JP2006312200A - Continuous casting powder and continuous casting method for al-containing ni-based alloy - Google Patents

Continuous casting powder and continuous casting method for al-containing ni-based alloy Download PDF

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JP2006312200A
JP2006312200A JP2006080510A JP2006080510A JP2006312200A JP 2006312200 A JP2006312200 A JP 2006312200A JP 2006080510 A JP2006080510 A JP 2006080510A JP 2006080510 A JP2006080510 A JP 2006080510A JP 2006312200 A JP2006312200 A JP 2006312200A
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JP4813225B2 (en
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Natsuki Shiga
夏樹 志賀
Teruaki Ishii
照彰 石井
Yuichi Kanbe
雄一 神戸
Kenji Mizuno
建次 水野
Hidekazu Todoroki
秀和 轟
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Nippon Yakin Kogyo Co Ltd
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Abstract

<P>PROBLEM TO BE SOLVED: To provide continuous casting powder for Al-containing Ni-based alloy to perform smooth continuous casting and a method for continuously casting a slab free from surface defects using the powder. <P>SOLUTION: The powder for continuously casting a molten steel containing more than 0.8 mass% to 3.5 mass% Al contains 20-30 mass% CaO, 30-40 mass% SiO<SB>2</SB>, 1-10 mass% Na<SB>2</SB>O, 0.5-5 mass% Al<SB>2</SB>O<SB>3</SB>, 10-15 mass% F, 0.1-8 mass% MgO, 0.5-5 mass% MnO, 4-10 mass% BaO, 4-10 mass% Li<SB>2</SB>O, 0.5-3 mass% C, and has a basicity controlled to 0.5<CaO/SiO<SB>2</SB><1.0, a viscosity of 0.4 to 2 poise at 1,300°C, a solidification temperature of 850°C to 1,100°C, and such a property that one side of the mold powder contacting with a mold is crystallized when the mold powder is poured between the mold and a solidified shell. The method for continuously casting the molten steel using the powder is also provided. <P>COPYRIGHT: (C)2007,JPO&INPIT

Description

本発明は、Al含有Ni基合金を連続鋳造するときに用いられる連続鋳造パウダーと、そのパウダーを用いて表面欠陥のないスラブを連続鋳造する方法に関するものである。   The present invention relates to a continuous casting powder used when continuously casting an Al-containing Ni-based alloy and a method for continuously casting a slab having no surface defects using the powder.

Ni基合金を連続鋳造する際に用いられる連続鋳造パウダーは、一般に、CaO、SiO、NaO、Al、F等の酸化物の他、骨材としてのカーボンを含有するものなどが用いられている。これらのパウダーの特徴は、酸化物が溶湯からの熱を受けて溶融し、鋳型と凝固シェルとの間に流入して、潤滑ならびに抜熱調整の役割を果たすように設計されている。また、骨材としてのカーボンは、溶融速度を調節するために添加されている。 Continuous casting powder used when continuously casting a Ni-based alloy generally contains carbon as an aggregate in addition to oxides such as CaO, SiO 2 , Na 2 O, Al 2 O 3 , F, etc. Is used. The characteristics of these powders are designed such that the oxide melts by receiving heat from the molten metal and flows between the mold and the solidified shell to play a role of lubrication and heat removal adjustment. Carbon as an aggregate is added to adjust the melting rate.

しかし、このような連続鋳造パウダーの場合、活性なAlを含有する合金溶湯の連続鋳造に用いると、そのAlが溶融したパウダー中に含まれるSiOと反応してAl(酸化物)を生成し、このAlがパウダー(スラグ)中に移される。そのため、パウダー組成が大きく変化するとともに、粘度や凝固温度等の物性が変化し、連続鋳造に適しないものになるという問題があった。その結果、鋳片(スラブ)には、デプレション、縦割れ、横割れ、ブリーディング等の表面欠陥を生じさせ、時にはブレークアウトまで招いて操業停止になるようなこともあった。 However, in the case of such continuous casting powder, when used for continuous casting of molten alloy containing active Al, the Al reacts with SiO 2 contained in the melted powder to react with Al 2 O 3 (oxide). This Al is transferred into the powder (slag). For this reason, there has been a problem that the powder composition changes greatly, and physical properties such as viscosity and solidification temperature change, which makes it unsuitable for continuous casting. As a result, surface defects such as depletion, vertical cracks, horizontal cracks, and bleeding were caused in the slab (slab), sometimes leading to a breakout and stopping the operation.

