JPH04176850A - Production of superalloy thin strip - Google Patents
Production of superalloy thin stripInfo
- Publication number
- JPH04176850A JPH04176850A JP17031890A JP17031890A JPH04176850A JP H04176850 A JPH04176850 A JP H04176850A JP 17031890 A JP17031890 A JP 17031890A JP 17031890 A JP17031890 A JP 17031890A JP H04176850 A JPH04176850 A JP H04176850A
- Authority
- JP
- Japan
- Prior art keywords
- superalloy
- strip
- ribbon
- thin strip
- superplasticity
- 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.)
- Pending
Links
- 229910000601 superalloy Inorganic materials 0.000 title claims abstract description 42
- 238000004519 manufacturing process Methods 0.000 title claims description 11
- 230000032683 aging Effects 0.000 claims abstract description 16
- 238000001816 cooling Methods 0.000 claims abstract description 15
- 239000012298 atmosphere Substances 0.000 claims abstract description 6
- 238000011282 treatment Methods 0.000 claims description 17
- 239000002184 metal Substances 0.000 claims description 13
- 229910052751 metal Inorganic materials 0.000 claims description 13
- 239000000203 mixture Substances 0.000 claims description 4
- 238000002347 injection Methods 0.000 claims 1
- 239000007924 injection Substances 0.000 claims 1
- 238000002844 melting Methods 0.000 abstract description 6
- 230000008018 melting Effects 0.000 abstract description 6
- 230000000171 quenching effect Effects 0.000 abstract description 4
- 238000010791 quenching Methods 0.000 abstract description 3
- 239000000155 melt Substances 0.000 abstract 1
- 238000000034 method Methods 0.000 description 22
- 238000005096 rolling process Methods 0.000 description 12
- 239000000463 material Substances 0.000 description 11
- 238000001513 hot isostatic pressing Methods 0.000 description 7
- 239000007789 gas Substances 0.000 description 6
- 238000010438 heat treatment Methods 0.000 description 6
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 4
- 238000005242 forging Methods 0.000 description 4
- 238000002074 melt spinning Methods 0.000 description 4
- 239000012300 argon atmosphere Substances 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 238000009689 gas atomisation Methods 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 239000000843 powder Substances 0.000 description 3
- 238000007712 rapid solidification Methods 0.000 description 3
- 229910052786 argon Inorganic materials 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 230000003679 aging effect Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000000280 densification Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000002149 energy-dispersive X-ray emission spectroscopy Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000010275 isothermal forging Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
Landscapes
- Continuous Casting (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
この発明は、ハニカム構造のコアー等に供して好適な超
合金薄帯に関し、特にかかる製品への加工の際に望まれ
る超塑性特性をそなえる薄帯を、有利に製造する方法を
提案しようとするものである。[Detailed Description of the Invention] (Industrial Application Field) The present invention relates to a superalloy ribbon suitable for use as a core of a honeycomb structure, etc., and in particular, a superalloy ribbon having superplastic properties desired when processed into such products. The present invention is intended to propose a method for manufacturing thin ribbons advantageously.
（従来の技術）
近年の進歩に伴う高速化の要請から、ガスタービンエン
ジン用、ディーゼルエンジン用をはじめ連続的に過酷な
高温ガス流に曝される機械部品が増大し、良好な高温強
度、耐熱性をもつ合金の使とする超合金である。このよ
うな超合金は、従来の鍛造法においては、加工が難しい
ことから、超塑性を利用して鍛造成形しようとする方法
が開発された。(Conventional technology) Due to the demand for higher speeds accompanying recent advances, the number of mechanical parts that are continuously exposed to harsh high-temperature gas flows, such as those for gas turbine engines and diesel engines, has increased. It is a superalloy that is used as an alloy with properties. Since such superalloys are difficult to process using conventional forging methods, a method of forging using superplasticity has been developed.
ここで超塑性現象は、結晶粒度と密接な関連があり、結
晶粒径が小さいほど優れた超塑性が現れることから、近
年、粒径が小さなものを得る手段として、ガスアトマイ
ズ、メルトスピニング等により急冷した粉末を用いる技
術が提案されている。Here, the superplastic phenomenon is closely related to the crystal grain size, and the smaller the crystal grain size, the better the superplasticity. Therefore, in recent years, rapid cooling using gas atomization, melt spinning, etc. A technique using powdered powder has been proposed.
