JPH0344437A - Ti-al intermetallic compound thin sheet and its manufacture - Google Patents
Ti-al intermetallic compound thin sheet and its manufactureInfo
- Publication number
- JPH0344437A JPH0344437A JP5030790A JP5030790A JPH0344437A JP H0344437 A JPH0344437 A JP H0344437A JP 5030790 A JP5030790 A JP 5030790A JP 5030790 A JP5030790 A JP 5030790A JP H0344437 A JPH0344437 A JP H0344437A
- Authority
- JP
- Japan
- Prior art keywords
- thin plate
- intermetallic compound
- thickness
- sec
- thin sheet
- 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.)
- Granted
Links
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 20
- 229910021362 Ti-Al intermetallic compound Inorganic materials 0.000 title abstract 2
- 239000013078 crystal Substances 0.000 claims abstract description 18
- 238000001816 cooling Methods 0.000 claims abstract description 17
- 229910052751 metal Inorganic materials 0.000 claims abstract description 13
- 239000002184 metal Substances 0.000 claims abstract description 12
- 239000011261 inert gas Substances 0.000 claims abstract description 9
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 4
- 229910000765 intermetallic Inorganic materials 0.000 claims description 18
- 229910010038 TiAl Inorganic materials 0.000 claims description 11
- 230000002093 peripheral effect Effects 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 2
- 229910045601 alloy Inorganic materials 0.000 abstract description 7
- 239000000956 alloy Substances 0.000 abstract description 7
- 229910004349 Ti-Al Inorganic materials 0.000 abstract 1
- 229910004692 Ti—Al Inorganic materials 0.000 abstract 1
- 238000010438 heat treatment Methods 0.000 abstract 1
- 238000000034 method Methods 0.000 description 26
- 238000005096 rolling process Methods 0.000 description 14
- 239000010936 titanium Substances 0.000 description 12
- 238000005266 casting Methods 0.000 description 7
- 239000000463 material Substances 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 238000007796 conventional method Methods 0.000 description 4
- 238000007711 solidification Methods 0.000 description 4
- 230000008023 solidification Effects 0.000 description 4
- 238000005336 cracking Methods 0.000 description 3
- 238000005520 cutting process Methods 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000010275 isothermal forging Methods 0.000 description 2
- 230000005499 meniscus Effects 0.000 description 2
- 238000001000 micrograph Methods 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000003672 processing method Methods 0.000 description 2
- 238000007712 rapid solidification Methods 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- KRQUFUKTQHISJB-YYADALCUSA-N 2-[(E)-N-[2-(4-chlorophenoxy)propoxy]-C-propylcarbonimidoyl]-3-hydroxy-5-(thian-3-yl)cyclohex-2-en-1-one Chemical compound CCC\C(=N/OCC(C)OC1=CC=C(Cl)C=C1)C1=C(O)CC(CC1=O)C1CCCSC1 KRQUFUKTQHISJB-YYADALCUSA-N 0.000 description 1
- 229910001069 Ti alloy Inorganic materials 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 229910000756 V alloy Inorganic materials 0.000 description 1
- 230000002730 additional effect Effects 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000015271 coagulation Effects 0.000 description 1
- 238000005345 coagulation Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000010924 continuous production Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000001192 hot extrusion Methods 0.000 description 1
- 238000000886 hydrostatic extrusion Methods 0.000 description 1
- 238000003780 insertion Methods 0.000 description 1
- 230000037431 insertion Effects 0.000 description 1
- 239000003562 lightweight material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 239000011819 refractory material Substances 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 229910000601 superalloy Inorganic materials 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 238000012546 transfer Methods 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)
本発明は均質なTiAl金属間化合物の連続した薄板お
よびその製造方法に関する。DETAILED DESCRIPTION OF THE INVENTION Field of the Invention The present invention relates to a continuous thin plate of homogeneous TiAl intermetallic compound and a method for producing the same.
TiAl金属間化合物は、一般にTiAl合金と呼ばれ
ており、金属材料としては極めて高い高温強度を持ち、
しかも耐食性が高く、軽量の材料である。TiAl intermetallic compound is generally called TiAl alloy, and has extremely high high temperature strength as a metal material.
Moreover, it is a lightweight material with high corrosion resistance.