こうした問題に対処するため、従来、例えば特許文献1では、塩基度(CaO/SiO)を0.4以下とし、凝固温度を790〜835℃としたパウダーを用いて鋳造し、パウダーが組成変化を起こしても物性値が適正範囲に収まるようにした技術を提案している。しかしながら、この技術は、塩基度ならびに凝固温度を低めに誘導していたことから、パウダーの結晶性が失われてガラス化し、凝固シェルと銅鋳型間への溶融パウダーの流入量が大幅に増大して、不均一冷却を招くという問題があった。 In order to deal with such problems, conventionally, for example, in Patent Document 1, casting is performed using powder having a basicity (CaO / SiO 2 ) of 0.4 or less and a solidification temperature of 790 to 835 ° C., and the composition of the powder changes. We have proposed a technology that ensures that the physical property value is within the proper range even if the problem occurs. However, since this technology induced a lower basicity and solidification temperature, the crystallinity of the powder was lost and it became vitrified, and the inflow of molten powder between the solidification shell and the copper mold was greatly increased. As a result, there is a problem that non-uniform cooling is caused.

また、特許文献2では、塩基度(CaO/SiO)を1.8〜2.5と高く調整したパウダーを用いて鋳造する技術を提案している。このようにパウダーの塩基度を高くすると、溶鋼成分のTiやAlとパウダー中のSiOとの反応が抑制され、パウダーの物性変化を防止することができる。しかしながら、このパウダーは、塩基度が高いため、凝固温度が高くなり、その分だけ作業温度域における粘性が低下し、パウダーの適性な流入量を確保することができなくなり、ひいてはスティッキング等を引き起すおそれがあった。 Patent Document 2 proposes a technique of casting using powder whose basicity (CaO / SiO 2 ) is adjusted as high as 1.8 to 2.5. When the basicity of the powder is increased in this way, the reaction between the molten steel components Ti and Al and the SiO 2 in the powder is suppressed, and changes in the physical properties of the powder can be prevented. However, since this powder has a high basicity, the coagulation temperature is increased, the viscosity in the working temperature range is lowered by that amount, and it is not possible to secure an appropriate amount of powder flow, which causes sticking and the like. There was a fear.

また、特許文献3では、Ti:0.08〜3.0mass%、Al:0.02〜0.8mass%を含有する溶鋼に、塩基度0.7<CaO/SiO<1.8、過熱度5〜50℃とした場合に、パウダー中のTiOおよびAlのピックアップを、鋳造適性範囲内(合計で30mass%以下)に抑える技術を開示している。しかし、この技術は、溶鋼中のAl濃度が0.8mass%を超えると、Alの著しいピックアップにより、凝固温度および粘度の上昇を招き、その結果、パウダーが流入不足となって、スティッキング等を起すという問題があった。
特開平4−100600号公報 特開平7−116797号公報 特開2003−94150号公報
In Patent Document 3, Ti: 0.08~3.0mass%, Al : the molten steel containing 0.02~0.8Mass%, basicity 0.7 <CaO / SiO 2 <1.8 , overheating When the temperature is set to 5 to 50 ° C., a technique for suppressing the pickup of TiO 2 and Al 2 O 3 in the powder within the casting suitability range (30 mass% or less in total) is disclosed. However, when the Al concentration in the molten steel exceeds 0.8 mass%, this technique leads to an increase in solidification temperature and viscosity due to remarkable pickup of Al 2 O 3 , resulting in insufficient inflow of powder and sticking. There was a problem of starting up.
Japanese Patent Laid-Open No. 4-100600 JP-A-7-116797 JP 2003-94150 A

上述したように、従来技術についてはなお、凝固シェルと鋳型間への溶融パウダーの流入不足や過剰流入を招いて、ブレークアウト、スティッキング、あるいは不均一冷却を引き起し、依然として表面性状の悪いスラブになるという課題があった。   As mentioned above, the slabs with poor surface properties still have the conventional technology, causing insufficient or excessive inflow of molten powder between the solidified shell and the mold, causing breakout, sticking, or non-uniform cooling. There was a problem of becoming.