例えば、特開昭５８−８７２０４号公報では、超合金粉
末をガスアトマイズ法により作製し、これを熱間静水圧
プレス処理（ＨＩＰ）Ｌ、恒温鍛造により超合金成形品
を得る方法が提案されている。また特開昭５８−８４９
０４号公報には、ガスアトマイズ溶滴を型で捕集し、得
られたプレフォームを再結晶温度以下に加熱処理し、Ｈ
ＩＰにより緻密化する方法が提案されている。For example, JP-A-58-87204 proposes a method in which a superalloy powder is produced by gas atomization, and then a superalloy molded product is obtained by hot isostatic pressing (HIP) and isothermal forging. . Also, JP-A-58-849
No. 04 discloses that gas atomized droplets are collected in a mold, the obtained preform is heat-treated to a temperature below the recrystallization temperature, and H
A method of densification using IP has been proposed.
これらの方法はいずれも、適切な急冷条件を選定するこ
とにより粒径を小さくでき、ＨＩＰ後に超塑性を得るこ
とは可能であるが、ＨＩＰにより固化し熱処理した際、
予め微細化した粒が局所的に成長して粒径がばらつく他
、恒温鍛造時のパウダー粒界の残存など、超塑性化を阻
害する材質上の問題があった。また超合金プリフォーム
を得るためにＨＩＰ等の多（のプロセスが必要となって
経済的とは言えない。さらに超合金薄帯とするためには
、より多くのプロセスを経る必要があるばかりか、得ら
れた薄帯が超塑性をそなえているとは限らなかった。In all of these methods, it is possible to reduce the particle size by selecting appropriate quenching conditions and obtain superplasticity after HIP, but when solidified by HIP and heat treated,
In addition to local growth of pre-refined grains, resulting in variation in grain size, there were also material-related problems that inhibited superplasticization, such as residual powder grain boundaries during constant-temperature forging. Furthermore, in order to obtain a superalloy preform, multiple processes such as HIP are required, which is not economical.Furthermore, in order to obtain a superalloy ribbon, it is not only necessary to undergo many more processes. However, the obtained ribbon did not necessarily have superplasticity.
また特開昭６３−３０９３６０号公報には、金ｌｌｉ溶
湯を急冷凝固させて金属薄帯板を得るメルトスピニング
法を用いて超合金薄帯板を製造する方法が提案されてい
る。この方法では、ＨＩＰ等の多くのプロセスを経るこ
となく、超合金薄帯を製造することが可能であるが、時
効処理としてＨＩＰ固化固化様同様えば９５０℃、２時
間次いで１０５０℃、２５時間といった２度、３度の熱
処理が必要となり、経済的でなく、かつ粒成長の要因と
なってしまう。Further, Japanese Patent Application Laid-Open No. 63-309360 proposes a method for producing a superalloy thin strip using a melt spinning method in which a metal thin strip is obtained by rapidly solidifying a gold molten metal. With this method, it is possible to produce superalloy ribbons without going through many processes such as HIP, but as with HIP solidification, aging treatment is performed at 950°C for 2 hours and then at 1050°C for 25 hours. Heat treatment is required two or three times, which is not economical and causes grain growth.
また金属間化合物を生成するＡＩ、 Ｔｉ、 Ｔａ、
Ｎｂ、 Ｍ。Also, AI, Ti, Ta, which generates intermetallic compounds
Nb, M.
などの活性金属成分を含有した溶融金属超合金の薄板は
、酸化しやすく表面性状が悪い。このため連続的に広幅
の超合金薄帯は得難かった。さらに得られた薄帯が超塑
性をそなえているとは限らなかった。Thin sheets of molten metal superalloys containing active metal components such as molten metal superalloys are susceptible to oxidation and have poor surface properties. For this reason, it has been difficult to obtain a continuous wide superalloy ribbon. Furthermore, the obtained ribbon did not always have superplasticity.
（発明が解決しようとする課題）
多数の製造プロセスを経ることなどの問題を有利に解決
して、かつ超塑性特性をそなえた超合金薄帯の製造方法
を提案することがこの発明の目的である。(Problems to be Solved by the Invention) It is an object of the present invention to propose a method for manufacturing a superalloy ribbon that advantageously solves problems such as going through a large number of manufacturing processes and has superplastic properties. be.