Metallurgical Transactio
n、 Vol、 6八(1975)。Metallurgical Transaction
n, Vol. 68 (1975).
p、1991には、800°Cで40kg/m−の高温
強度が得られたことが報告されている。そこでこれらの
特性を利用して、TiAl合金は、ガス・タービン軸晶
、自動車用エンジンのバルブやピストンへの適用、高温
用ディスクや軸受は軸晶、航空機用のフレーム、超高速
旅客機の機体外板等への適用が好適と考えられる。p, 1991, it is reported that a high temperature strength of 40 kg/m- was obtained at 800°C. Taking advantage of these properties, TiAl alloys have been applied to gas turbine axial crystals, automobile engine valves and pistons, high-temperature disks and bearings as axial crystals, aircraft frames, and the exterior of ultra-high-speed passenger planes. It is considered suitable for application to plates, etc.
Ti/V合金は軽量で耐熱温度が高く、耐食性も高いた
め、高温で使用するタービンブレードなどに好適である
が、室温での延性が小さいため圧延・鍛造などによる底
形が困難である。Ti/V alloys are lightweight, have a high heat resistance, and have high corrosion resistance, so they are suitable for turbine blades used at high temperatures, but their low ductility at room temperature makes it difficult to form the bottom shape by rolling or forging.
また、・特にTiAl金属間化合物の薄板は、上記適用
例のうち超高速旅客機の機体外板部分への適用が考えら
れるが、この場合、厚さ約1mmで30craX30c
m程度の薄板の製造法確立が必須となる。In addition, in particular, the thin plate of TiAl intermetallic compound is considered to be applied to the outer panel of an ultra-high-speed passenger aircraft among the above application examples, but in this case, the thickness is about 1 mm and the thickness is 30cra x 30cm.
It is essential to establish a manufacturing method for thin plates with a thickness of about 1.5 m.
従来TiAl金属間化合物の薄板は、インゴットからの
切り出し、あるいは特開昭61−213361号公報に
示されているようにシース加工などによって製造されて
いるが、長尺の薄板は得られていない。Conventionally, thin plates of TiAl intermetallic compounds have been produced by cutting out ingots or by sheathing as shown in Japanese Patent Application Laid-Open No. 61-213361, but long thin plates have not been obtained.
また、インゴットからの切り出しでは歩留まりが悪く、
重力偏析などによって均一なa戊が得られにくいという
問題がある。従来の高温塑性加工には、シース加工、静
水圧押し出し、恒温鍛造、熱間押し出し等の方法がある
。しかし、これら加工法の適用は難しく、TiA!金属
間化合物の場合は高温強度が大きくて(1050’Cで
200MPa) 、歪速度依存性が高いという問題を克
服しなければならなかった。すなわち、前述した特開昭
61−213361号公報では、シース加工を用い、S
−816Go基超超合金シース材使って1100°C1
1,5m/minの圧延速度が必要であるとしている。In addition, the yield rate is poor when cutting from ingots,
There is a problem in that it is difficult to obtain a uniform aura due to gravitational segregation and the like. Conventional high-temperature plastic working methods include sheath processing, hydrostatic extrusion, isothermal forging, hot extrusion, and the like. However, it is difficult to apply these processing methods, and TiA! In the case of intermetallic compounds, it was necessary to overcome the problems of high high-temperature strength (200 MPa at 1050'C) and high strain rate dependence. That is, in the above-mentioned Japanese Patent Application Laid-Open No. 61-213361, sheath processing is used to
-1100°C1 using 816Go-based superalloy sheath material
It is said that a rolling speed of 1.5 m/min is required.
また、日本金属学会シンポジウム予稿、9月21日、(
1988)、 p、24では恒温鍛造において、950
〜1000°Cの温度で、10−2〜10−” 5ec
−’の歪速度が必要であるとしている。したがって、温
度制御が難しく、生産速度が遅いという問題があった。Also, Japan Institute of Metals Symposium Proceedings, September 21st, (
1988), p. 24, in isothermal forging, 950
10-2 to 10-” 5ec at a temperature of ~1000°C
-' strain rate is required. Therefore, there were problems in that temperature control was difficult and production speed was slow.