そこで本発明の目的は、従来技術が抱えている上述した問題がなく、円滑な連続鋳造を行うために有効なAl含有Ni基合金連続鋳造用パウダーを提供すること、およびそのパウダーを用いて表面欠陥のないスラブを連続鋳造する方法を提案することにある。   Accordingly, an object of the present invention is to provide an Al-containing Ni-based alloy continuous casting powder that is effective for performing smooth continuous casting without the above-mentioned problems of the prior art, and a surface using the powder. The object is to propose a method for continuously casting slabs without defects.

上記目的の実現に向けて研究するの中で、発明者らはまず、Al:0.8mass%を超えて3.5mass%以下を含むNi基合金を連続鋳造するときのパウダーとしてどのようなものが好ましいかについて、溶湯の凝固試験や熱分析を行った。その結果、1300℃における粘度が0.4〜2poise、凝固温度が850〜1100℃であり、さらに、特に限定はしないが、カスピダイン、CaO−SiO−Al系、LiO−SiO−Al系またはLiO−BaO−CaO−SiO−Al系の一種または二種以上含む結晶相を晶出する特性を有するパウダーであれば、Al含有Ni基合金を、表面欠陥を伴うことなく円滑に鋳造できることをつきとめた。 In the research for the realization of the above-mentioned object, the inventors first of all, what kind of powder is used when continuously casting a Ni-based alloy containing Al: more than 0.8 mass% and not more than 3.5 mass%. As to whether or not is preferable, a solidification test and thermal analysis of the molten metal were performed. As a result, the viscosity at 1300 ° C. is 0.4 to 2 poise, the solidification temperature is 850 to 1100 ° C., and there is no particular limitation, but caspidine, CaO—SiO 2 —Al 2 O 3 system, Li 2 O—SiO As long as the powder has a characteristic of crystallizing a crystal phase containing one or more of 2- Al 2 O 3 system or Li 2 O—BaO—CaO—SiO 2 —Al 2 O 3 system, an Al-containing Ni-based alloy Has been found to be able to be cast smoothly without surface defects.

次に、発明者らは、上記物性のパウダーは、どのような成分組成にすればよいかについて究明するために、粘度ならびに凝固温度の測定を行った。その結果、好適なパウダーと考えられるものは、CaO:20〜30mass%、SiO2:30〜40mass%、Na2O:1〜10mass%、Al:0.5〜5mass%、F:10〜15mass%、MgO:0.1〜8mass%、MnO:0.5〜5mass%、BaO:4〜10mass%、LiO:4〜10mass%を含む成分組成のものであることがわかった。 Next, the inventors measured the viscosity and coagulation temperature in order to investigate what component composition should be used for the powder having the above physical properties. As a result, what is considered to be preferred powder, CaO: 20~30mass%, SiO 2 : 30~40mass%, Na 2 O: 1~10mass%, Al 2 O 3: 0.5~5mass%, F: 10~15mass%, MgO: 0.1~8mass%, MnO: 0.5~5mass%, BaO: 4~10mass%, Li 2 O: was found to be that of the component composition containing 4~10Mass% .

さらに、発明者らは、Al含有Ni基合金を連続鋳造するための好適条件についても検討した。即ち、高周波誘導炉を用い、種々の成分組成の連続鋳造パウダーとAl:0.8mass%を超えて3.5mass%以下を含む合金溶湯との反応実験を行った。その結果、鋳造すべき溶湯の過熱度を50℃以下とし、かつそのパウダーは、塩基度を0.5<CaO/SiO<1.0を満足するように調整したものを用いると、パウダー中へのAlのピックアップを、鋳造適性範囲(30mass%以下)にすることができることをつきとめた。 Furthermore, the inventors also examined suitable conditions for continuously casting the Al-containing Ni-based alloy. That is, using a high-frequency induction furnace, a reaction experiment was performed between continuously cast powder having various component compositions and molten alloy containing Al: more than 0.8 mass% and not more than 3.5 mass%. As a result, when the superheat degree of the molten metal to be cast is 50 ° C. or less and the powder is adjusted so that the basicity satisfies 0.5 <CaO / SiO 2 <1.0, It has been found that the Al 2 O 3 pickup can be within the casting suitability range (30 mass% or less).