（課題を解決するための手段）
上述した各問題を解決すべく超合金薄帯を双ロール法に
よって製造するこの発明は、真空又は不活性雰囲気中で
溶解した超合金組成の溶湯を、板厚に相当する間隙を隔
てて横軸平行配置した、互いに向かい合って回転させる
一対の冷却用ロールの上部からこれらのロール間隙に向
け注入して、急冷凝固・圧延することで板厚１■以下の
急冷薄帯とした後、この急冷薄帯に処理温度９００〜１
０００℃、処理時間１５〜２５時間の時効処理を施すこ
とで微細結晶粒超塑性特性を有する超合金薄帯の製造方
法である。(Means for Solving the Problems) In order to solve the above-mentioned problems, the present invention manufactures a superalloy ribbon by a twin roll method. A pair of cooling rolls, which are arranged parallel to each other on the horizontal axis with a gap equivalent to After forming into a thin ribbon, the quenched ribbon was subjected to a processing temperature of 900 to 1
This is a method for producing a superalloy ribbon having fine grain superplastic properties by performing an aging treatment at 000°C for a treatment time of 15 to 25 hours.
（作 用）
以下この発明に従う超合金薄帯の製造方法を具体的に説
明する。(Function) The method for producing a superalloy ribbon according to the present invention will be specifically explained below.
第１図に、この発明を実施するための双ロール法による
薄帯製造装置の一例を示す０図中１は溶解炉、２は超合
金組成の溶湯、３は冷却用ロール、４は圧力調整器、５
は超合金薄帯である。溶解炉１内にて、ＡＩ、 Ｔｉ、
Ｔａ５Ｎｂ又はＭＯ等の活性金属成分を含有す、る超
合金をアルゴン雰囲気中で溶解し、この溶湯を収容する
。第１図では、Ａｒリザーバー６からアルゴンガスを供
給して溶解炉１中をアルゴン雰囲気としているが、この
発明ではアルゴン雰囲気に限ることはなく、不活性雰囲
気、又は真空雰囲気とする。真空雰囲気の場合は、真空
ポンプなどを用いればよい。Fig. 1 shows an example of a ribbon manufacturing apparatus using a twin roll method for carrying out the present invention. vessel, 5
is a superalloy ribbon. In the melting furnace 1, AI, Ti,
A superalloy containing an active metal component such as Ta5Nb or MO is melted in an argon atmosphere and the molten metal is contained. In FIG. 1, argon gas is supplied from the Ar reservoir 6 to create an argon atmosphere in the melting furnace 1, but the present invention is not limited to an argon atmosphere, and may be an inert atmosphere or a vacuum atmosphere. In the case of a vacuum atmosphere, a vacuum pump or the like may be used.
次に溶解炉ｌ内に収容した超合金組成の溶湯２を、溶解
炉１の下部に取りつけたノズル１ａを通じて超合金組成
の溶湯２を横軸平行配置にした、互いに向かい合って回
転させる一対の冷却用ロール３．３′のロール間隙に向
け注入し、急冷凝固・圧延する。この冷却用ロール３．
３′には、所定の圧下刃が加わるようになっていて、圧
力調整器４．４′によりこの圧下刃が調整される。かか
る圧下刃は、板厚１ｍ以下の薄帯を作るために必要であ
る。例えば１，１〜１０ ｔがよい。Next, the molten metal 2 of the superalloy composition housed in the melting furnace 1 is cooled through a nozzle 1a attached to the lower part of the melting furnace 1, and the molten metal 2 of the superalloy composition is rotated facing each other with horizontal axes parallel to each other. It is injected into the gap between the rolls 3 and 3', and is rapidly solidified and rolled. This cooling roll 3.
A predetermined reduction blade is applied to 3', and this reduction blade is adjusted by a pressure regulator 4.4'. Such a reduction blade is necessary to make a thin strip with a thickness of 1 m or less. For example, 1.1 to 10 t is good.