以上の観点から厚さ約1閣で30cmX 30 cm程
度の薄板は、前述の従来法によってインゴット等の鋳塊
から製造することは生産速度や設備的な面からも実質的
に不可能と考えられる。From the above point of view, it is considered virtually impossible to manufacture a thin plate with a thickness of about 30 cm x 30 cm from an ingot or other ingot using the conventional method described above, both from the production speed and equipment standpoint. .
さらに上記従来技術による薄板の製造方法では、得られ
る薄板の寸法が例えば、長さ20mm、幅10閣、厚さ
10閣程度と小さいうえに、工程が複雑で、多大の労力
や多くの設備を必要とするという問題があった。Furthermore, in the method for manufacturing a thin plate according to the above-mentioned conventional technology, the dimensions of the obtained thin plate are small, for example, about 20 mm in length, 10 mm in width, and 10 mm in thickness, and the process is complicated and requires a lot of labor and equipment. The problem was that it was necessary.
TiAl金属間化合物に急冷法を用いた従来の技術とし
ては、特開昭62−256902号公報に示されている
ように、単ロール法や双ロール法などの急速凝固プロセ
スを用いて溶融金属を10’°C/sec以上の冷却速
度で急冷凝固させて、フレーク状凝固物を得る方法があ
るが、連続した薄板を得たという報告はない。As a conventional technique using a rapid cooling method for TiAl intermetallic compounds, as shown in Japanese Patent Application Laid-Open No. 62-256902, molten metal is cooled using a rapid solidification process such as a single roll method or a twin roll method. There is a method of obtaining a flake-like solidified product by rapid solidification at a cooling rate of 10'°C/sec or higher, but there is no report of obtaining a continuous thin plate.
前記したように、従来技術では、Ti7V全7V化合物
の、厚さ約1mmで30cmX 30cm程度の薄板製
造は不可能であったが、本発明はそれを解決し、連続し
たTiAZ金属間化合物の薄板を提供すること、及び同
薄板の容易かつ効率的な製造方法を提供することを目的
とするものである。As mentioned above, with the conventional technology, it was impossible to manufacture a thin plate of Ti7V all 7V compound with a thickness of about 1 mm and a size of about 30 cm x 30 cm, but the present invention solves this problem and produces a continuous thin plate of TiAZ intermetallic compound. The object of the present invention is to provide an easy and efficient manufacturing method for the same thin plate.
双ロール法は厚さ数肋×幅数10cmの薄板を数m/s
ecの速度で連続、的に製造する方法として一般的に知
られており、前述した薄板の寸法の観点からTi/V金
属間化合物薄板製造の理想的プロセスとして考えられる
。また、従来技術と比較して、薄板の製造までの工程が
非常に簡単であり、省工程、省設備および労力の削減な
ど付随的な効果も考えられる。The twin roll method can process a thin plate several meters thick x several tens of centimeters wide at several m/s.
It is generally known as a method for continuous production at a speed of EC, and is considered to be an ideal process for producing Ti/V intermetallic compound thin plates from the viewpoint of the dimensions of the thin plates mentioned above. In addition, compared to conventional techniques, the process up to the production of thin plates is extremely simple, and additional effects such as process savings, equipment savings, and labor savings are also possible.
溶融金属から薄板を直接鋳造する他のプロセスとして、
双ベルト法、単ベルト法や単ロール法等の方法がある。Other processes that cast sheet metal directly from molten metal include
There are methods such as the twin belt method, single belt method, and single roll method.
しかしながら、ベルトを使用した方法では、得られる薄
板の厚さが数cmであり、最終製品の厚さに対して厚過
ぎるため、後工程において従来法で費やす労力と大差な
い。一方、単ロール法の場合、得られる薄板の厚さが数
100μmと薄く、シェル強度が弱いため連続した薄板
になりにくい、また、単ロール法の宿命ともいえる片側
冷却のため、不均一凝固になり易く、後述するように割
れが発生し易い。However, in the method using a belt, the thickness of the obtained thin plate is several centimeters, which is too thick compared to the thickness of the final product, so there is not much difference in the amount of labor required in the post-process with the conventional method. On the other hand, in the case of the single-roll method, the thickness of the thin plate obtained is as thin as several 100 μm, and the shell strength is weak, making it difficult to form a continuous thin plate.Also, the single-roll method has one-sided cooling, which can lead to uneven solidification. This tends to cause cracks to occur, as will be described later.
