JPH05277656A - Thin plate of alloy containing ti3al group intermetallic compound and manufacture thereof - Google Patents
Thin plate of alloy containing ti3al group intermetallic compound and manufacture thereofInfo
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- JPH05277656A JPH05277656A JP8254392A JP8254392A JPH05277656A JP H05277656 A JPH05277656 A JP H05277656A JP 8254392 A JP8254392 A JP 8254392A JP 8254392 A JP8254392 A JP 8254392A JP H05277656 A JPH05277656 A JP H05277656A
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- atomic
- intermetallic compound
- slab
- thin plate
- cast
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明はＴｉ3 Ａｌ基金属間化合
物を含む合金の薄板製造における問題点である表面割れ
の防止策に関するものであり、表面性状に優れた薄板材
の製造方法を提供するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for preventing surface cracking, which is a problem in the production of thin plates of alloys containing Ti 3 Al-based intermetallic compounds, and provides a method for producing thin plate materials having excellent surface properties. To do.
【０００２】[0002]
【従来の技術】耐環境性構造材としての材料開発が進め
られている材料にＴｉＡｌ金属間化合物、Ｔｉ3 Ａｌ金
属間化合物、Ｎｂ3 Ａｌ金属間化合物、ＦｅＡｌ金属間
化合物、Ｆｅ3 Ａｌ金属間化合物、Ａｌ3 Ｔｉ金属間化
合物等がある。これらの材料は優れた高温強度特性をも
つために将来の構造用材料としての開発が期待されてい
る。しかし、いずれの材料においても共通してみられる
問題として、その成形困難性がある。従って、薄板を製
造するためには最終製品に近いニア・ネット・シェイプ
の鋳造技術が必要である。2. Description of the Related Art TiAl intermetallic compounds, Ti 3 Al intermetallic compounds, Nb 3 Al intermetallic compounds, FeAl intermetallic compounds, and Fe 3 Al intermetallic compounds have been developed as materials for environment-resistant structural materials. There are compounds, Al 3 Ti intermetallic compounds and the like. Since these materials have excellent high-temperature strength characteristics, they are expected to be developed as future structural materials. However, a common problem with any material is its difficulty in molding. Therefore, a near net shape casting technique, which is close to the final product, is required to manufacture a thin plate.
【０００３】このようなニア・ネット・シェイプ化とし
ての薄板製造技術は最近急速に進展しており、特に金属
材料系ではステンレス・薄板製造などへの応用が進んで
いる。その薄板製造技術としては、種々の鋳造方法が提
案されているが、その中で双ロール法は厚みの一様な連
続した薄板を作製するのに適している。上記技術の金属
間化合物材料への適応例としては、微量のボロンを添加
することにより延性が改善されたニッケル・アルミニウ
ム金属間化合物（Ｎｉ3 Ａｌ）の例が知られている。こ
の例は１９８８年１１月に開催された「ニア・ネット・
シェイプ製品の鋳造」（“Ｃａｓｔｉｎｇ ｏｆ Ｎｅ
ａｒ Ｎｅｔ Ｓｈａｐｅ Ｐｒｏｄｕｃｔｓ”）に関
する国際会議に報告されている（Ｐｒｏｃｅｅｄｉｎｇ
ｓ ｏｆａｎ Ｉｎｔｅｒｎａｔｉｏｎａｌ Ｓｙｍｐ
ｏｓｉｕｍ ｏｆ ＮｅａｒＮｅｔ Ｓｈａｐｅ Ｐｒ
ｏｄｕｃｔｓ、３１５〜３３３ページ、Ｔｈｅ Ｍｅｔ
ａｌｌｕｒｇｉｃａｌ Ｓｏｃｉｅｔｙ 発行）。ま
た、ＴｉＡｌ金属間化合物薄板の製造方法は特願平１−
５０６４８号公報に記載されている。The thin plate manufacturing technique for forming such a near net shape has been rapidly developed in recent years, and the application to the production of stainless steel / thin plate is progressing especially in the metal material system. As a thin plate manufacturing technique, various casting methods have been proposed. Among them, the twin roll method is suitable for producing a continuous thin plate having a uniform thickness. As an example of applying the above technique to an intermetallic compound material, an example of a nickel-aluminum intermetallic compound (Ni 3 Al) whose ductility is improved by adding a trace amount of boron is known. An example of this is "Near Net." Held in November 1988.
