優れないた
め、出力や熱効率を上げるのに限度がある。However, these alloys do not have excellent creep rupture strength, so there is a limit to their ability to increase output and thermal efficiency.
優れたクリープ破断強度を持つ既存合金としてはＮＡＳ
Ａ■−Ａ合金（米国ＮＡＳ人製、組成後記）がある。し
かし、この合金は高価なＲｅを使用するため、合金が高
価となる問題点がある。NAS is an existing alloy with excellent creep rupture strength.
There is an A■-A alloy (manufactured by NAS in the United States, composition listed below). However, since this alloy uses expensive Re, there is a problem that the alloy is expensive.
本発明はＮＡＳＡ■−人合金における如きＲｅを使用す
ることなく、クリープ破断強度の優れたＮｉ基耐熱合金
を提供するにある。The object of the present invention is to provide a Ni-based heat-resistant alloy with excellent creep rupture strength without using Re as in the NASA alloy.
本発明のＮｉ基耐熱合金は、Ｃ０１８−以下、Ｃｒ３〜
７％、Ｗｌｌ 〜２２１、Ａｌ ３．５〜８．５％、Ｔ
ｉ２−以下、Ｔａ０．５〜９１１、Ｃ０，００１〜０．
２−１Ｂ Ｏ，００１〜０．０５ＩＩＩ、 Ｚｒ ０．
００１〜０．２％を含み、残部は実質的にＮｉよりなり
、同時にＷ＋Ｔａ＝１４〜２５慢を満たすＮｉ基耐熱合
金である。The Ni-based heat-resistant alloy of the present invention is C018- or less, Cr3-
7%, Wll ~221, Al 3.5~8.5%, T
i2- or less, Ta0.5-911, C0,001-0.
2-1B O,001-0.05III, Zr 0.
It is a Ni-based heat-resistant alloy containing 0.001 to 0.2%, the remainder substantially consisting of Ni, and satisfying W+Ta=14 to 25.
ただし、Ｗの５−までをＭｏで置き換え、またＴｍの２
−までをＮｂで置き換えてもよく、更に前記成分に２−
以下のＨｆを含ませ【も、同様にクリープ破断強度の優
れたものが得られる。However, up to 5- of W are replaced with Mo, and 2 of Tm
- may be replaced with Nb, and furthermore, 2-
When the following Hf is included, a product with excellent creep rupture strength can be obtained as well.
本発明のＮ１基耐熱合金の組成成分の作用ならびに組成
割合の限定理由は次の通りである。The effects of the compositional components of the N1-based heat-resistant alloy of the present invention and the reason for limiting the composition ratio are as follows.
Ｃｏはγ相および化学量論的ＫＮｉｓＡｔで表わされる
ｒ′相中に固溶して、これらの相の固溶化に寄与すると
共に、γ相中におけるｒ′相の析出量を増加して析出強
化を助長する作用をする。その量が１８％を超えると、
Ｃ相などの有害析出物が現われてクリープ破断強度が低
下する欠点を生ずる。その好ましい量は５〜１５−であ
る。Co dissolves in the γ phase and the r' phase represented by stoichiometric KNisAt, contributes to the solid solution of these phases, and increases the amount of r' phase precipitated in the γ phase, resulting in precipitation strengthening. acts to promote If the amount exceeds 18%,
Harmful precipitates such as C phase appear, resulting in a decrease in creep rupture strength. Its preferred amount is 5-15.
Ｃｒは合金の耐硫化腐食性を良好にする作用をするもの
であり、その量が７％を超えるとＣ相やβ相などの有害
相が板上に生成して、クリープ破断強度が低下する欠点
を生ずる。３ｇ４より少なくなると、前記作用が得られ
なくなる。Cr has the effect of improving the sulfide corrosion resistance of the alloy, and if its amount exceeds 7%, harmful phases such as C phase and β phase will form on the plate, reducing creep rupture strength. produce defects. When the amount is less than 3g4, the above effect cannot be obtained.
ただし、８００〜９００℃の比較的低温度で５０００時
間以上の長時間使用すると前記有害相の生成傾向が強ま
るので、３チ〜６チと低くするのが好ましい。However, if it is used for a long time of 5,000 hours or more at a relatively low temperature of 800 to 900°C, the tendency to generate the harmful phase increases, so it is preferable to set the temperature as low as 3 to 6 degrees.