冷却用ロール３．３′によって急冷凝固・圧延して得ら
れる超合金薄帯は、冷却速度１０３°Ｃ／ｓ以上を得て
、均一に急冷凝固させるために板厚が１ｍ＋以下である
ことが必要である。かくして急冷された超合金薄帯の粒
径は、３μｍ以下となって、超塑性特性を得るのに十分
に細かい粒径となる。The superalloy ribbon obtained by rapid solidification and rolling by the cooling roll 3.3' must have a thickness of 1 m+ or less in order to obtain a cooling rate of 103 ° C / s or more and to achieve uniform rapid solidification. is necessary. The grain size of the superalloy ribbon thus quenched is 3 μm or less, which is sufficiently fine to obtain superplastic properties.
ところでＮｉ基超超合金おいて、超塑性現象が出現する
ためには、オーステナイト相（γ）へ、中間相であるＴ
′相が析出することが必須とされている。その理由は、
Ｔ′相は微細析出相であって、耐熱性があり、さらに時
効処理により微細等軸晶となり変形中も粒界を維持する
からである。ここでこの発明に従う双ロール法による板
厚１ｒｍ以下の急冷凝固材は、冷却速度も１０″″Ｃ／
ｓ以上と大きく、さらに圧延による歪の導入、二次冷却
での復熱時効効果により第２図（ａ）に透過電子顕微鏡
による鋳造ままの材料の金属組織写真を、同図（ｂ）に
そのＸ線写真を示すように、鋳造ままの材料で、規則格
子であるＴ′相が析出している。また薄帯の両表面は、
冷却用ロールによる急冷凝固・圧延時の酸化が少なく、
欠陥も少ない。By the way, in order for the superplastic phenomenon to appear in Ni-based superalloys, the intermediate phase T
It is essential that the ' phase precipitates. The reason is,
This is because the T' phase is a fine precipitated phase and has heat resistance, and furthermore, it becomes fine equiaxed crystals by aging treatment and maintains grain boundaries even during deformation. Here, the rapidly solidified material with a plate thickness of 1 rm or less produced by the twin roll method according to the present invention has a cooling rate of 10''C/
Due to the introduction of strain due to rolling and the recuperative aging effect during secondary cooling, the metallographic structure of the as-cast material is shown in Figure 2 (a) using a transmission electron microscope, and in Figure 2 (b). As shown in the X-ray photograph, the T' phase, which is an ordered lattice, is precipitated in the as-cast material. Also, both surfaces of the thin strip are
Less oxidation during rapid solidification and rolling with cooling rolls,
There are few defects.
しかしこの鋳造ままの材料は、第３図（ａ）に金属組織
写真を、同図（ｂ）にＭ２３Ｃ６を同定するために行っ
たＥ Ｄ Ｘ （Ｅｎｅｒｇｙ Ｄｉｓｐｅｒｓｉｏｎ
Ｘ−ｒａｙ ）分析のチャート図を示すように、粒界
にＭｚ、Ｃ６の微細な炭化物が析出していて、この鋳造
ままの材料自身の超塑性特性の出現を阻害してしまう、
そこでこの発明では、時効熱処理を、均質化を目的とし
て９００〜１０００℃、１５〜２５時間の時効処理条件
を急冷凝固した鋳造ままの薄板に適用すること乙こより
析出物のうち特に炭化物は固溶させ、一方Ｔ′相は粗大
化させることがないので、超塑性を出現させることが可
能となるのである。However, this as-cast material was subjected to an energy dispersion (ED
As shown in the X-ray) analysis chart, fine carbides of Mz and C6 are precipitated at the grain boundaries, which inhibits the appearance of superplastic properties of the as-cast material itself.
Therefore, in this invention, aging heat treatment is applied to an as-cast thin plate that has been rapidly solidified under aging treatment conditions of 900 to 1000°C for 15 to 25 hours for the purpose of homogenization. On the other hand, since the T' phase is not coarsened, it is possible to exhibit superplasticity.