"Casting of Ne"
ar Net Shape Products ”) (Proceeding)
s offan International Symp
osium of NearNet Shape Pr
products, pages 315-333, The Met
published by allrural Society). A method for manufacturing a TiAl intermetallic compound sheet is described in Japanese Patent Application No.
It is described in Japanese Patent No. 50648.
【０００４】[0004]
【発明が解決しようとする課題】薄板直接鋳造技術によ
るニア・ネット・シェイプ化は、工程省略などの利点を
有するが、鋳造後に急速冷却を伴うために薄板の欠陥
（表面割れ、ポロシティ）が生じるという欠点をもつ。
特に金属間化合物材料等の延性−脆性遷移温度が室温以
上の材料では熱歪に伴う割れが発生しやすく、この問題
は顕著である。The near net shape forming by the thin plate direct casting technique has advantages such as the omission of steps, but defects (surface cracks, porosity) of the thin plate occur due to rapid cooling after casting. It has the drawback.
In particular, a material having a ductile-brittle transition temperature of room temperature or higher, such as an intermetallic compound material, is apt to crack due to thermal strain, and this problem is remarkable.
【０００５】従って、難加工性材料を直接鋳造により薄
板を作製する際に、材質の健全性を確保するためには表
面欠陥の除去が重要な課題となる。Therefore, when a thin plate is produced by directly casting a difficult-to-process material, the removal of surface defects is an important issue for ensuring the soundness of the material.
【０００６】[0006]
【課題を解決するための手段】本発明の目的とするとこ
ろは、室温以上に延性−脆性温度遷移点をもつ難加工性
材料であるＴｉ3 Ａｌ基金属間化合物材料の直接鋳造技
術における、その製品欠陥（表面割れ、ポロシティ）を
防止する技術を提供するものである。本発明が対象とし
ている金属間化合物を含む合金は、原子％で、 ・Ａｌ：７％超〜２８％含有し、残部がＴｉからなるＴ
ｉ3 Ａｌ系金属間化合物あるいは、 ・Ａｌ：７％超〜２８％含有し、さらにＭｏ：０．５〜
３％、Ｎｂ：０．５〜１８％の１種または２種を含有
し、残部がＴｉからなるＴｉ3 Ａｌ系金属間化合物を含
む合金材料からなり、ニア・ネット・シェイプ化用装置
として、図１に示す双ドラム式連続鋳造機を用いて鋳造
した０．２５〜２５ｍｍ厚の薄板である。The object of the present invention is to provide a direct casting technique for a Ti 3 Al-based intermetallic compound material which is a difficult-to-process material having a ductile-brittle temperature transition point above room temperature. It provides technology to prevent product defects (surface cracks, porosity). The alloy containing the intermetallic compound, which is the object of the present invention, is in atomic%: Al: more than 7% to 28% and the balance is Ti
i 3 Al-based intermetallic compound or ・ Al: more than 7% to 28% and further Mo: 0.5 to
3%, Nb: 0.5 to 18% of one or two kinds, and the balance is made of an alloy material containing a Ti 3 Al-based intermetallic compound, and is used as a near net shape forming device. It is a thin plate having a thickness of 0.25 to 25 mm cast by using the twin drum type continuous casting machine shown in FIG. 1.