Ｗはγ相およびｒ′相中に固溶し【、これらの相を著し
く強化する。そのためには１１％以上含有させる必要が
あるが、２２％を超えると、β相などの有害析出物を生
成し、クリープ破断寿命が低下する欠点を生ずる。W forms a solid solution in the γ and r' phases and significantly strengthens these phases. For this purpose, it is necessary to contain 11% or more, but if it exceeds 22%, harmful precipitates such as β phase are formed, resulting in a shortened creep rupture life.
この場合、Ｗの一部をＭｏで置きかえてもよい。Ｍｏは
Ｗと同様にγ相およびｒ′相に固溶してこれらの相を強
化する。しかし、５％を超えるとμ相などの有害析出物
を生じ、クリープ破断寿命が低下する欠点を生ずる。In this case, part of W may be replaced with Mo. Like W, Mo forms a solid solution in the γ phase and r' phase to strengthen these phases. However, if it exceeds 5%, harmful precipitates such as μ phase are produced, resulting in a shortcoming of reduced creep rupture life.
ＡＩはγ′相を生成するために必要な元素であり、ｒ′
相を十分に析出させるためＫは、３．５１１１ｉ以上含
有させることが必要である。しかし、６．５ｍを超える
と共晶ｒ′と呼ばれる粗大なｒ′相の量が過多となり、
クリープ破断強度が低下する欠点を生ずる。AI is an element necessary to generate the γ′ phase, and r′
In order to sufficiently precipitate the phase, K must be contained in an amount of 3.5111i or more. However, if the length exceeds 6.5 m, the amount of coarse r' phase called eutectic r' becomes excessive.
This results in the disadvantage that creep rupture strength decreases.
ＴＪはその大部分がｒ′相に固溶し、ｒ′相を強化する
と共に、ｒ’相の量を増加させて析出強化に寄与する。Most of TJ dissolves in the r' phase, strengthens the r' phase, increases the amount of the r' phase, and contributes to precipitation strengthening.
しかし、２−を超えると！相を生じてクリープ破断強度
を低下させる欠点を生ずる。However, if it exceeds 2-! This has the disadvantage of forming phases and lowering the creep rupture strength.
Ｔａはその大部分がｒ′相に固溶して著しく固溶強化す
ると共に、ｒ′相の量を増加させ又祈出強化に寄与する
。その効果を得るためには０．５−以上必要である。し
かし、９−を超えるとＣ相などの有害析出物が生じてク
リープ破断寿命が低下する。Most of Ta dissolves in the r' phase and significantly strengthens it as a solid solution, increases the amount of the r' phase, and contributes to the strength strengthening. In order to obtain this effect, 0.5- or more is required. However, when it exceeds 9-, harmful precipitates such as C phase are generated, resulting in a decrease in creep rupture life.
この場合、Ｔａの一部なＮｂで置きかえてもよい。Ｎｂ
はＴＪＩと同様な作用をする。しかし、Ｎｂの含有量が
２−を超えるとＣ相などの有害析出物を生じ、クリープ
破断寿命を低下する。In this case, part of Ta may be replaced with Nb. Nb
has a similar effect to TJI. However, if the Nb content exceeds 2-, harmful precipitates such as C phase are generated, which reduces the creep rupture life.
Ｃは、よく知られているようにＭＣ型、ＭｔｓＣ６屋、
ＭｓＣ型の３種類の炭化物を作りて、主として合金の結
晶の粒界を強化する。その効果を得るにはＣが０．００
１−以上必要である。しかし、０．２−を超えると粗大
な炭化物を多量に晶出し、かえってクリープ破断強度を
低下させる。好ましい範囲は０．０５〜０．２である。As is well known, C is MC type, MtsC6 type,
Three types of MsC type carbides are created to mainly strengthen the grain boundaries of the alloy crystals. To get that effect, C is 0.00
1- or more is required. However, if it exceeds 0.2-, a large amount of coarse carbides will crystallize, which will actually lower the creep rupture strength. The preferred range is 0.05-0.2.
Ｂは粒界に偏析して高温での粒界強度を向上させ、クリ
ープ破断強度と破断のびな増加させる作用をする。この
効果を得るためＫは０．００１−以上必要である。しか
し、０．０５％を超えると粒界に低融点の共晶を生成し
、合金の溶融損傷を起こし易くなる欠点を生ずる。B segregates at grain boundaries, improves grain boundary strength at high temperatures, and functions to increase creep rupture strength and fracture elongation. In order to obtain this effect, K needs to be 0.001- or more. However, if it exceeds 0.05%, a low melting point eutectic is produced at the grain boundaries, resulting in the disadvantage that the alloy is more likely to be damaged by melting.