そして、このような知見の下に開発した連続鋳造パウダーを、最終的に実機にて使用し、種々の鋳造条件で試験鋳造を行った。その結果、上記成分組成のものにさらに、骨材としてのCを0.5〜3mass%含む連続鋳造パウダーを用い、溶湯過熱度を5〜50℃とし、引抜き速度を600〜900mm/分に制御して連続鋳造を行ったところ、パウダーの溶融速度ならびに溶融パウダーの流入量をともに適性範囲に制御できることが明らかになった。   And the continuous casting powder developed based on such knowledge was finally used in an actual machine, and test casting was performed under various casting conditions. As a result, a continuous casting powder containing 0.5 to 3 mass% of C as an aggregate is used in addition to the above component composition, the superheat degree of the molten metal is set to 5 to 50 ° C., and the drawing speed is controlled to 600 to 900 mm / min. As a result of continuous casting, it became clear that both the melting rate of the powder and the inflow amount of the molten powder could be controlled within a suitable range.

即ち、本発明は正に、上記の知見ならびに試験結果に基づき開発されたものであって、その要旨構成とするところは、Al:0.8mass%を超えて3.5mass%以下を含有する鋼の連続鋳造に用いるパウダーであって、このパウダーは、CaO:20〜30mass%、SiO:30〜40mass%、NaO:1〜10mass%、Al:0.5〜5mass%、F:10〜15mass%、MgO:0.1〜8mass%、MnO:0.5〜5mass%、BaO:4〜10mass%、Li2O:4〜10mass%、骨材としてC:0.5〜3mass%を含有する成分組成を有し、かつ、塩基度が0.5<CaO/SiO2<1.0、1300℃における粘度が0.4〜2poiseおよび凝固温度が850〜1100℃の特性を有し、さらに、鋳型と凝固シェルとの間に流入したときに鋳型に接する側に結晶相を晶出する性質を有することを特徴とするAl含有Ni基合金用連続鋳造パウダーである。 That is, the present invention was developed based on the above knowledge and test results, and the gist of the present invention is that steel containing Al: more than 0.8 mass% and not more than 3.5 mass%. a powder for use in the continuous casting, the powder, CaO: 20~30mass%, SiO 2 : 30~40mass%, Na 2 O: 1~10mass%, Al 2 O 3: 0.5~5mass%, F: 10~15mass%, MgO: 0.1~8mass %, MnO: 0.5~5mass%, BaO: 4~10mass%, Li 2 O: 4~10mass%, C as aggregate: 0.5 has a component composition containing 3 mass%, and a viscosity at basicity 0.5 <CaO / SiO 2 <1.0,1300 ℃ is 0.4~2poise and coagulation temperature 8 Continuous for Al-containing Ni-based alloys characterized by having a property of 0 to 1100 ° C. and further having a property of crystallizing a crystal phase on the side in contact with the mold when it flows between the mold and the solidified shell It is a casting powder.

なお、本発明の上記パウダーは、凝固時に、カスピダイン、CaO−SiO−Al系、LiO−SiO−Al系またはLIO−BaO−CaO−SiO−Al系の一種または二種以上含む結晶相を晶出するものであることが望ましく、その結晶相の厚みは、鋳型と凝固シェルとの間に流入したパウダー層全層の10〜80%に当たる厚さにすることが有効である。 In addition, the above-mentioned powder of the present invention is prepared by caspidine, CaO—SiO 2 —Al 2 O 3 system, Li 2 O—SiO 2 —Al 2 O 3 system or LI 2 O—BaO—CaO—SiO 2 —Al during solidification. It is desirable to crystallize a crystal phase containing one or more of 2 O 3 system, and the thickness of the crystal phase is 10 to 80% of the total powder layer flowing between the mold and the solidified shell. It is effective to make the thickness equivalent to.