【０００７】本発明者らは、上述した課題を達成すべく
種々の検討を重ね、鋳造直後の熱処理を特定することが
有効であることを見出し、本発明を完成した。本発明の
別の対象は、前記難加工性材料の溶湯を双ドラム式連続
鋳造機の鋳型に注入して板状薄板鋳片を鋳造した後、鋳
造直後の該鋳片に５００〜１０００℃に一定時間保定す
ることと、その後の２００℃／ｈｒの緩冷却により熱応
力に伴う歪の発生を防止し、表面割れの発生を防止して
健全な薄板材を製造する方法にある。また、この後のＨ
ＩＰ処理によるポロシティ低減による熱間加工での伸び
の向上を図る。また、上記方法によって得られる材料の
特徴は、薄板材の表面方向に揃った柱状晶および中心部
の等軸晶組織、ＤＯ19構造相とβ−Ｔｉ相との結晶学的
相関性をもつ複合組織を具備せしめたことである。The inventors of the present invention have conducted various studies to achieve the above-mentioned problems, found that it is effective to specify the heat treatment immediately after casting, and completed the present invention. Another object of the present invention is to cast a plate-shaped thin plate slab by injecting the molten metal of the difficult-to-process material into a mold of a twin-drum type continuous casting machine, and then at 500 to 1000 ° C. in the slab immediately after casting. There is a method for producing a sound thin plate material by holding the material for a certain period of time and then slowly cooling it at 200 ° C./hr to prevent the occurrence of strain due to thermal stress and prevent the occurrence of surface cracks. Also, after this
We aim to improve elongation in hot working by reducing porosity by IP treatment. In addition, the characteristics of the material obtained by the above method are the columnar crystals aligned in the surface direction of the thin plate and the equiaxed crystal structure of the central portion, and the compound having the crystallographic correlation between the DO 19 structural phase and the β-Ti phase. That is to have an organization.
【０００８】[0008]
【作用】まず、塑性加工に有利な鋳造組織について説明
する。本発明の双ロール鋳造薄板は、鋳造ままの凝固組
織が鋳片の両表面から中心に向かう柱状晶のみか、ある
いは前記柱状晶と鋳片中心付近に存在する等軸晶との混
合組織からなっている。[Operation] First, the cast structure advantageous for plastic working will be described. The twin-roll cast thin plate of the present invention has a solidification structure as cast only columnar crystals directed from both surfaces of the slab toward the center, or a mixed structure of the columnar crystals and equiaxed crystals existing near the slab center. ing.
【０００９】次にかかる板状薄肉鋳片を鋳造する方法に
ついて説明する。一般にドラム式連続鋳造機（以下、連
鋳機という）は、２本の冷却ドラムを平行にかつ逆方向
に回転するように配置し、該冷却ドラムの外側にサイド
・ダムを設けて湯溜り部（鋳型）を構成し、該湯溜り部
内の溶湯を前記冷却ドラムの回転によって冷却しつつ薄
板鋳片を製造するようになっている。Next, a method of casting the plate-shaped thin cast piece will be described. Generally, a drum type continuous casting machine (hereinafter referred to as a continuous casting machine) has two cooling drums arranged so as to rotate in parallel and in opposite directions, and a side dam is provided outside the cooling drums to form a molten metal pool. A (mold) is configured and a thin plate cast is manufactured while cooling the molten metal in the molten metal pool by rotating the cooling drum.
【００１０】本発明では各種金属間化合物の溶湯を上記
湯溜り部に注入して薄肉鋳片を製造するが、金属間化合
物材料は延性の小さい材料であるために、鋳片の冷却中
における割れが発生し易く、従って不均一凝固の原因と
なるメニスカス部における酸化物の形成を抑制する必要
がある。このため、不活性ガス（Ａｒ、 Ｈｅなど）中
での溶解、 鋳造が必要である。In the present invention, molten metal of various intermetallic compounds is injected into the pool to manufacture a thin cast slab. However, since the intermetallic compound material is a material having low ductility, the slab is cracked during cooling. Therefore, it is necessary to suppress the formation of oxides in the meniscus portion, which easily causes uneven solidification. Therefore, it is necessary to melt and cast in an inert gas (Ar, He, etc.).
【００１１】上記の方法での直接鋳造が従来法である
が、上記の方法のみでは、特に延性−脆性遷移温度が高
温にある金属間化合物では直接鋳造に伴う急冷により、
急激な熱歪が延性−脆性の遷移温度を経た時点で亀裂を
生じさせる原因となり、細かな表面割れの原因となる。
この表面割れの除去が本発明の目的である。この問題の
解決策として、鋳型離脱後の鋳片は急激な冷却を避ける
ために２００℃／ｈｒ以下の冷却速度で２００℃以下ま
で徐冷されることが望ましい。しかし、徐冷方法として
凝固直後の鋳片を５００〜１０００℃の温度範囲に一定
時間保定してその後炉冷することにより、２００℃／ｈ
ｒより遅い冷却速度を達成してもよい。この保定温度は
熱応力による割れの発生を防止するための温度である。Although direct casting by the above-mentioned method is a conventional method, the above-mentioned method alone causes a rapid cooling accompanying the direct casting, especially in the case of an intermetallic compound having a high ductile-brittle transition temperature.