以上から双ロール法でのみ厚さ数mmの連続した薄板を
製造することが可能であるものと考えられる。From the above, it is considered that it is possible to manufacture a continuous thin plate with a thickness of several mm only by the twin roll method.
本発明の要旨は下記の通りである。The gist of the invention is as follows.
すなわち、本発明は、A435〜44wt%、残部Ti
および不可避不純物からなり、鋳造ままの凝固組織が薄
板の両表面から板厚中心部に向かう柱状晶のみか、ある
いは前記柱状晶と板厚中心付近に存在する等軸晶との混
合組織からなる板厚032〜3mmの連続したTiAj
金属間化合物薄板であって、その製造方法は、IV35
〜44wt%と残部Tiとを不活性ガス雰囲気中で加熱
・溶解し、該溶融金属をロール周速0.1〜10 m
/secで回転する一対の冷却ロール間に連続して供給
し、一定のロール支持力下で、102〜10’°(:/
secの冷却速度で凝固させることを特徴とする。That is, in the present invention, A435 to 44 wt%, the balance Ti
and unavoidable impurities, and the solidified structure as cast is either columnar crystals extending from both surfaces of the thin plate toward the center of the thickness, or a mixed structure of the columnar crystals and equiaxed crystals existing near the center of the plate thickness. Continuous TiAj with thickness 032~3mm
An intermetallic compound thin plate, the manufacturing method of which is IV35
44 wt% and the remaining Ti are heated and melted in an inert gas atmosphere, and the molten metal is rolled at a peripheral speed of 0.1 to 10 m.
It is continuously supplied between a pair of cooling rolls rotating at a speed of 102 to 10'° (:/
It is characterized by solidifying at a cooling rate of sec.
なお、双ロール法として、垂直型、傾斜型、異径型等の
鋳造形式が異なるものがあるが、本発明はいずれも適用
可能である。In addition, although there are different casting types such as vertical type, inclined type, and different diameter type as the twin roll method, the present invention is applicable to any of them.
以下に本発明を作用とともに詳細に説明する。 The present invention will be explained in detail below along with its operation.
Mの組成範囲を35〜44wt%に限定する理由は、こ
の範囲でのみTi/V金属間化合物及び少量の他相(例
えばTi3/V)との混合相からなり、マイクロビッカ
ース硬度350Hv程度の均質なTiA1が得られ易い
ためである。The reason why the composition range of M is limited to 35 to 44 wt% is that only in this range, it consists of a mixed phase of Ti/V intermetallic compound and a small amount of other phases (for example, Ti3/V), and is homogeneous with a micro Vickers hardness of about 350 Hv. This is because it is easy to obtain TiA1.
板厚を0.2〜31!III+に限定した理由は、0.
2 mmより薄い場合、薄板の強度や材料の変形能不足
によって、鋳造時およびその後の搬送時に薄板が破断し
易いためであり、連続した薄板を安定して得るためには
、板厚は0.2 mm以上の場合でも、より厚くする方
が好ましい。また、3Mより厚い場合には内部に空隙が
形式され易くなる。The board thickness is 0.2~31! The reason for limiting it to III+ is 0.
This is because if the thickness is less than 2 mm, the thin plate is likely to break during casting and subsequent transportation due to insufficient strength of the thin plate or deformability of the material.In order to stably obtain a continuous thin plate, the thickness of the plate must be 0.2 mm. Even if it is 2 mm or more, it is preferable to make it thicker. Furthermore, if the thickness is greater than 3M, voids are likely to form inside.
本発明によって得られた薄板の鋳造方向における断面組
織を第1図に示す。鋳造ままの凝固組織は薄板の両表面
から板厚中心部に向かう柱状晶のみか、あるいは前記柱
状晶と板厚中心付近に存在する等軸晶との混合組織から
構成される。FIG. 1 shows a cross-sectional structure in the casting direction of a thin plate obtained by the present invention. The as-cast solidified structure consists of only columnar crystals extending from both surfaces of the thin plate toward the center of the plate thickness, or a mixed structure of the columnar crystals and equiaxed crystals existing near the center of the plate thickness.