また、本発明は、C≦1.0mass%、Si≦2.0mass%、Mn≦2.0mass%、Cu:20〜40mass%、Al:0.8mass%を超えて3.5mass%以下、Fe≦3.0mass%、残部がNiおよび不可避的不純物からなる合金溶湯、または、C≦1.0mass%、Si≦2.0mass%、Mn≦2.0mass%、Cr:20〜30mass%、Al:0.8〜3.5mass%、残部がNiおよび不可避的不純物からなる合金溶湯を、引抜き速度600〜900mm/分、溶湯過熱度:5〜50℃の条件下で、上記連続鋳造パウダーを用いて連続鋳造する方法を提案する。   Further, the present invention provides C ≦ 1.0 mass%, Si ≦ 2.0 mass%, Mn ≦ 2.0 mass%, Cu: 20 to 40 mass%, Al: more than 0.8 mass% and 3.5 mass% or less, Fe ≦ 3.0 mass%, the molten alloy consisting of Ni and inevitable impurities as the balance, or C ≦ 1.0 mass%, Si ≦ 2.0 mass%, Mn ≦ 2.0 mass%, Cr: 20-30 mass%, Al: Using the above continuous casting powder, a molten alloy consisting of 0.8 to 3.5 mass%, the balance being Ni and inevitable impurities, under conditions of a drawing speed of 600 to 900 mm / min and a molten metal superheat degree of 5 to 50 ° C. A continuous casting method is proposed.

なお、本発明方法において、連続鋳造時における、パウダー中へのAlのピックアップはパウダーの塩基度を0.5〜1.0にすることにより、30mass%以下に制御できる。 In the method of the present invention, the pick-up of Al 2 O 3 into the powder during continuous casting can be controlled to 30 mass% or less by setting the basicity of the powder to 0.5 to 1.0.

以上説明した構成に係る本発明のパウダーを使用すれば、デプレッションや縦割れ、横割れ、ブリーディング等の表面欠陥のないAl含有Ni基合金の連続鋳造スラブを得ることができる。また、本発明の連続鋳造方法によれば、パウダーの流入不良を招いてスティキングを招いたり、不均一冷却等を起すことなく、Ni基合金溶湯の連鋳が可能となる。その結果、本発明によれば、研削歩留りが向上し、生産性の向上と製造コストの低下を実現することができる。   If the powder of the present invention according to the configuration described above is used, a continuous casting slab of an Al-containing Ni-based alloy having no surface defects such as depletion, vertical cracking, lateral cracking, and bleeding can be obtained. Further, according to the continuous casting method of the present invention, Ni-base alloy molten metal can be continuously cast without causing powder inflow failure and causing sticking, non-uniform cooling, or the like. As a result, according to the present invention, the grinding yield can be improved, and the productivity can be improved and the manufacturing cost can be reduced.

本発明に係る連続鋳造パウダー(以下、単に「パウダー」ともいう)は、上述したように、実験を通じて開発されたものであり、基本的に、CaO−SiO−Al−BaO−LiO−MgO−MnO−NaO−F系から構成されているものである。そして、このパウダーはまた、1300℃における粘度が0.4〜2poise、凝固温度が850〜1100℃という特性を有し、かつ鋳型と凝固シェルとの間にあって、少なくともその一部が結晶化することが特徴となっている。以下、本発明のかかるパウダーの物性を上記のように限定した理由について説明する。 The continuous casting powder (hereinafter also simply referred to as “powder”) according to the present invention has been developed through experiments as described above, and is basically CaO—SiO 2 —Al 2 O 3 —BaO—Li. It is composed of a 2 O—MgO—MnO—Na 2 O—F system. And this powder has the characteristics that the viscosity at 1300 ° C. is 0.4 to 2 poise, the solidification temperature is 850 to 1100 ° C., and it is between the mold and the solidification shell, and at least a part thereof is crystallized. Is a feature. Hereinafter, the reason why the physical properties of the powder of the present invention are limited as described above will be described.