The rapid thermal strain causes a crack at the time when the ductile-brittle transition temperature is passed, which causes a fine surface crack.
The removal of this surface crack is the object of the present invention. As a solution to this problem, it is desirable that the cast slab after demolding is gradually cooled to 200 ° C. or less at a cooling rate of 200 ° C./hr or less in order to avoid rapid cooling. However, as a gradual cooling method, the slab immediately after solidification is held in the temperature range of 500 to 1000 ° C. for a certain period of time and then cooled in the furnace to obtain 200 ° C./h.
Cooling rates slower than r may be achieved. This holding temperature is a temperature for preventing the occurrence of cracks due to thermal stress.
【００１２】また、上記方法によって、材料の特徴とし
ての試料表面方向に揃った柱状晶および中心部の等軸晶
組織、ＤＯ19構造相とβ−Ｔｉ相との結晶学的相関性を
もつ複合組織が得られる。次に鋳造材のポロシティ（空
隙部）をつぶす目的でＨＩＰ処理を行う。ＨＩＰ処理条
件としては鋳片を１０００〜１４００℃（溶融温度以
下）の温度範囲で１０００気圧以上の雰囲気内に１０分
〜１時間保持する。By the above method, the columnar crystals aligned in the sample surface direction and the equiaxed crystal structure of the central portion, which are the characteristics of the material, and the compound having the crystallographic correlation between the DO 19 structural phase and the β-Ti phase are obtained. The organization is obtained. Next, HIP processing is performed for the purpose of crushing the porosity (void portion) of the cast material. As the HIP processing condition, the slab is held in a temperature range of 1000 to 1400 ° C. (melting temperature or lower) in an atmosphere of 1000 atm or higher for 10 minutes to 1 hour.
【００１３】以上の方法により、表面性状の優れたポロ
シティのない健全な、金属間化合物を含む合金の薄板を
製造することができる。By the above method, it is possible to manufacture a thin plate of an alloy containing an intermetallic compound, which is excellent in surface quality and has no porosity.
【００１４】[0014]
【実施例】アルミニウム地金とスポンジチタンおよび他
の元素（Ｍｏ、 Ｎｂ）を表１で示す組成で配合し、こ
れをプラズマアークにて溶解して母合金を精製した。次
に、上記各母合金を図１に示す鋳造機に注入し、薄肉鋳
片を鋳造した。上記鋳造機は概略次のような構成をな
す。図において金属間化合物を溶解する坩堝１の下方に
溶湯を均一供給するためのタンディシュ２を配置し、そ
の直下に冷却ドラム３とサイド・ダム４で構成する湯溜
り部５（鋳型）を設け、これらを雰囲気調整容器７内に
配設する。８は不活性ガス導入機構、９は排出機構であ
る。EXAMPLE Aluminum ingot, titanium sponge, and other elements (Mo, Nb) were mixed in the composition shown in Table 1, and this was melted by a plasma arc to refine a mother alloy. Next, each of the master alloys was poured into the casting machine shown in FIG. 1 to cast a thin cast piece. The casting machine has the following structure. In the figure, a tundish 2 for uniformly supplying a molten metal is arranged below a crucible 1 for melting an intermetallic compound, and a molten metal pool 5 (mold) composed of a cooling drum 3 and a side dam 4 is provided immediately below the tundish 2. These are arranged in the atmosphere adjusting container 7. Reference numeral 8 is an inert gas introducing mechanism, and 9 is an discharging mechanism.