本発明によって得られた薄板のミクロ組織を第3図(A
)に示す。同図において、ミクロ組織はTi/ijと微
量のTi3AjおよびAl z T iの3相からなる
が、組成を変えることによってTiIV単相に近いもの
を得ることも可能である。また、比較のためにアークメ
ルト法によって得られたインゴットのミクロ組織を第3
図(B)に示す。なお、本発明によって得られた薄板の
平均結晶粒度は約100−である。The microstructure of the thin plate obtained by the present invention is shown in Figure 3 (A
). In the same figure, the microstructure consists of three phases: Ti/ij, trace amounts of Ti3Aj, and Al z Ti, but it is also possible to obtain one close to a TiIV single phase by changing the composition. In addition, for comparison, the microstructure of the ingot obtained by the arc melt method was
Shown in Figure (B). Note that the average crystal grain size of the thin plate obtained by the present invention is about 100-.
金属、1月号、 (1989)、 p、49では、急冷
法によるラメラ−組織の絶対量の増加、ラメラ−間隔の
減少によって、延性、強度などの機械的性質の向上が期
待されることが報告されている。したがって、双ロール
法は機械的性質の向上においても非常に有効な手段と考
えられる。Metals, January issue, (1989), p. 49, states that mechanical properties such as ductility and strength are expected to improve by increasing the absolute amount of lamellar structure and decreasing the lamellar spacing by rapid cooling. It has been reported. Therefore, the twin roll method is considered to be a very effective means for improving mechanical properties.
次に上記薄板の製造方法を説明する。Next, a method for manufacturing the above-mentioned thin plate will be explained.
AIとTiを組成が35〜44wt%Mになるように配
合して、不活性ガス雰囲気中で1500〜1600°C
に加熱・溶融し、1400〜1500”Cに降温・調整
する。その後、該溶融合金をロール周速0.1〜10m
/secで回転する一対の冷却ロール間に連続して供給
し、一定のロール支持力下で、102〜10″′’(:
/secで凝固させ、連続したTiAl金属間化合物薄
板を製造する。なお、ここでは、MとTi との金属間
化合物を形成する反応を促進させ、均一溶融状態を得る
ため、溶解温度は1500〜1600°Cに高めること
が好ましい。Blend AI and Ti to a composition of 35 to 44 wt%M and heat at 1500 to 1600°C in an inert gas atmosphere.
The molten alloy is heated and melted to a temperature of 1,400 to 1,500"C. Then, the molten alloy is rolled at a peripheral speed of 0.1 to 10 m.
102 to 10'''' (:
/sec to produce a continuous TiAl intermetallic thin plate. Here, in order to promote the reaction between M and Ti to form an intermetallic compound and obtain a uniform molten state, it is preferable to raise the melting temperature to 1500 to 1600°C.
板厚を0.2〜3 mmにするためには、ロール周速は
10〜0.1m/secが必要であり、そのときの鋳片
の冷却速度は10’〜102°(:/secに相当する
。In order to make the plate thickness 0.2 to 3 mm, the peripheral speed of the rolls needs to be 10 to 0.1 m/sec, and the cooling rate of the slab at that time is 10' to 102° (:/sec). Equivalent to.
したがって、ロール周速を0.1〜10 m / se
cに、並びに冷却速度を102〜105°C/secに
限定した。Therefore, the roll circumferential speed is 0.1 to 10 m/se
c and the cooling rate was limited to 102-105°C/sec.
TiAZ金属間化合物の最大の問題点は材料の延性が小
さいことである。これは双ロール法においても、凝固・
冷却中の鋳片の割れと関連する非常に重要な問題である
。延性の不足に伴う割れの主原因として幅方向の不均一
冷却・凝固が考えられる。したがって、鋳片の割れを軽
減するためには不均一凝固の原因となる注湯流の不均一
性やメニスカス表面における酸化膜等のロール/メタル
間の伝熱抵抗を極力除去する必要がある。注湯流の均一
化のためにはスリット状の注湯ノズルを用いることが望
ましい。また、メニスカス表面における酸化膜の生成を
抑制するためには、不活性ガス中での溶解・鋳造が必要
である。不活性ガスはAr、 Heなどのいずれでもよ
い。The biggest problem with the TiAZ intermetallic compound is that the material has low ductility. This also applies to coagulation and
This is a very important problem related to cracking of slabs during cooling. Uneven cooling and solidification in the width direction is thought to be the main cause of cracking due to lack of ductility. Therefore, in order to reduce the cracking of slabs, it is necessary to eliminate as much as possible the heat transfer resistance between the rolls and the metal, such as non-uniform pouring flow and oxide films on the meniscus surface, which cause non-uniform solidification. In order to make the pouring flow uniform, it is desirable to use a slit-shaped pouring nozzle. Furthermore, in order to suppress the formation of an oxide film on the meniscus surface, melting and casting in an inert gas is necessary. The inert gas may be Ar, He, or the like.