1300℃における粘度:0.4〜2poise
パウダーの粘度は、0.4poise未満になるとパウダーの流入過多となり、デプレッション、縦割れ、横割れ、ブリーディングを発生する。一方、その粘度が2poiseを超えると、逆に流入不足を招いてスティッキングを起し、いずれにしてもスラブ表面欠陥を発生することになり、スラブの研削量の増大を招いて歩留りが低下する。また、最悪のケースでは、ブレークアウトを引き起すこともある。このことから、溶融パウダーの1300℃における粘度は0.4〜2poiseとする。
Viscosity at 1300 ° C .: 0.4-2 poise
If the viscosity of the powder is less than 0.4 poise, the powder will flow in excessively, causing depletion, vertical cracking, horizontal cracking, and bleeding. On the other hand, if the viscosity exceeds 2 poise, the inflow is insufficient and sticking occurs. In any case, a slab surface defect is generated, and the yield of the slab is increased and the yield is lowered. In the worst case, it may cause a breakout. For this reason, the viscosity of the molten powder at 1300 ° C. is set to 0.4 to 2 poise.

凝固温度:850〜1100℃
パウダーの凝固温度が、850℃未満だとパウダーの流入過多の状態を招いてデプレッションや縦割れ、横割れ、ブリーディング等が発生し、一方、その温度が1100℃を超えると流入不足を招いてスティッキングを発生し、いずれにしてもスラブの表面欠陥を発生することになり、スラブ研削量が増加して歩留りが低下し、最悪の場合には、ブレークアウトを引き起こすことがある。このことから、本発明では、溶融パウダー凝固温度を850℃〜1100℃とする。
Solidification temperature: 850-1100 ° C
If the solidification temperature of the powder is lower than 850 ° C., it will cause excessive powder inflow, causing depletion, vertical cracking, horizontal cracking, bleeding, etc. On the other hand, if the temperature exceeds 1100 ° C., it will lead to insufficient inflow and sticking In any case, surface defects of the slab will be generated, the amount of slab grinding will increase, the yield will decrease, and in the worst case, breakout may occur. Therefore, in the present invention, the molten powder solidification temperature is set to 850 ° C to 1100 ° C.

結晶化挙動
酸化物あるいは酸フッ化物は一般に、凝固の際に結晶化する場合とガラス化する場合とがある。溶融したパウダーは、鋳造中に凝固シェルと鋳型内壁面との間に流入し、少なくともその一部は凝固し凝固層を形成する。このとき、パウダーがガラス化することなく結晶化すれば、パウダーフイルムが均一に形成されるようになり、スラブの均一冷却が実現される。従って、パウダーの特性として、凝固時に、少なくとも鋳型に接する側が所定の厚みで結晶化することが必要である。なお、パウダーが凝固する際に生成する該結晶相の組成は、カスピダイン、CaO−SiO−Al系、LiO−SiO−Al系またはLIO−BaO−CaO−Al系を一種または二種以上含むものであることが望ましい。
Crystallization Behavior In general, oxides or oxyfluorides are sometimes crystallized or vitrified during solidification. The molten powder flows between the solidified shell and the mold inner wall surface during casting, and at least a part of the powder is solidified to form a solidified layer. At this time, if the powder is crystallized without vitrification, the powder film is uniformly formed, and uniform cooling of the slab is realized. Therefore, as a characteristic of the powder, at the time of solidification, at least the side in contact with the mold needs to be crystallized with a predetermined thickness. The composition of the crystal phase generated when the powder solidifies is caspidine, CaO—SiO 2 —Al 2 O 3 system, Li 2 O—SiO 2 —Al 2 O 3 system, or LI 2 O—BaO—CaO. It is desirable that it contains one or more of —Al 2 O 3 system.

