JPS6173852A - Ni base alloy for super plasticity forging and its manufacture - Google Patents
Ni base alloy for super plasticity forging and its manufactureInfo
- Publication number
- JPS6173852A JPS6173852A JP19397884A JP19397884A JPS6173852A JP S6173852 A JPS6173852 A JP S6173852A JP 19397884 A JP19397884 A JP 19397884A JP 19397884 A JP19397884 A JP 19397884A JP S6173852 A JPS6173852 A JP S6173852A
- Authority
- JP
- Japan
- Prior art keywords
- less
- alloy
- gamma prime
- base alloy
- superplastic
- 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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Links
Abstract
Description
【発明の詳細な説明】
産業上の利用分野
本発明は超塑性鍛造用Ｎｉ基合金及びその製造法に関す
るものである。DETAILED DESCRIPTION OF THE INVENTION Field of Industrial Application The present invention relates to a Ni-based alloy for superplastic forging and a method for producing the same.
Ｎｉ基超超合金用いてガスタービンディスクなどの大型
で複雑な形状の製品を成形する方法として超塑性鍛造法
が知られている。これは金属材料があたかも粘土のよう
に小さい力で数百−以上も塑性変形する現象すなわち超
塑性現象を利用するものである。Superplastic forging is known as a method for forming large, complex-shaped products such as gas turbine disks using Ni-based superalloys. This utilizes the phenomenon of superplasticity, in which a metal material undergoes plastic deformation of hundreds of degrees or more with a small force, just like clay.
従来技術
従来の超塑性鍛造用Ｎｉ基合金としては、例えばＲｅｎ
ｅ９５（Ｇ、ｇ社製）のＮｉ基合金が知られている。し
かし、この合金は実施例において比較合金として示すよ
うに、結晶粒径も大きく、特に超塑性鍛造時の変形抵抗
が大きすぎる問題点があったっ変形抵抗が大きすぎると
大型製品や複雑形状製品の成形が困難となり、たとえ成
形が可能であったとしても、そのためには大型のプレス
が必要となり、生産性の点で好オしくないっ
この超塑性変形抵抗を小さくするには、押出加工によっ
て結晶粒を微細化することが効果的であることは知られ
ているが、前記既存のＮｉ基合金では、結晶粒を小さく
するのも限度があった。Prior Art Conventional Ni-based alloys for superplastic forging include, for example, Ren.
Ni-based alloy e95 (G, manufactured by G Company) is known. However, as shown as a comparative alloy in the examples, this alloy has a large grain size and has the problem that the deformation resistance is too large, especially during superplastic forging. This makes molding difficult, and even if molding is possible, a large press is required.In order to reduce this superplastic deformation resistance, which is unfavorable in terms of productivity, extrusion is used to Although it is known that making grains finer is effective, in the existing Ni-based alloys, there is a limit to how small crystal grains can be made.
発明の目的
本発明は既存の超塑性鍛造用Ｎｉ基合金の問題点を解消
すべくなされたもので、その目的は結晶粒の微細化が容
易で、かつ超塑性変形抵抗の小さいＮｉ基合金を提供す
るにある。Purpose of the Invention The present invention was made to solve the problems of existing Ni-based alloys for superplastic forging, and its purpose is to create a Ni-based alloy that has easy crystal grain refinement and low superplastic deformation resistance. It is on offer.
発明の構成
本発明者は前記目的を達成するために、結晶粒を微細化
するのに最適なＮｉ基合金を見出すべく検討を行った。DESCRIPTION OF THE INVENTION In order to achieve the above object, the present inventor conducted studies to find a Ni-based alloy that is optimal for refining crystal grains.
Ｎｉ基合金中のガンマプライム相の量とこれが押出し加
工時の結晶粒微細化との関係について調べた。The relationship between the amount of gamma prime phase in the Ni-based alloy and grain refinement during extrusion processing was investigated.
ここで言うガンマプライム相とは、Ｎｉ元素３に対して
Ａｔ元素１の比の金属間化合物Ｎｉ 、Ａｔを基本組成
とするものである。このＮ ｉ ＊ Ａｔはｃｏ、 Ｏ
ｒ、 Ｍｏ、 Ｗ、 ＴｉＸＮｂ、 Ｔａ、 Ｈｆ、
その他多くの元素を固溶し得る。この場合、例えばＣ
Ｏは主ＫＮｉＫ置換し、Ｏｒは約半分のＮ１３残部がＡ
ｔと置換し、またＴｉ、 Ｎｂ、 Ｔａ、 Ｈｆ、 Ｍ
ｏ、 Ｗは主にｋｌと置換する。 このような、Ｎｔ３
Ａｔ及びこれに他の元素が固溶したもの全体をガンマプ
ライム相と総称する。The gamma prime phase mentioned here has a basic composition of intermetallic compounds Ni and At with a ratio of 3 parts Ni to 1 part At. This N i * At is co, O
r, Mo, W, TiXNb, Ta, Hf,
Many other elements can be dissolved in solid solution. In this case, for example, C
O is mainly KNiK substituted, and about half of the N13 remainder in Or is A.