【００１５】表１に示す各母合金を２０００〜３５００
ｇの重量範囲で上記坩堝に投入し、Ａｒ雰囲気中で加熱
溶解し、一旦１７００℃の温度に調整した後、幅４ｍ
ｍ、長さ９５ｍｍの開口部をもつタンディシュを介して
湯溜り部５に注入した。該湯溜り部５を構成する冷却ド
ラム３は直径３００ｍｍ、幅１００ｍｍの一対の銅合金
製であって内部冷却されている。この冷却ドラム３によ
り、溶湯を一定のドラム支持力で、かつ１０3 ℃／ｓｅ
ｃの冷却速度により急冷凝固し、表１（Ｎｏ．１、
２）に示す厚さの連続板状鋳片を作製した。Each of the mother alloys shown in Table 1 is 2000-3500.
After being put in the crucible in a weight range of g, melted by heating in an Ar atmosphere, and once adjusted to a temperature of 1700 ° C., a width of 4 m
It was poured into the pool 5 through a tundish having an opening of m and a length of 95 mm. The cooling drum 3 which constitutes the pool 5 is made of a pair of copper alloys having a diameter of 300 mm and a width of 100 mm and is internally cooled. This cooling drum 3 holds the molten metal at a constant drum supporting force and at 10 3 ° C / se.
It was rapidly solidified according to the cooling rate of c, and the results are shown in Table 1 (No. 1,
A continuous plate-shaped slab having the thickness shown in 2) was produced.
【００１６】冷却ドラム３から送り出された鋳片６は雰
囲気調整容器７内で１℃／ｓｅｃの冷却速度で徐冷され
ながら搬送系加熱炉に挿入され、該炉において表１で示
す二次冷却条件で処理された。次いで、炉の電源を止
め、２００℃以下まで冷却した。表１（Ｎｏ．３〜８）
に示すように緩冷却処理により表面割れが防止され、表
面性状が向上した。The slab 6 sent out from the cooling drum 3 is gradually cooled in the atmosphere adjusting container 7 at a cooling rate of 1 ° C./sec and then inserted into the heating furnace for the transport system. In the furnace, the secondary cooling shown in Table 1 is carried out. Treated with conditions. Then, the power of the furnace was stopped and the temperature was cooled to 200 ° C or lower. Table 1 (No. 3 to 8)
As shown in (3), the gentle cooling treatment prevented surface cracks and improved the surface properties.
【００１７】得られた鋳片の鋳造方向における断面組織
は、鋳造ままの凝固組織は鋳片の両表面から中心部に向
かう柱状晶のみか、あるいは前記柱状晶と鋳片中心部付
近に存在する等軸晶との混合組織から構成されている。
本発明法で得られた鋳片のミクロ組織はＴｉ3 Ａｌ基金
属間化合物においてはＤＯ19型構造の＜０００１＞結晶
方向が鋳片厚方向に優先的に配向した組織を中心とした
β−Ｔｉ相を含む組織が微細な層状複合構造をなしてい
るが、Ｍｏ、Ｎｂ等の第三元素が添加されていることの
ために上記層状構造が極めて微細になっており、１層の
幅が１０００ｎｍであった。第三元素を添加せずに鋳込
む通常の凝固組織においてはこの幅は１００００ｎｍで
あり、粗大な組織である。Regarding the sectional structure in the casting direction of the obtained slab, the as-cast solidification structure exists only in the columnar crystals extending from both surfaces of the slab toward the center, or in the vicinity of the columnar crystal and the slab center. It is composed of a mixed structure with equiaxed crystals.
The microstructure of the cast slab obtained by the method of the present invention is β-centered around the structure in which the <0001> crystal direction of the DO 19 type structure in the Ti 3 Al-based intermetallic compound is preferentially oriented in the cast slab thickness direction. The structure including the Ti phase has a fine layered composite structure, but the layered structure is extremely fine due to the addition of the third element such as Mo and Nb, and the width of one layer is It was 1000 nm. In a normal solidified structure that is cast without adding the third element, this width is 10,000 nm, which is a coarse structure.
【００１８】このようにして得た鋳片の室温における機
械的性質（三点曲げの破断応力）を表２に示した。本発
明例は高い値を示している。なお、緩冷却された鋳片表
面性状と冷却ドラム離脱後放冷された鋳片の表面性状を
それぞれ図２（Ａ）と（Ｂ）に示す。緩冷却された鋳片
の表面には割れが殆ど見られないが、放冷却された鋳片
の表面には細かい表面割れが認められた。Table 2 shows the mechanical properties (breaking stress of three-point bending) at room temperature of the thus obtained slab. The present invention example shows a high value. The surface texture of the slowly cooled slab and the surface texture of the slab left to cool after leaving the cooling drum are shown in FIGS. 2 (A) and 2 (B), respectively. Almost no cracks were found on the surface of the slowly cooled slab, but fine surface cracks were observed on the surface of the slab that was allowed to cool.