Ｚｒ ４． Ｂ同様粒界強化の作用をする。この効果を
得るには０．００１−以上必要である。しかし、０．２
−を超えると粒界に金属間化合物が生じ、かえってクリ
ープ破断強度を低下させる欠点を生ずる。Zr4. Like B, it acts to strengthen grain boundaries. To obtain this effect, a ratio of 0.001- or more is required. However, 0.2
If it exceeds -, intermetallic compounds will be formed at the grain boundaries, resulting in a disadvantage of lowering the creep rupture strength.
前記のような組成のものからなるものに、更にＨｆを２
１以下含有させてもよい。Furthermore, 2 Hf was added to the composition as described above.
You may contain 1 or less.
Ｈｆは粒界強化の作用をする。しかし、２−を超えると
有害な金属間化合物が生成し、クリープ破断寿命が低下
するので２−以下であることが必要である。Hf acts to strengthen grain boundaries. However, if it exceeds 2-, harmful intermetallic compounds will be generated and the creep rupture life will be reduced, so it is necessary that it is 2- or less.
以上、各元素の組成割合について説明したが、クリープ
破断強度の大きい最適組成には複−数の元素に関連した
条件が必要である。The composition ratios of each element have been explained above, but conditions related to a plurality of elements are required for an optimal composition with a high creep rupture strength.
即ち、ｒ相またはｒ′相の固溶強化に有効な元素である
ＷとＴａの合計量が１４−〜２５９Ｇであることが必要
である。Ｗ＋Ｔａが１４−未満であると、固溶強化量が
不足し、十分なりリープ破断強度が得られない。逆にそ
の合計量が２５−を超えるとＣ相、μ相などの有害析出
物が生成し、クリープ破断強度が低下する欠点を生ずる
。That is, it is necessary that the total amount of W and Ta, which are elements effective for solid solution strengthening of the r phase or r' phase, is 14-259G. When W+Ta is less than 14-, the amount of solid solution strengthening is insufficient and sufficient leap rupture strength cannot be obtained. On the other hand, if the total amount exceeds 25 -, harmful precipitates such as C phase and μ phase are formed, resulting in a disadvantage that the creep rupture strength is reduced.
Ｗ、Ｔａの１部をＮｂ、Ｍｏのどちらか一方あるいは両
者置きかえた場合においても、それらの全体の合計量が
同じ理由で１．４１〜２５秦の範囲である必要がある。Even when a part of W and Ta is replaced with one or both of Nb and Mo, the total amount of them needs to be in the range of 1.41 to 25 squares for the same reason.
以下、実施例を挙げると共に従来のＮＪ基耐熱合金との
比較を示す。Examples will be given below, as well as a comparison with conventional NJ-based heat-resistant alloys.
実施例
本発明合金９種と既存合金４種を溶解鋳造し、クリープ
破断試験を行りた。溶解は高周波真空溶解炉で行い、８
００’ＣＫ保温した６ｍｍ−クリープ破断試験片１２本
とりのロストワックス歴に鋳込んだ。試験片は鋳造のま
まクリープ破断試験に供した。しかし、粉末冶金法によ
っても製造し得られる。EXAMPLE Nine types of alloys of the present invention and four types of existing alloys were melted and cast, and creep rupture tests were conducted. Melting is carried out in a high frequency vacuum melting furnace.
12 pieces of 6 mm creep rupture test specimens kept at 00'CK temperature were cast into lost wax history. The test piece was subjected to a creep rupture test as cast. However, it can also be produced by powder metallurgy.
クリープ破断試験はＪＩＳＺ−２２７２に基づいて行っ
た。The creep rupture test was conducted based on JISZ-2272.
その試験結果は次の表に示す通りでありた。The test results were as shown in the following table.
表中の破断寿命のうち、ψ印はラーソンミラーパラメー
タ（定数＝２０）を用いた推定値である。Among the fracture lives in the table, the ψ symbol is an estimated value using the Larson-Miller parameter (constant=20).
前記衣の結果が示すように、本発明合金のクリープ破断
寿命は、ｌＮ−７３８ＬＣ，Ｍｓ＋ｒＭ２００゜Ｍａｒ
Ｍ２４７の現在最強合金とされている合金よりも大きい
ことが分かる。この原因は主として固溶強化量（Ｗ＋Ｍ
ｏ＋Ｔａ＋Ｎｂ）Ｋよっ”Ｃ説明することができる。（
ここにＭｏとＮｂは１−当りＷ、Ｔａと同等の固溶強化
の効果をもつので、Ｗ十Ｍｏ＋Ｔａ＋Ｎｂを固溶強化量
とみ【よい。）ＩＮ−７３８ＬＣは固溶強化量が本発明
合金に比べ大巾に少なく、またＷ量も少なり、Ｃｒが多
い。As shown in the above results, the creep rupture life of the alloy of the present invention is lN-738LC, Ms+rM200°Mar.