t, and also Ti, Nb, Ta, Hf, M
o and W are mainly replaced with kl. Such, Nt3
The entire solid solution of At and other elements is collectively referred to as the gamma prime phase.
先ず、押出加工温度の平衡状態において含有するガンマ
プライム相の景が種々異なるＮｉ基合金粉末を作った。First, Ni-based alloy powders containing various types of gamma prime phase in an equilibrium state of extrusion temperature were prepared.
これらの合金粉をそれぞれ予備焼結した後、押出加工し
て再結晶を起させ微細化したところ、ガンマプライム体
積の多い合金はど再結晶粒がより微細となり、また再結
晶粒の微細な程超塑性変形抵抗が小さいことを確認した
。After pre-sintering each of these alloy powders, they were extruded to cause recrystallization and refinement. The alloys with a large gamma prime volume had finer recrystallized grains, and the finer the recrystallized grains. It was confirmed that the superplastic deformation resistance was small.
この知見に基いて本発明を完成した。The present invention was completed based on this knowledge.
本発明の超塑性鍛造用Ｎｉ基合金は、１１００℃の温度
での熱力学的平衡状態において、７０体積チ以上のガン
マプライム相を含有したものからなるＮｉ基合金である
。 ガンマプライム相の養
量が７０体積より少ないと、押出加工により結チで、Ａ
Ａ２８チ以下、’ｒｉ１６．５係以下、Ｎｂ８チ以下、
ＭＯ６％以下、Ｗ６％以下、Ｃｒ１４％以下、Ｃ１％以
下、８０．２％以下、ＺｒＱ、１％以下を含有し、Ａｔ
＋Ｔｉ ＋Ｎｂ＋Ｍｏ＋Ｗ＝ １９〜２８％、買的にＮ
ｉあるいＶよその２０チまでをＣＯで置換［７た組成で
ある。The Ni-based alloy for superplastic forging of the present invention is a Ni-based alloy containing a gamma prime phase with a volume of 70 or more in a thermodynamic equilibrium state at a temperature of 1100°C. If the amount of nutrients in the gamma prime phase is less than 70 volumes, the extrusion process will result in caking and A
A28 or less, 'ri 16.5 or less, Nb 8 or less,
Contains MO 6% or less, W 6% or less, Cr 14% or less, C 1% or less, 80.2% or less, ZrQ, 1% or less, At
+Ti +Nb+Mo+W= 19~28%, N
It has a composition in which up to 20 parts of i or V are replaced with CO.
Ａｔけガンマプライム相を生成するために必須の元素で
ある。しかし、その贋が２８チ（原子チ以下同じ）を超
えると、ガンマプライム相が不安定になってベータ相が
生成し、押出加工時に粗大な割れを生ずる原因となる。It is an essential element for producing At and gamma prime phases. However, if the number of counterfeits exceeds 28 atoms (the same applies below atoms), the gamma prime phase becomes unstable and a beta phase is generated, which causes coarse cracks to occur during extrusion processing.
そのため２８チ以下であることが必要である。Therefore, it needs to be 28 inches or less.
ＴｉＸＮｂ、 Ｍｏ、Ｗの元素はガンマプライム相中で
、Ａｔと置換し、Ａｔと同様にガンマプライム相の量を
増加させる作用をし、押出加工時の結晶粒微細化を促進
する作用をする。しかし、いずれの元素も過剰に加える
とガンマプライム相を不安定にし、有害相が生成する。The elements TiXNb, Mo, and W replace At in the gamma prime phase, and like At, they act to increase the amount of the gamma prime phase and promote grain refinement during extrusion processing. However, adding either element in excess destabilizes the gamma prime phase and generates a harmful phase.