かかるパウダー層の凝固層のうち、鋳型に接する側に生成する結晶相は、該凝固層のトータル厚みの5〜90%に相当する厚みになるようにする。このような結晶相を有するパウダー凝固層にする理由は、結晶相の割合が5%未満だと、ほとんどガラス状態と等しいものになるため、溶融パウダーの流入過多を招いて不均一冷却になる。一方、結晶相の厚みの割合が90%を超えると、溶融パウダーのトータル厚みが薄くなり、凝固シェルの潤滑性が低下する。これらの場合、いずれも表面欠陥をもたらす危険性がきわめて高くなる。従って、本発明に係るパウダーとしては、鋳型内壁面と凝固シェルとの間に流入したパウダーが結晶化した部分の割合が、凝固層トータル厚みの5〜90%を占めるようなものにする。この結晶層の上記割合については、CaOやSiO、Al、NaO、Fの含有量を調整することにより達成することができる。なお、凝固層に対する結晶層の割合は、上記の効果をより一層向上させるには、10〜80%、好ましくは15〜75%程度とする。なお、鋳型と凝固シェルとの間に流入するパウダーの凝固層のトータル厚みは、特に限定がある訳ではないが、0.5〜3mm程度にすることが好ましい。 Of the solidified layer of the powder layer, the crystal phase generated on the side in contact with the mold is set to a thickness corresponding to 5 to 90% of the total thickness of the solidified layer. The reason for the powder solidified layer having such a crystal phase is that when the proportion of the crystal phase is less than 5%, it becomes almost the same as the glass state. On the other hand, when the ratio of the thickness of the crystal phase exceeds 90%, the total thickness of the molten powder becomes thin, and the lubricity of the solidified shell decreases. In these cases, the risk of causing surface defects is extremely high. Therefore, the powder according to the present invention is such that the proportion of the crystallized powder flowing between the inner wall surface of the mold and the solidified shell occupies 5 to 90% of the total thickness of the solidified layer. For the ratio of the crystal layer, CaO and SiO 2, Al 2 O 3, Na 2 O, can be achieved by adjusting the content of F. The ratio of the crystal layer to the solidified layer is about 10 to 80%, preferably about 15 to 75% in order to further improve the above effect. The total thickness of the solidified layer of the powder flowing between the mold and the solidified shell is not particularly limited, but is preferably about 0.5 to 3 mm.

次に、本発明に係るパウダーは、成分組成が、CaO:20〜30mass%、SiO:30〜40mass%、NaO:1〜10mass%、Al:0.5〜5mass%、F:10〜15mass%、MgO:0.1〜8mass%、MnO:0.5〜5mass%、BaO:4〜10mass%、LiO:4〜10mass%、C:0.5〜3mass%のものである。この成分組成のものを使う理由は、発明者らが多くの鋳造実験の中で知り得た実験的数値範囲であり、上記した物性値ならびに結晶化挙動を達成するために必要な成分組成だからである。 Then, powder of the present invention, the component composition, CaO: 20~30mass%, SiO 2 : 30~40mass%, Na 2 O: 1~10mass%, Al 2 O 3: 0.5~5mass%, F: 10~15mass%, MgO: 0.1~8mass %, MnO: 0.5~5mass%, BaO: 4~10mass%, Li 2 O: 4~10mass%, C: the 0.5~3Mass% Is. The reason for using this component composition is the experimental numerical range that the inventors have learned in many casting experiments, because it is the component composition necessary to achieve the physical property values and crystallization behavior described above. is there.

上記パウダーの成分組成のうち、MgOは、凝固温度を上げる作用がある。ただし、このMgO含有量が8mass%を超えると、凝固温度が1100℃を超えて高すぎてしまい、一方、0.1mass%未満では、その凝固温度が850℃未満と低すぎてしまう。好ましい、MgOの含有量は、0.2〜7mass%である。   Of the component composition of the powder, MgO has the effect of increasing the solidification temperature. However, if the MgO content exceeds 8 mass%, the solidification temperature exceeds 1100 ° C. and is too high, whereas if it is less than 0.1 mass%, the solidification temperature is too low and less than 850 ° C. The MgO content is preferably 0.2 to 7 mass%.

Cは、パウダーの溶融速度を制御するために添加するものであり、0.5mass%未満では溶融速度が速すぎて、過剰流入を招き、デプレッション、縦割れ、縦割れ、ブリーディング等の表面欠陥を発生してスラブの歩留りが低下する。一方、このCが3mass%を超えると、溶融速度が遅くなりすぎて流入が追いつかず、スティッキングやブリーディング等の表面欠陥を発生しやすくなり、スラブの歩留りが低下する。最悪のときはブレークアウトを引き起こす。   C is added to control the melting rate of the powder, and if it is less than 0.5 mass%, the melting rate is too high, resulting in excessive inflow, and surface defects such as depletion, vertical cracks, vertical cracks, and bleeding. Occurs and the yield of slabs decreases. On the other hand, if the C exceeds 3 mass%, the melting rate becomes too slow and the inflow cannot catch up, surface defects such as sticking and bleeding tend to occur, and the yield of the slab decreases. Causes a breakout in the worst case.