鋳片の割れを低減するための方法として、ロール最近接
点における鋳片中心部の未凝固部分をなるべく少なくし
た鋳造が望ましい。そのためには、CAMP−ISIJ
、 1 (1988)、 p、186に記されているよ
うに、ロールの支持にスプリンク等ヲ用い、ロールを固
定せず、一定の力で凝固シェルを押し付け、シェルの成
長とともにロールが自然に開くような構造にする必要が
ある。As a method for reducing cracks in the slab, it is desirable to perform casting in which the unsolidified portion of the center of the slab at the point closest to the rolls is minimized. To that end, CAMP-ISIJ
, 1 (1988), p. 186, the rolls are supported by sprinks, etc., and the rolls are not fixed, but the solidified shells are pressed with a constant force, and the rolls open naturally as the shells grow. It is necessary to have a structure like this.
凝固の不均一性を改善する以外の着眼点として、幅方向
への凝固シェル収縮時に拘束の原因となる鋳片端部の鋳
バリを皆無にする必要があるが、−殻内にサイド堰とロ
ール側面の間への溶融金属の差し込みを軽減するために
は、サイド堰の押し付は力をコントロールしなければな
らない。In addition to improving the non-uniformity of solidification, it is necessary to completely eliminate flash at the ends of the slab, which causes restraint when the solidified shell contracts in the width direction. In order to reduce the insertion of molten metal between the sides, the pressing force of the side weirs must be controlled.
第2図は、本発明の方法に使用する装置の概略を示すも
ので、1は金属間化合物TtjVを溶解・供給するため
のるつぼである。ロール間への供給を幅方向で均一にす
るため、溶融金属は耐火物製のタンデイツシュ2を通り
、回転する一対のロール3.3′間に供給される。4は
耐火物製のサイド堰であり、ロール間に溶融金属の湯溜
りを形成させるためのものである。5は不活性ガスによ
り保護雰囲気とする雰囲気制御容器である。6は製造さ
れた薄板である。7は容器5への不活性ガス導入機構、
8は排気機構である。FIG. 2 schematically shows the apparatus used in the method of the present invention, and 1 is a crucible for melting and supplying the intermetallic compound TtjV. In order to make the supply between the rolls uniform in the width direction, the molten metal passes through a refractory tundish 2 and is supplied between a pair of rotating rolls 3.3'. 4 is a side weir made of refractory material, which is used to form a pool of molten metal between the rolls. Reference numeral 5 denotes an atmosphere control container in which a protective atmosphere is created using an inert gas. 6 is the manufactured thin plate. 7 is an inert gas introduction mechanism into the container 5;
8 is an exhaust mechanism.
以下に本発明の実施例を示す。 Examples of the present invention are shown below.
アル電ニウム地金とスポンジチタンをA136wt%、
Ti64wt%の組成を得るように配合したちの8kg
をるつぼに投入し、これをAr雰囲気中で1600°C
まで加熱溶解して合金化した。次に、−旦1500°C
に温度を調整した後、該溶融合金を幅4IIlffl、
長さ95mmの開口部を持つタンデイツシュを通し、種
々のロール周速で回転する直径300 mm、幅100
mmの一対の調合金製のロールの間に供給し、一定のロ
ール支持力下で、102〜105°C/secの冷却速
度で凝固させて、第1表に示す厚さの連続薄板を得た。Aluminum base metal and sponge titanium are A136wt%,
8kg of Ti blended to obtain a composition of 64wt%
was placed in a crucible and heated at 1600°C in an Ar atmosphere.
It was heated and melted to form an alloy. Next, -1500°C
After adjusting the temperature to
A tundish with a diameter of 300 mm and a width of 100 mm rotates at various roll circumferential speeds through a tundish with an opening of 95 mm in length.