ここに時効処理温度が９００°Ｃに満たないと炭化物が
固溶しない不利があり、また１０００°Ｃを超えるとＴ
′相が再結晶し粗大化するという問題点がある。同様に
時効処理時間が１５時間に満たないと炭化物が完全固溶
しないといった不利があり、また２５時間を超えると粒
径粗大化という問題点があるので、時効処理条件は、処
理温度９００〜１０００°Ｃ２処理時間１５〜２５時間
とする。Here, if the aging treatment temperature is less than 900°C, there is a disadvantage that the carbide does not dissolve into solid solution, and if it exceeds 1000°C, T
There is a problem that the ' phase recrystallizes and becomes coarse. Similarly, if the aging treatment time is less than 15 hours, there is a disadvantage that carbides are not completely dissolved, and if it exceeds 25 hours, there is a problem of coarsening of the grain size. Therefore, the aging treatment conditions are as follows: The treatment time at °C2 is 15 to 25 hours.
なお従来知られている超合金の時効熱処理としては、固
溶化処理後の熱処理として例えば９００〜１１００″Ｃ
１３〜６時間次いで８００〜１０００°Ｃで１８〜２２
時間の２段処理が知られている。In addition, conventionally known aging heat treatment for superalloys includes heat treatment at 900 to 1100''C after solution treatment.
13-6 hours then 18-22 at 800-1000°C
Two-stage processing of time is known.
またこの発明に適用する超合金としては、ニッケル基超
合金としてＩＮ ６００、ＩＮ ７１３、ＩＮ １００
、ｌＮ６１７、Ｍａｒ−Ｍ２４７等が、またコバルト基
超合金としてＭａｒ−Ｍ３２２等が代表例として挙げら
れるが、これらにかぎるものではない。In addition, examples of superalloys applicable to this invention include IN 600, IN 713, and IN 100 as nickel-based superalloys.
, IN617, Mar-M247, etc., and cobalt-based superalloys such as Mar-M322, but are not limited to these.
（実施例）
以下この発明にしたがい双ロール法により超合金薄帯を
製造した実施例を、比較例とともに述べる。(Example) Hereinafter, an example in which a superalloy ribbon was manufactured by the twin roll method according to the present invention will be described together with a comparative example.
超合金材料として、表１に示す各成分になる４種の超合
金を用意した。Four types of superalloys having the respective components shown in Table 1 were prepared as superalloy materials.
表１
これらの超合金をＡｒ雰囲気中で熔解し、溶湯温度１６
５０℃で以下に示す各急冷プロセスで薄板を製造した。Table 1 These superalloys were melted in an Ar atmosphere and the molten metal temperature was 16
Sheets were produced at 50° C. with each of the quenching processes described below.
（１）双ロール法・・・回転冷却用ロールは６００φ、
ロール周速を３〜７＋＋＋／ｓに設定した。(1) Twin roll method...rotating cooling roll is 600φ,
The roll circumferential speed was set at 3 to 7+++/s.
（２）メルトスピニング法・・・冷却用ロールは、１ｏ
ｏｏφ、ロール周速は２５〜３５ｍ／ｓに設定した。(2) Melt spinning method...cooling roll is 1o
ooφ, and the roll circumferential speed was set at 25 to 35 m/s.
（３）ガスアトマイズ法・・・アルゴンガス、圧力１０
ｋｇｆ／ｍＩ２、その後固化ＨＩＰして鍛造加工かくし
て得られた超合金薄帯の板厚及び施した熱処理について
表２にまとめて示す。(3) Gas atomization method...Argon gas, pressure 10
kgf/mI2, followed by solidification HIP and forging. Table 2 summarizes the plate thickness and heat treatment of the thus obtained superalloy ribbon.
表 ２
これらの試料について、１０５０°Ｃ歪速度０．０２１
／ｍｉｎで引張り試験を行って、超塑性特性を調べた。Table 2 For these samples, 1050°C strain rate 0.021
A tensile test was carried out at /min to examine the superplastic properties.
なお超塑性特性は、１０５０°Ｃでの引張り試験での伸
びが８００％を超す延性で評価した。The superplastic properties were evaluated based on the ductility, where the elongation exceeded 800% in a tensile test at 1050°C.