It can be seen that it is larger than M247, which is currently considered the strongest alloy. This is mainly due to the amount of solid solution strengthening (W+M
o+Ta+Nb)K can be explained.(
Here, Mo and Nb have the same solid solution strengthening effect as W and Ta per 1 -, so W0Mo+Ta+Nb can be regarded as the amount of solid solution strengthening. ) IN-738LC has a much smaller amount of solid solution strengthening than the alloy of the present invention, and also has a smaller amount of W and a larger amount of Cr.
Ｍａｒ Ｍ２００合金とＭａｒＭ２４７合金も本発明合
金に比べてＷ＋Ｍｏ＋Ｔａ＋Ｎｂ量が少な（、Ｃｒ量が
多い。そのため、以上の３種合金は本発明合金に比べて
クリープ破断強度が小さいと考えられる。The Mar M200 alloy and the Mar M247 alloy also have a smaller amount of W + Mo + Ta + Nb (and a larger amount of Cr) than the alloy of the present invention. Therefore, it is thought that the above three alloys have lower creep rupture strength than the alloy of the present invention.
ＮＡ８ＡＶｌ−人合金は本発明合金と同等穐度のクリー
プ破断寿命を示している。この合金はＴａによるｒ′相
の固溶強化とＲｅの添加による粒界強化とを利用したも
のである。一方、本発明合金は高価なＲｅを使用せず、
またＴａの使用量も少ないものであり、主として安価な
Ｗの固溶強化を利用したものである。従って、本発明合
金はＮＡＳＡｖｉ−人合金に比べて極めて安価に製造し
得られる。しかも、工場での製造の生臘管理において、
例えばスクラップの他合金への転用等においても本発明
合金の方が有利である等の優れた効果を有する。The NA8AVl-man alloy exhibits a creep rupture life of comparable toughness to the invention alloy. This alloy utilizes solid solution strengthening of the r' phase by Ta and grain boundary strengthening by adding Re. On the other hand, the alloy of the present invention does not use expensive Re,
Further, the amount of Ta used is small, and solid solution strengthening of inexpensive W is mainly utilized. Therefore, the alloy of the present invention can be manufactured at a much lower cost than the NASA alloy. Moreover, in the management of raw carrots during manufacturing at the factory,
For example, the alloy of the present invention has excellent effects, such as being more advantageous when converting scrap to other alloys.
本発明合金は、これを動翼材として用いることによって
、ジェットエンジンや発電設備などの各種ガスタービン
の高効率化が可能となる。By using the alloy of the present invention as a moving blade material, it is possible to improve the efficiency of various gas turbines such as jet engines and power generation equipment.
また、この合金は耐酸化あるいは耐硫化コーティングを
行って使用することも可能である。This alloy can also be used with an oxidation-resistant or sulfur-resistant coating.
更に一方向凝固材あるいは単結晶材とし【の使用も可能
であり、これによって高温での強度と延性の向上が得ら
れる。このほか粒子分散強化合金の基地としての使用も
可能である。Furthermore, it is also possible to use it as a directionally solidified material or a single crystal material, which improves strength and ductility at high temperatures. In addition, it can also be used as a base for particle dispersion strengthened alloys.
Claims (1)
Ａｌ１．５〜６．５９１１Ｔｉ２−以下、Ｔ１０．５〜
９−（ただし、２チ以下なＮｂで代えることができる。 ）、ＣＯ，００１〜０．２Ｉｓ、Ｂ Ｏ，００１〜０．
０５９ｇ、ＺｒＯ，００１〜０．２−を含み、残部は実
質的ＫＮ轟よりなり、同時に Ｗ＋Ｔａ＝＝１４〜２５１ｇ （ただし、５−以下をＭｏで代えることができる。）、
Ａｌ１．５〜６．５％、Ｔｉ２１以下、Ｔａ０．５〜９
１Ｇ（ただし、２％以下なＮｂで代えることができる。 ）、Ｃ０，００１〜０．２−１Ｂ Ｏ，００１〜０．０
５１．ＺｒＯ，００１〜０．２＊、Ｈｆ２−以下を含み
、残部は実質的ＫＮｉよりなり、同時に Ｗ＋Ｔａ＝１４〜２５ｍ を満たすＮｉ基耐熱合金。[Claims] (However, 5- or less can be replaced with No.),
Al1.5~6.5911Ti2- or less, T10.5~
9- (However, it can be replaced with 2 or less Nb.), CO,001~0.2Is, BO,001~0.