The material was fed between a pair of rolls made of a prepared alloy of mm, and solidified at a cooling rate of 102 to 105 °C/sec under a constant roll supporting force to obtain a continuous thin plate having the thickness shown in Table 1. Ta.
薄板の長さは約3mから10mであった。なお、ロール
間に形成される溶鋼の湯だまり部の高さは約80Mであ
った。The length of the slats was approximately 3 m to 10 m. The height of the pool of molten steel formed between the rolls was approximately 80M.
得られた薄板の鋳造方向における断面Mi織の一例を第
1図に示す。鋳造ままの凝固組織は薄板の両表面から板
厚中心部に向かう柱状晶のみか、あるいは前記柱状晶と
板厚中心付近に荏存する等軸晶との混合組織から構成さ
れる。An example of the cross-sectional Mi weave in the casting direction of the obtained thin plate is shown in FIG. The as-cast solidified structure consists of only columnar crystals extending from both surfaces of the thin plate toward the center of the plate thickness, or a mixed structure of the columnar crystals and equiaxed crystals existing near the center of the plate thickness.
上述した通り、双ロール法で得られた薄板のξクロ組織
第3図(A)は、TiA/と微量のTi3/VおよびA
iz T iの3相からなるが、組成を変えることによ
ってTiA/単相に近いものを得ることも可能である。As mentioned above, the ξ-chromatic structure of the thin plate obtained by the twin roll method in Figure 3 (A) shows TiA/ and trace amounts of Ti3/V and A.
Although it consists of three phases of iz Ti, it is also possible to obtain something close to TiA/single phase by changing the composition.
なお、このときの平均結晶粒度は双ロール法の場合約1
00nでアークメルト法と比較して115程度であった
。Note that the average grain size at this time is approximately 1 in the case of the twin roll method.
00n, it was about 115 compared to the arc melt method.
さらに、鋳造ままのマイクロビッカース硬度は薄板の測
定箇所に依らず35011vとインゴット法等で得られ
る値とほぼ同等であった。Furthermore, the micro-Vickers hardness of the as-cast material was 35011v, which was almost the same as the value obtained by the ingot method, etc., regardless of the measurement location of the thin plate.
第 1 表
〔発明の効果〕
本発明の製造方法を用いることにより、0.2〜3mm
厚さの連続した金属間化合物TiA!の薄板の製造が容
易になる。従って、通常の粉末冶金法、インゴットから
の切り出し、あるいは高温塑性加工法と異なり、工程の
複雑さに伴う労力、設備負担等を大幅に低減することが
できるなど、金属間化合物TiA1の薄板を均質にかつ
安価に量産する上で極めて効果が大きい。Table 1 [Effects of the invention] By using the manufacturing method of the present invention, 0.2 to 3 mm
Intermetallic compound TiA with continuous thickness! The production of thin plates becomes easier. Therefore, unlike the usual powder metallurgy method, cutting from an ingot, or high-temperature plastic processing method, it is possible to significantly reduce the labor and equipment burden associated with the complexity of the process, and to produce a homogeneous thin plate of intermetallic compound TiA1. It is extremely effective for mass production at low cost.
第1図は本発明によって得られた薄板の鋳造方向におけ
る断面金属組織を示す写真図、第2図は本発明を実施す
る装置の概略を示す説明図、第3図(A)、(B)は各
々双ロール法およびアークメルト法によって得られた薄
板の鋳造ままのミクロ組織を示す金属顕微鏡写真図であ
る。
l・・・るつぼ、2・・・タンデインシュ、3,3′・
・・ロール、4・・・サイド堰、5・・・雰囲気制御容
器、6・・・薄板、7・・・不活性ガス導入機構、8・
・・排気機構。
第棗図
509レエ
6咄;’JT?、l」
第2図
゛ずr3丁畢
!A)
’>00y*
手続輔正書(方式)
%式%
事件の表示
平成2年特許願第50307号
発明の名称
TiAl金属間化合物薄板およびその製造方法3、補正
をする者
事件との関係 特許出願人
東京都千代田区大手町二丁目6番3号
(665)新日本製鐵株式會社
代表者 山 本 全 作
4゜
代
埋入〒100
東京都千代田区丸の内二丁目4番1号
5、補正命令の日付
平成
年
月26
日
(発送日)
(1)明細書14頁10〜11行「ミクロ組織を示す金
属顕微鏡写真図である。」を「金属組織を示す顕微鏡写
真図である。」に補正する。Fig. 1 is a photographic diagram showing the cross-sectional metal structure in the casting direction of a thin plate obtained by the present invention, Fig. 2 is an explanatory diagram showing an outline of the apparatus for carrying out the present invention, and Figs. 3 (A) and (B). are metallurgical micrographs showing as-cast microstructures of thin plates obtained by the twin roll method and the arc melt method, respectively. l...crucible, 2...tandine, 3,3'.