すなわちＴｉ含有骨が１６，５チを超えるとＮｉ３Ｔｉ
型化合物が生成し、Ｎｂ含有倚が８％を超えるとＮｉ、
Ｎｂ型化合物が生成し７、ＭＯ含有酔が６チを超えると
アルファＭＯ相が生成し、Ｗ含有帯が６チを超えるとア
ルファＷ相が生成し、Ｏｒ含有量が１４％４Ｍえるとシ
グマ相が生成し、いずれの場合も押出加工の時に粗大な
割れが生成し易くなる欠点が生ずる。In other words, if the Ti-containing bone exceeds 16.5 Ti, Ni3Ti
type compounds are formed, and when the Nb content exceeds 8%, Ni,
When the Nb-type compound is generated 7, when the MO content band exceeds 6 mm, the alpha MO phase is generated, when the W content band exceeds 6 mm, the alpha W phase is generated, and when the Or content increases to 14%4M, the sigma Phases are formed, and in either case, there is a disadvantage that coarse cracks are likely to form during extrusion processing.
Ａｔ＋Ｔｉ ＋Ｎｂ＋Ｍｏ＋Ｗの値が１９係未満である
と１１００℃に２時間以上加熱して得られる熱力学的平
衡状態において含有するガンマプライム相の骨が７０体
積％以上とならない。そのため押出加工による再結晶微
細粒化が不十分となる。一方その値が２８係を超えると
ベータ相が生成し、押出加工時に粗大な割れが生成し易
くなる。従って、入ｔ＋ Ｔｉ ＋Ｎｂ ＋Ｍｏ ＋Ｗ
＝ １９〜２８チであることが必要である。If the value of At+Ti+Nb+Mo+W is less than 19, the gamma prime phase bone content will not exceed 70% by volume in the thermodynamic equilibrium state obtained by heating to 1100° C. for 2 hours or more. Therefore, recrystallization into fine grains by extrusion becomes insufficient. On the other hand, if the value exceeds a factor of 28, a beta phase is generated, and coarse cracks are likely to occur during extrusion processing. Therefore, input t+ Ti +Nb +Mo +W
= It is necessary to be 19 to 28 inches.
］二十乏立＋ｙ工十異≦１．２であることが必要１６．
５ ８ ６ ６
である。この値が１．２を超えるとシグマ相などの有害
相が生成し７、押出加工時に粗大な割れを生ずる原因と
なる。なお、Ｎｉの一部をＣＯで置換することができる
。その置換量が２０％を超えるとシグマ相などの有害相
が生成し、押出加工時に粗大な割れを生ずる原因となる
。従って００での置換骨の限度は２０チ以下であること
が必要である。これらの原料粉末から超塑性鍛造用合金
を製造するには、これらの粉末を容器に入れ、−８００
〜２０００気圧下で１０２５〜１２５０℃で３０〜２０
０分高温高圧処理（以下ＨＩＰＩＰ処理う）する。] It is necessary that 20% + y% = 1.2 16.
5 8 6 6. If this value exceeds 1.2, harmful phases such as sigma phase will be generated7, which will cause large cracks to occur during extrusion processing. Note that a part of Ni can be replaced with CO. When the amount of substitution exceeds 20%, harmful phases such as sigma phase are generated, which causes coarse cracks to occur during extrusion processing. Therefore, the limit of replacement bone in 00 must be 20 inches or less. To produce a superplastic forging alloy from these raw powders, place these powders in a container and heat them to -800
30-20 at 1025-1250℃ under ~2000 atmospheres
High temperature and high pressure treatment (hereinafter referred to as HIPIP treatment) is performed for 0 minutes.
このＩ（ＩＰ処理は超塑性変形抵抗の低下には直接結び
つかないが、粉末が焼結するため、その後の押出加工の
操作が容易となる利点がある。This I (IP treatment) does not directly lead to a reduction in superplastic deformation resistance, but since the powder is sintered, it has the advantage of facilitating subsequent extrusion processing operations.
例えば押出用容器に挿入する際減圧処理や封入処理が必
要としなくなり、作業性が向上する。For example, when inserting into an extrusion container, there is no need for depressurization treatment or encapsulation treatment, which improves work efficiency.
Ｆ（ＩＰ処理の条件は、温度１０２５〜１２５０℃、圧
力８００〜２０００気圧、処理時間は３０〜２００分で
あることが好ましい。F(IP treatment conditions are preferably a temperature of 1025 to 1250°C, a pressure of 800 to 2000 atm, and a treatment time of 30 to 200 minutes.