【００１９】なお、各試料の炉冷後の表面性状を表１に
示した。本発明例はいずれも良好であった。また、２０
０℃以下まで炉冷された鋳片に１０００℃、１５００気
圧で１時間保持のＨＩＰ処理を施したものの破断応力を
調べた。この結果を表２に示す。本発明例は比較例に比
べ破断応力は大きく、ＨＩＰ処理を施すことにより破断
応力が著しく増大することが確認された。Table 1 shows the surface texture of each sample after furnace cooling. The examples of the present invention were all good. Also, 20
The rupture stress of the slab that had been furnace-cooled to 0 ° C. or lower and subjected to the HIP treatment of holding at 1000 ° C. and 1500 atm for 1 hour was examined. The results are shown in Table 2. It was confirmed that the inventive example had a larger breaking stress than the comparative example, and that the breaking stress was remarkably increased by the HIP treatment.
【００２０】なお、ＨＩＰ処理によるポロシティ除去効
果をみるために、１２５０℃、１５００気圧、１時間保
持のＨＩＰ処理を施したところ、ＨＩＰ処理前のポロシ
ティが殆ど除去されていることがわかった。また、Ｍｏ
とＮｂの含有材について熱間加工度（８００℃、５×１
０-4ｓｅｃ-1の歪速度）を調査したところ、ＨＩＰ処理
後に１００％の伸びを得ることができ、比較例の試料と
の差は歴然たるものであった。In order to examine the porosity removing effect of the HIP treatment, HIP treatment at 1250 ° C., 1500 atm for 1 hour was performed, and it was found that most of the porosity before the HIP treatment was removed. Also, Mo
Degree of hot working (800 ℃, 5 × 1
The strain rate of 0 −4 sec −1 ) was investigated, and it was possible to obtain 100% elongation after the HIP treatment, and the difference from the sample of the comparative example was obvious.
【００２１】以上の通り、本発明によれば、得られた鋳
片または処理薄板の機械的性質は著しく改善された。こ
れは主に、第三元素の添加によりＴｉ3 Ａｌ金属間化合
物の集合組織が微細化されたことと、鋳片の保定処理、
ＨＩＰ処理の結果と考えられる。As described above, according to the present invention, the mechanical properties of the obtained slab or treated thin plate are remarkably improved. This is mainly because the texture of the Ti 3 Al intermetallic compound was refined by the addition of the third element,
This is considered to be the result of HIP processing.
【００２２】[0022]
【表１】 [Table 1]
【００２３】[0023]
【表２】 [Table 2]
【００２４】[0024]
【発明の効果】以上の実施例からも明らかな如く本発明
により製造された急冷凝固薄肉鋳片またはその処理薄板
は、従来の薄肉鋳片よりも一層優れた機械的特性や表面
性状を有しており、難加工性素材の新しい製造方法を提
供するため、工業上極めて有用である。As is apparent from the above examples, the rapidly solidified thin cast piece or the treated thin plate produced by the present invention has mechanical properties and surface properties superior to those of conventional thin cast pieces. Since it provides a new method for producing a difficult-to-process material, it is extremely useful industrially.
【図１】本発明を実施する装置の概略を示す断面側面図
である。1 is a cross-sectional side view showing the outline of an apparatus for carrying out the present invention.
【図２】（Ａ）は本発明材を鋳造後冷却したときの表面
状態を示す写真図、（Ｂ）は本発明材を鋳造後放冷した
ときの表面状態を示す写真図である。FIG. 2 (A) is a photograph showing the surface state of the material of the present invention after cooling after casting, and FIG. 2 (B) is a photograph showing the surface state of the material of the present invention after cooling after casting.