その結果、この発明に従い双ロール法によって板厚１■
以下（冷却速度１０３°Ｃ／ｓ以上）の薄帯を製造し、
９００〜１０００°Ｃ５１５〜２５時間の範囲の種々の
時効処理を行ったＮｏ、 １〜５は、鋳造のままの材料
のＴ′相の析出相を保持したまま、炭化物時効処理をお
こなったために超塑性が安定して得られた。一方、板厚
又は時効処理条件がこの発明を満足しない試料Ｎｏ、
６〜工２は、超塑性が得られなかった。さらにメルトス
ピニング法を用いた試料Ｎｏ、 １３〜１６、アトマイ
ズ法を用いた試料ｋ１７、インゴット法で試作した試料
Ｎｏ、１８は、いずれも超塑性が得られなかった。As a result, according to the present invention, a plate thickness of 1 cm was obtained using the twin roll method.
Producing a ribbon with the following (cooling rate of 103 ° C / s or more),
Nos. 1 to 5, which were subjected to various aging treatments in the range of 900 to 1000°C for 515 to 25 hours, were super-aged because the carbide aging treatment was performed while retaining the precipitated T' phase of the as-cast material. Stable plasticity was obtained. On the other hand, sample No. whose plate thickness or aging treatment conditions do not satisfy the present invention,
In Steps 6 to 2, superplasticity was not obtained. Furthermore, samples Nos. 13 to 16 using the melt spinning method, sample k17 using the atomizing method, and sample No. 18 using the ingot method did not exhibit superplasticity.
（発明の効果）′
かくしてこの発明によれば、超合金薄帯を双ロール法に
より製造することから、以下のような効果を得ることが
できる。(Effects of the Invention) According to the present invention, since the superalloy ribbon is manufactured by the twin roll method, the following effects can be obtained.
（１）溶湯から直接製板することにより、プロセスの省
略さらには時間短縮を図ることができる。(1) By directly manufacturing the plate from the molten metal, it is possible to eliminate processes and shorten the time.
（２）双ロール法により、薄帯の表面性状の劣化（酸化
、欠陥）が阻止される。また鋳造ままの材料でＴ′相の
析出が可能となり、時効熱処理はオーステナイト材の粒
界析出炭化物の固溶処理のみで２段時効を行わずに済み
、プロセスの省略を図ることができる。(2) The twin roll method prevents deterioration (oxidation, defects) of the surface properties of the ribbon. Further, it is possible to precipitate the T' phase in the as-cast material, and the aging heat treatment is only a solid solution treatment of grain boundary precipitated carbides of the austenitic material, eliminating the need for two-stage aging, making it possible to omit the process.
（３）急冷効果である粒径の微細化が維持でき、優れた
超塑性を得ることができる。(3) Fine grain size, which is a quenching effect, can be maintained and excellent superplasticity can be obtained.
第１図は、この発明を実施するための双ロール法による
薄帯製造装置の一例の説明図、第２図（ａ）は、透過電
子顕微鏡による鋳造ままの材料の金属組織写真、同図（
ｂ）はその鋳造ままの材料のＸ線写真、
第３図（ａ）はＭｚｓＣｂの金属組織写真、同図（ｂ）
はこのＭ２３Ｃ６を同定するために行ったＥＤＸ分析の
チャート図である。
１・・・溶解炉 １ａ・・・ノズル２・・・
超合金組成の溶湯 ３・・・冷却用ロール４・・・圧下
力調整装置 ５・・・超合金薄帯６・・・Ａｒガスリ
ザーバーFIG. 1 is an explanatory diagram of an example of a ribbon manufacturing apparatus using a twin-roll method for carrying out the present invention, and FIG.
b) is an X-ray photograph of the as-cast material, Figure 3 (a) is a photograph of the metallographic structure of MzsCb, and Figure 3 (b) is a photograph of the metallographic structure of MzsCb.
is a chart of EDX analysis performed to identify this M23C6. 1... Melting furnace 1a... Nozzle 2...
Molten metal of superalloy composition 3... Cooling roll 4... Reduction force adjustment device 5... Superalloy ribbon 6... Ar gas reservoir
Claims (1)
湯を、板厚に相当する間隙を隔てて横軸平行配置した、
互いに向かい合って回転させる一対の冷却用ロールの上
部からこれらのロール間隙に向け注入して、急冷凝固・
圧延することで板厚１ｍｍ以下の急冷薄帯とした後、こ
の急冷薄帯に処理温度９００〜１０００℃、処理時間１
５〜２５時間の時効処理を施すことを特徴とする超合金
薄帯の製造方法。1. Molten metal having a superalloy composition melted in a vacuum or an inert atmosphere is arranged parallel to the horizontal axis with a gap corresponding to the thickness of the plate.