059 g, ZrO, 001 to 0.2-, the remainder substantially consists of KN metal, and at the same time W + Ta = 14 to 251 g (however, 5- or less can be replaced with Mo),
Al1.5-6.5%, Ti21 or less, Ta0.5-9
1G (however, it can be replaced with 2% or less Nb), C0,001~0.2-1B O,001~0.0
51. A Ni-based heat-resistant alloy containing ZrO,001~0.2*, Hf2- or less, the remainder being substantially KNi, and satisfying W+Ta=14~25m.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13784181A JPS5839760A (en) | 1981-09-03 | 1981-09-03 | Heat resistant ni alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13784181A JPS5839760A (en) | 1981-09-03 | 1981-09-03 | Heat resistant ni alloy |
Related Child Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP15519885A Division JPS6152339A (en) | 1985-07-16 | 1985-07-16 | Heat resistant ni alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS5839760A true JPS5839760A (en) | 1983-03-08 |
Family
ID=15208065
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP13784181A Pending JPS5839760A (en) | 1981-09-03 | 1981-09-03 | Heat resistant ni alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS5839760A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60159143A (en) * | 1983-12-29 | 1985-08-20 | アソシアシオン・プール・ラ・ルシエルシユ・エ・ル・デヴロプマン・デ・メトド・エ・プロセシユ・アンデユストリエル（ア．エール．エム．イ．エヌ．ウ．エス．） | Single crystal metal using nickel-base mother material |
| JPS6148550A (en) * | 1984-08-14 | 1986-03-10 | Natl Res Inst For Metals | Gamma-phase precipitation-strengthened nickel base heat-resistant alloy containing dispersed yttria particles |
| JPS63213632A (en) * | 1987-03-02 | 1988-09-06 | Natl Res Inst For Metals | Super plasticity heat resisting ni based alloy for forging and its production |
| JP2016056448A (en) * | 2014-09-05 | 2016-04-21 | ゼネラル・エレクトリック・カンパニイ | Nickel-base superalloy article, and method for forming the article |
| US9359658B2 (en) | 2009-07-29 | 2016-06-07 | Nuovo Pignone S.P.A | Nickel-based superalloy, mechanical component made of the above mentioned super alloy, piece of turbomachinery which includes the above mentioned component and related methods |
-
1981
- 1981-09-03 JP JP13784181A patent/JPS5839760A/en active Pending
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60159143A (en) * | 1983-12-29 | 1985-08-20 | アソシアシオン・プール・ラ・ルシエルシユ・エ・ル・デヴロプマン・デ・メトド・エ・プロセシユ・アンデユストリエル（ア．エール．エム．イ．エヌ．ウ．エス．） | Single crystal metal using nickel-base mother material |
| JPH0561337B2 (en) * | 1983-12-29 | 1993-09-06 | Ass Ra Rusherushu E Ru Dev De | |
| JPS6148550A (en) * | 1984-08-14 | 1986-03-10 | Natl Res Inst For Metals | Gamma-phase precipitation-strengthened nickel base heat-resistant alloy containing dispersed yttria particles |
| JPH0352525B2 (en) * | 1984-08-14 | 1991-08-12 | Kagaku Gijutsucho Kinzoku Zairyo Gijutsu Kenkyu Shocho | |
| JPS63213632A (en) * | 1987-03-02 | 1988-09-06 | Natl Res Inst For Metals | Super plasticity heat resisting ni based alloy for forging and its production |
| JPH0338330B2 (en) * | 1987-03-02 | 1991-06-10 | Kagaku Gijutsucho Kinzoku Zairyo Gijutsu Kenkyu Shocho | |
| US9359658B2 (en) | 2009-07-29 | 2016-06-07 | Nuovo Pignone S.P.A | Nickel-based superalloy, mechanical component made of the above mentioned super alloy, piece of turbomachinery which includes the above mentioned component and related methods |
| JP2016056448A (en) * | 2014-09-05 | 2016-04-21 | ゼネラル・エレクトリック・カンパニイ | Nickel-base superalloy article, and method for forming the article |
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