１ 坩堝 ２ タンディシュ ３、 ３ 冷却ドラム ４ サイド・ダム ５ 湯溜り部 ６ 鋳片 ７ 雰囲気調整容器 ８ 不活性ガス導入機構 ９ 排気機構 1 crucible 2 tundish 3, 3 cooling drum 4 side dam 5 molten metal pool 6 cast slab 7 atmosphere control container 8 inert gas introduction mechanism 9 exhaust mechanism
Claims (6)
を含有し、残部がＴｉからなるＴｉ3 Ａｌ系金属間化合
物を含む合金材料あるいはＡｌ：７原子％超〜２８原子
％を含有し、さらにＭｏ：０．５〜３原子％、Ｎｂ：
０．５〜１８原子％の１種または２種を含有し、残部が
ＴｉからなるＴｉ3 Ａｌ系金属間化合物を含む合金材料
からなり、鋳造ままの凝固組織が板状薄肉鋳片の両表面
から中心部に向かう柱状晶組織であって、上記鋳片の厚
さが０．２５〜２．５ｍｍであることを特徴とするＴｉ
3 Ａｌ系金属間化合物を含む合金の薄板。1. Al in atomic%: more than 7 atomic% to 28 atomic%
Alloy material containing Ti 3 Al-based intermetallic compound containing Ti and the balance being Ti or Al: more than 7 atomic% to 28 atomic%, further Mo: 0.5 to 3 atomic%, Nb:
It is made of an alloy material containing 0.5 to 18 atomic% of one or two kinds and the balance is a Ti 3 Al-based intermetallic compound composed of Ti, and the as-cast solidification structure is on both surfaces of a plate-shaped thin cast piece. Ti having a columnar crystal structure extending from the center to the center, and the thickness of the slab is 0.25 to 2.5 mm.
3 Thin alloy plate containing Al-based intermetallic compound.
が鋳片の両表面から中心に向かう柱状晶組織と鋳片中心
部付近に存在する等軸晶との混合組織からなるＴｉ3 Ａ
ｌ系金属間化合物を含む合金の薄板。2. The Ti 3 A composition according to claim 1, wherein the as-cast solidification structure is a mixed structure of a columnar crystal structure extending from both surfaces of the slab toward the center and an equiaxed crystal existing near the center of the slab.
An alloy thin plate containing an l-based intermetallic compound.
晶組織が鋳片の両表面から中心部に向かう方向にＤＯ19
構造の＜０００１＞方向が優先的に配向されていると共
に、β−Ｔｉ相とＤＯ19構造の微細複合組織で形成され
ているＴｉ3Ａｌ系金属間化合物を含む合金の薄板。3. The method according to claim 1 or 2, wherein the columnar crystal structure is DO 19 in a direction from both surfaces of the cast slab toward the center.
A thin plate of an alloy containing a Ti 3 Al-based intermetallic compound which is preferentially oriented in the <0001> direction of the structure and which has a β-Ti phase and a fine composite structure of a DO 19 structure.
を含有し、残部がＴｉからなるＴｉ3 Ａｌ系金属間化合
物を含む合金材料あるいはＡｌ：７原子％超〜２８原子
％を含有し、さらにＭｏ：０．５〜３原子％、Ｎｂ：
０．５〜１８原子％の１種または２種を含有し、残部が
ＴｉからなるＴｉ3 Ａｌ系金属間化合物を含む合金材料
の溶湯を不活性ガス雰囲気中の双ドラム式連続鋳造機の
鋳型に注入し、双ドラムにより急冷凝固して０．２５〜
２．５ｍｍの板状薄肉鋳片を鋳造し、得られた鋳片が上
記双ドラムから離脱した直後に２００℃／ｈｒ以下の冷
却速度で２００℃以下まで冷却することを特徴とするＴ
ｉ3 Ａｌ系金属間化合物を含む合金の薄板の製造方法。4. Al in atomic%: more than 7 atomic% to 28 atomic%
Alloy material containing Ti 3 Al-based intermetallic compound containing Ti and the balance being Ti or Al: more than 7 atomic% to 28 atomic%, further Mo: 0.5 to 3 atomic%, Nb:
Mold of twin-drum type continuous casting machine containing molten alloy material containing 0.5 to 18 atomic% of 1 or 2 and the balance of Ti 3 Al based intermetallic compound consisting of Ti in an inert gas atmosphere 0.25 to 0.25
A 2.5 mm plate-shaped thin cast piece is cast, and the obtained cast piece is cooled to 200 ° C. or less at a cooling rate of 200 ° C./hr or less immediately after being separated from the twin drum.