The injection is injected from the top of a pair of cooling rolls that rotate facing each other into the gap between these rolls to rapidly solidify and solidify.
After being rolled into a quenched ribbon with a thickness of 1 mm or less, the quenched ribbon is subjected to a treatment temperature of 900 to 1000°C and a treatment time of 1.
A method for producing a superalloy ribbon, characterized by subjecting it to an aging treatment for 5 to 25 hours.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17031890A JPH04176850A (en) | 1990-06-29 | 1990-06-29 | Production of superalloy thin strip |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17031890A JPH04176850A (en) | 1990-06-29 | 1990-06-29 | Production of superalloy thin strip |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH04176850A true JPH04176850A (en) | 1992-06-24 |
Family
ID=15902738
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP17031890A Pending JPH04176850A (en) | 1990-06-29 | 1990-06-29 | Production of superalloy thin strip |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH04176850A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2017221965A (en) * | 2016-06-16 | 2017-12-21 | 新日鐵住金株式会社 | Ni-BASED HEAT-RESISTANT ALLOY WELD METAL |
| CN114559001A (en) * | 2022-03-08 | 2022-05-31 | 太原科技大学 | High-temperature alloy double-roller casting and rolling process |
-
1990
- 1990-06-29 JP JP17031890A patent/JPH04176850A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2017221965A (en) * | 2016-06-16 | 2017-12-21 | 新日鐵住金株式会社 | Ni-BASED HEAT-RESISTANT ALLOY WELD METAL |
| CN114559001A (en) * | 2022-03-08 | 2022-05-31 | 太原科技大学 | High-temperature alloy double-roller casting and rolling process |
| CN114559001B (en) * | 2022-03-08 | 2024-04-12 | 太原科技大学 | High-temperature alloy twin-roll casting and rolling process |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US11603583B2 (en) | Ribbons and powders from high strength corrosion resistant aluminum alloys | |
| US3920489A (en) | Method of making superalloy bodies | |
| JP7049312B2 (en) | Ribbons and powders from high-strength corrosion-resistant aluminum alloys | |
| WO2021004579A1 (en) | Nckel base alloy for powder and method for producing a powder | |
| EP0460234B1 (en) | Sheet of titanium-aluminum intermetallic compound and process for producing the same | |
| JP2798842B2 (en) | Manufacturing method of high strength rolled aluminum alloy sheet | |
| US5028277A (en) | Continuous thin sheet of TiAl intermetallic compound and process for producing same | |
| JPH04176850A (en) | Production of superalloy thin strip | |
| JPS6362582B2 (en) | ||
| JPH05277656A (en) | Thin plate of alloy containing ti3al group intermetallic compound and manufacture thereof | |
| JPS6283453A (en) | Manufacture of aluminum alloy ingot for extrusion | |
| US4481034A (en) | Process for producing high hafnium carbide containing alloys | |
| JPS60238460A (en) | Manufacture of superplastic aluminum alloy | |
| JP2958792B2 (en) | Method for producing TiA1 intermetallic compound sheet | |
| JPH0617486B2 (en) | Method for forging powder-made Ni-base superalloy | |
| CN117403154A (en) | Heat treatment process suitable for laser near-net forming nickel-titanium shape memory alloy | |
| JP3694341B2 (en) | TiAl intermetallic compound based alloy material with excellent high temperature characteristics and method for producing the same | |
| JP2901345B2 (en) | Titanium-aluminum intermetallic compound sheet and method for producing the same | |
| JPH11216556A (en) | Manufacture of semi finished steel or nickelous system alloy | |
| JP2954779B2 (en) | Method for producing high-strength nickel-based alloy | |
| JPH02224803A (en) | Production of sheet of intermetallic compound | |
| Yoshizawa et al. | Characterization of Nickel Base Superalloy Consolidated From Rapidly Solidified Ribbons | |
| JPH0237416B2 (en) | ||
| JPH05287453A (en) | Sheet of alloy containing fe3al base intermetallic compound and its production | |
| JPH0621327B2 (en) | Manufacturing method of metal consolidated material |