処理温度が１０２５℃より低いと粉末が十分焼結しなく
、１２５０℃を超えると合金が一部溶融して有害組織を
生成し、押出加工の際割れを生ずる原因となる。処理圧
力が８００気圧未満では粉末が十分焼結固化しなく、２
０００気圧を超えるとそれに相当する高圧装置を必Ｗ”
Ｌ、実質的するう押出加工条件は押出温度１０５０〜１
２２５℃、押出比４〜１５であることが最も好ましい。If the processing temperature is lower than 1025° C., the powder will not be sufficiently sintered, and if it exceeds 1250° C., the alloy will partially melt and form a harmful structure, which may cause cracking during extrusion processing. If the processing pressure is less than 800 atm, the powder will not be sufficiently sintered and solidified, and 2
If the pressure exceeds 1,000 atmospheres, a corresponding high-pressure device is required.
L, the actual extrusion processing conditions are extrusion temperature 1050-1
Most preferred is 225°C and an extrusion ratio of 4 to 15.
押出温度が１０５０℃未満では押出しによって割れが生
じ、実用的なものが得られなく、その温度が１２２５℃
を超えると結晶粒の微細化が不十分となり、超塑性変形
抵抗が小さくならない。If the extrusion temperature is less than 1050°C, cracks will occur during extrusion, making it impossible to obtain a practical product;
If it exceeds, grain refinement becomes insufficient and superplastic deformation resistance does not become small.
押出比が４より小さいと結晶粒の微細化が不十分で、超
塑性変形抵抗が小さくならなく、その値が１５を紹える
と押出しができなくなる。If the extrusion ratio is less than 4, the crystal grains will not be refined enough and the superplastic deformation resistance will not become small, and if the value exceeds 15, extrusion will no longer be possible.
実施例
表１に示す組成の本発明のＮｉ基合金及びガンマプライ
ム量の少ない既存合金の几ｅｎｅ９５合金他２合金で試
験片を作った。EXAMPLE Test specimens were made using the Ni-based alloy of the present invention having the composition shown in Table 1, the existing alloy ENE95 alloy with a small amount of gamma prime, and two other alloys.
た。Ta.
試験片の大きさは、平行部長さ２０ｖｍ、平行部室径３
．５籠とした。The size of the test piece is: parallel part length 20vm, parallel part chamber diameter 3
．． There were 5 baskets.
これらの試験片を１０５０℃で初期歪速度ｌＸ１０−’
／秒の変形速度で引張超塑性変形させたつその結果は表
ＩＫ示す通りであった。These test pieces were heated at 1050°C with an initial strain rate of lX10-'
The results of tensile superplastic deformation at a deformation rate of /sec are shown in Table IK.
１１００℃の熱力学的平衡状態におけるガンマプライム
量と再結晶粒径の関係は第１図の通りである。また、再
結晶粒径と超塑性変形抵抗の関係は第２図の通りである
。The relationship between the amount of gamma prime and the recrystallized grain size in a thermodynamic equilibrium state of 1100° C. is shown in FIG. Furthermore, the relationship between recrystallized grain size and superplastic deformation resistance is shown in FIG.
この結果から明らかなように、Ａｔ＋Ｔｉ＋Ｎｂ＋Ｍｏ
＋Ｗが１９〜２８０間である本発明合金が７０体積−以
上のガンマプライムへ含有し、これは既存押出加工によ
る再結晶粒径が小さくなっており、超塑性変形抵抗が大
幅に低下している。As is clear from this result, At+Ti+Nb+Mo
The alloy of the present invention with +W between 19 and 280 is contained in gamma prime of 70 volume or more, which means that the recrystallized grain size due to existing extrusion processing has become smaller, and the superplastic deformation resistance has been significantly reduced. .
発明の効果
本発明のＮｉ基合金は押出加工により、結晶粒径を極め
て微細なものとなし得、また超塑性変形抵抗が小さく、
大型製品や複雑な形状品も容易に鍛造し得られる優れた
効果を有し、また、この合金も極めて容易に製造し得ら
れる効果も有する。Effects of the Invention The Ni-based alloy of the present invention can be made to have an extremely fine crystal grain size by extrusion processing, and has low superplastic deformation resistance.
It has an excellent effect in that large products and products with complicated shapes can be easily forged, and this alloy also has the advantage that it can be produced extremely easily.
第１図は１１００℃の熱力学的平衡状態におけるガンマ
プライム険と再結晶粒径の関係図、第２図は再結晶粒径
と超塑性変形抵抗の関係図で ・あるう
特許出願人 科学技術庁金属材料技術研究所長中 川
龍 −Figure 1 is a relationship diagram between gamma prime steepness and recrystallized grain size in a thermodynamic equilibrium state of 1100°C, and Figure 2 is a relationship diagram between recrystallized grain size and superplastic deformation resistance. Ryu Kawa, Director of the Metals and Materials Technology Research Institute -
Claims (3)
、７０体積％以上のガンマプライム相を含有したものか
らなる超塑性鍛造用Ｎｉ基合金。(1) A superplastic Ni-based alloy for forging that contains 70% by volume or more of a gamma prime phase in a thermodynamic equilibrium state at a temperature of 1100°C.