A method for manufacturing a thin plate of an alloy containing an i 3 Al-based intermetallic compound.
却した鋳片を１０００℃以上の温度および１０００気圧
以上の雰囲気のもとで高温静水圧による圧下処理を行う
ことを特徴とするＴｉ3 Ａｌ系金属間化合物を含む合金
の薄板の製造方法。5. The Ti 3 Al according to claim 4, wherein the slab cooled to 200 ° C. or lower is subjected to a reduction treatment by high temperature hydrostatic pressure in a temperature of 1000 ° C. or higher and an atmosphere of 1000 atmospheric pressure or higher. A method for manufacturing a thin plate of an alloy containing a base intermetallic compound.
離脱した直後に、５００〜１０００℃の温度範囲に１〜
２０分間保持し、続いて２００℃／ｈｒ以下の冷却速度
で室温まで冷却することを特徴とするＴｉ3 Ａｌ系金属
間化合物を含む合金の薄板の製造方法。6. The method according to claim 4, wherein the slab is separated from the twin drum, and immediately after the cast slab is separated from the twin drum, the temperature range of 500 to 1000.degree.
A method for producing a thin plate of an alloy containing a Ti 3 Al-based intermetallic compound, which is maintained for 20 minutes and then cooled to room temperature at a cooling rate of 200 ° C./hr or less.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP8254392A JPH05277656A (en) | 1992-04-04 | 1992-04-04 | Thin plate of alloy containing ti3al group intermetallic compound and manufacture thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP8254392A JPH05277656A (en) | 1992-04-04 | 1992-04-04 | Thin plate of alloy containing ti3al group intermetallic compound and manufacture thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH05277656A true JPH05277656A (en) | 1993-10-26 |
Family
ID=13777424
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP8254392A Withdrawn JPH05277656A (en) | 1992-04-04 | 1992-04-04 | Thin plate of alloy containing ti3al group intermetallic compound and manufacture thereof |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH05277656A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1322156C (en) * | 2003-12-24 | 2007-06-20 | 中国科学院金属研究所 | Titanium three-aluminum base alloy and method for preparing same |
| JP2015501224A (en) * | 2011-09-30 | 2015-01-15 | ゼネラル・エレクトリック・カンパニイ | Titanium aluminide article having improved surface finish and method for producing the same |
| US8956472B2 (en) | 2008-11-07 | 2015-02-17 | Alcoa Inc. | Corrosion resistant aluminum alloys having high amounts of magnesium and methods of making the same |
| CN107299250A (en) * | 2017-05-26 | 2017-10-27 | 中国科学院金属研究所 | As cast condition is tough Ti3Al intermetallic compounds and its manufacture method and application |
| CN109504874A (en) * | 2018-10-26 | 2019-03-22 | 中国航发北京航空材料研究院 | A kind of Ti3The preparation method of Al alloy bolt |
-
1992
- 1992-04-04 JP JP8254392A patent/JPH05277656A/en not_active Withdrawn
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1322156C (en) * | 2003-12-24 | 2007-06-20 | 中国科学院金属研究所 | Titanium three-aluminum base alloy and method for preparing same |
| US8956472B2 (en) | 2008-11-07 | 2015-02-17 | Alcoa Inc. | Corrosion resistant aluminum alloys having high amounts of magnesium and methods of making the same |
| JP2015501224A (en) * | 2011-09-30 | 2015-01-15 | ゼネラル・エレクトリック・カンパニイ | Titanium aluminide article having improved surface finish and method for producing the same |
| CN107299250A (en) * | 2017-05-26 | 2017-10-27 | 中国科学院金属研究所 | As cast condition is tough Ti3Al intermetallic compounds and its manufacture method and application |
| CN109504874A (en) * | 2018-10-26 | 2019-03-22 | 中国航发北京航空材料研究院 | A kind of Ti3The preparation method of Al alloy bolt |
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