... Roll, 4... Side weir, 5... Atmosphere control container, 6... Thin plate, 7... Inert gas introduction mechanism, 8...
・Exhaust mechanism. No. 509 Ree 6; 'JT? ,l'' Figure 2 ゛zur3choden! A) '>00y* Procedural support document (method) % formula % Display of the case 1990 Patent Application No. 50307 Name of the invention TiAl intermetallic compound thin plate and its manufacturing method 3, relationship with the amendment person case Patent Applicant 2-6-3 Otemachi, Chiyoda-ku, Tokyo (665) Nippon Steel Corporation Representative Zen Yamamoto 4゜Embedment 〒100 2-4-1-5 Marunouchi, Chiyoda-ku, Tokyo Amended Date of order: March 26, 2008 (Date of dispatch) (1) Changed "This is a metallographic micrograph showing a microstructure." to "This is a microscopic photo showing a metallographic structure." on page 14 of the specification, lines 10-11. to correct.
Claims (2)
純物からなり、鋳造ままの凝固組織が薄板の両表面から
板厚中心部に向かう柱状晶のみか、あるいは前記柱状晶
と板厚中心付近に存在する等軸晶との混合組織からなる
板厚0.2〜3mmの連続したTiAl金属間化合物薄
板。(1) Consisting of 35 to 44 wt% Al, balance Ti and unavoidable impurities, the solidified structure as cast is present only in columnar crystals extending from both surfaces of the thin plate toward the center of the plate thickness, or in the presence of the columnar crystals and near the center of the plate thickness. A continuous TiAl intermetallic compound thin plate having a thickness of 0.2 to 3 mm and consisting of a mixed structure with equiaxed crystals.
雰囲気中で加熱・溶解し、該溶融金属をロール周速0.
1〜10m/secで回転する一対の冷却ロール間に連
続して供給し、一定のロール支持力下で、10^2〜1
0^5℃/secの冷却速度で凝固させることを特徴と
する連続したTiAl金属間化合物薄板の製造方法。(2) 35 to 44 wt% Al and the remainder Ti are heated and melted in an inert gas atmosphere, and the molten metal is rolled at a peripheral speed of 0.
Continuously supplied between a pair of cooling rolls rotating at a speed of 1 to 10 m/sec, and under a constant roll supporting force, 10^2 to 1
A method for producing a continuous TiAl intermetallic compound thin plate, characterized by solidifying at a cooling rate of 0^5°C/sec.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP5030790A JP2958792B2 (en) | 1989-03-02 | 1990-03-01 | Method for producing TiA1 intermetallic compound sheet |
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP5064989 | 1989-03-02 | ||
JP1-50649 | 1989-03-02 | ||
JP5030790A JP2958792B2 (en) | 1989-03-02 | 1990-03-01 | Method for producing TiA1 intermetallic compound sheet |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH0344437A true JPH0344437A (en) | 1991-02-26 |
JP2958792B2 JP2958792B2 (en) | 1999-10-06 |
Family
ID=26390772
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP5030790A Expired - Fee Related JP2958792B2 (en) | 1989-03-02 | 1990-03-01 | Method for producing TiA1 intermetallic compound sheet |
Country Status (1)
Country | Link |
---|---|
JP (1) | JP2958792B2 (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0460234A4 (en) * | 1989-12-25 | 1995-04-19 | Nippon Steel Corp |
-
1990
- 1990-03-01 JP JP5030790A patent/JP2958792B2/en not_active Expired - Fee Related
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0460234A4 (en) * | 1989-12-25 | 1995-04-19 | Nippon Steel Corp |
Also Published As
Publication number | Publication date |
---|---|
JP2958792B2 (en) | 1999-10-06 |
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