Ｔｉ１６．５％以下、Ｎｂ８％以下、Ｍｏ６％以下、Ｗ
６％以下、Ｃｒ１４％以下、Ｃ１％以下、Ｂ０．２％以
下、Ｚｒ０．１％以下を含有し、Ａｌ＋Ｔｉ＋Ｎｂ＋Ｍ
ｏ＋Ｗ＝１９〜２８％、かつＴｉ／１６．５＋Ｎｂ／８
＋Ｍｏ／６＋Ｗ／６≦１．２であり、残部が実質的にＮ
ｉあるいはその２０％までをＣｏで置換した組成である
特許請求範囲第１項記載の超塑性鍛造用Ｎｉ基合金。(2) Ni-based alloy composition is Al28% or less in atomic %,
Ti 16.5% or less, Nb 8% or less, Mo 6% or less, W
6% or less, Cr14% or less, C1% or less, B0.2% or less, Zr0.1% or less, Al+Ti+Nb+M
o+W=19-28% and Ti/16.5+Nb/8
+Mo/6+W/6≦1.2, and the remainder is substantially N
The Ni-based alloy for superplastic forging according to claim 1, which has a composition in which i or up to 20% of it is replaced with Co.
Ｎｂ８％以下、Ｍｏ６％以下、Ｗ６％以下、Ｃｒ１４％
以下、Ｃ１％以下、Ｂ０．２％以下、Ｚｒ０．１％以下
含有し、 Ａｔ＋Ｔｉ＋Ｎｂ＋Ｍｏ＋Ｗ＝１９〜２８％で、Ｔｉ／
１６．５＋Ｎｂ／８＋Ｍｏ／６＋Ｗ／６≦１．２％であ
り、残部が実質的にＮｉあるいはその２０％までをＣｏ
で置換した組成の粉末を、８００〜２０００気圧下で、
１０２５〜１２５０℃で３０〜２００分高温高圧処理し
た後、１０２５〜１２５０℃、押出し比４〜１５で押出
すことを特徴とする１１００℃の温度での熱力学平衡状
態において７０体積％以上のガンマプライム相を含有す
る超塑性鍛造用Ｎｉ基合金の製造法。(3) In atomic %, Al: 28% or less, Ti: 16.5% or less, Nb: 8% or less, Mo: 6% or less, W: 6% or less, Cr: 14%
Below, it contains C1% or less, B0.2% or less, Zr0.1% or less, At+Ti+Nb+Mo+W=19-28%, Ti/
16.5+Nb/8+Mo/6+W/6≦1.2%, and the remainder is substantially Ni or up to 20% of it is Co.
Powder with a composition substituted with
Gamma of 70% by volume or more in a thermodynamic equilibrium state at a temperature of 1100°C, characterized by subjecting it to high temperature and high pressure treatment at 1025 to 1250°C for 30 to 200 minutes, and then extruding at 1025 to 1250°C and an extrusion ratio of 4 to 15. A method for producing a Ni-based alloy for superplastic forging containing a prime phase.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP19397884A JPS6173852A (en) | 1984-09-18 | 1984-09-18 | Ni base alloy for super plasticity forging and its manufacture |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP19397884A JPS6173852A (en) | 1984-09-18 | 1984-09-18 | Ni base alloy for super plasticity forging and its manufacture |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6173852A true JPS6173852A (en) | 1986-04-16 |
| JPS6362577B2 JPS6362577B2 (en) | 1988-12-02 |
Family
ID=16316938
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP19397884A Granted JPS6173852A (en) | 1984-09-18 | 1984-09-18 | Ni base alloy for super plasticity forging and its manufacture |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6173852A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6447828A (en) * | 1987-08-12 | 1989-02-22 | Agency Ind Science Techn | Turbin disk by super plastic forging of different alloys |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| SE516696C2 (en) | 1999-12-23 | 2002-02-12 | Perstorp Flooring Ab | Process for producing surface elements comprising an upper decorative layer as well as surface elements produced according to the method |
-
1984
- 1984-09-18 JP JP19397884A patent/JPS6173852A/en active Granted
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6447828A (en) * | 1987-08-12 | 1989-02-22 | Agency Ind Science Techn | Turbin disk by super plastic forging of different alloys |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6362577B2 (en) | 1988-12-02 |
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| Date | Code | Title | Description |
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| EXPY | Cancellation because of completion of term |