塩基度:0.5<CaO/SiO<1.0
パウダーの塩基度は0.5以下では、パウダー中のSiOの活量が高くなるため、下記(1)式のような反応によって、パウダー中のAlのピックアップが30mass%を超えて高く生じると共に、ガラス化しやすくなって粘度も高くなる傾向がある。このAlのピックアップ量が5mass%を超えると物性値が鋳造適性範囲を逸脱してしまう。その結果、スティッキング等の表面欠陥が発生し、スラブの研削量が増加して歩留りが低下する。
一方、パウダーの塩基度が1.0以上だと、粘度が低下し、デプレッション、縦割れ、横割れ、ブリーディング等の表面欠陥を発生し、上記物性値を得ることができなくなる。したがって、本発明ではパウダーの塩基度を0.5超え1.0未満とした。
3(SiO)+4Al=2(Al)+3Si…(1)
なお、( )内はパウダー中の成分であり、下線部は溶鋼中の成分を表す。
Basicity: 0.5 <CaO / SiO 2 <1.0
When the basicity of the powder is 0.5 or less, the activity of SiO 2 in the powder becomes high, so that the pickup of Al 2 O 3 in the powder exceeds 30 mass% by the reaction shown in the following formula (1). It tends to be highly vitrified and increase in viscosity. If the Al 2 O 3 pickup amount exceeds 5 mass%, the physical property value deviates from the casting suitability range. As a result, surface defects such as sticking occur, the amount of slab grinding increases, and the yield decreases.
On the other hand, when the basicity of the powder is 1.0 or more, the viscosity decreases, surface defects such as depletion, vertical cracking, horizontal cracking, and bleeding occur, and the above physical property values cannot be obtained. Therefore, in the present invention, the basicity of the powder is set to be more than 0.5 and less than 1.0.
3 (SiO 2 ) +4 Al = 2 (Al 2 O 3 ) +3 Si (1)
In addition, the inside of () is a component in powder, and an underline part represents the component in molten steel.

本発明はまた、上記パウダーを用いてAl含有Ni基合金を円滑に連続鋳造する方法を提案する。上記パウダーが効果的に用いられる対象合金としては、例えば、C≦1.0mass%、Si≦2.0mass%、Mn≦2.0mass%、Cu:20〜40mass%、Al:0.8〜3.5mass%、Fe≦3.0mass%、残部がNiおよび不可避的不純物からなる合金、または、C≦1.0mass%、Si≦2.0mass%、Mn≦2.0mass%、Cr:20〜30mass%、Al:0.8mass%を超えて3.5mass%以下、残部がNiおよび不可避的不純物からなる合金である。そして、これらの合金溶湯を連続鋳造する際は、スラブの引抜き速度を600〜900mm/分、溶湯過熱度を5〜50℃にする。それは上記のパウダーを用いて、このような条件で連続鋳造を行うと、パウダー中へのAlピックアップ量を30mass%以下に制御することが可能になり、その結果、表面欠陥がなくなるため、スラブ研削に伴う歩留りを90%以上確保すことができるようになる。以下に、各鋳造条件について、その限定理由を説明する。 The present invention also proposes a method for smoothly continuously casting an Al-containing Ni-based alloy using the powder. Examples of target alloys in which the powder is effectively used include C ≦ 1.0 mass%, Si ≦ 2.0 mass%, Mn ≦ 2.0 mass%, Cu: 20 to 40 mass%, and Al: 0.8 to 3 .5 mass%, Fe.ltoreq.3.0 mass%, the balance being Ni and an inevitable impurity alloy, or C.ltoreq.1.0 mass%, Si.ltoreq.2.0 mass%, Mn.ltoreq.2.0 mass%, Cr: 20 to 30 mass %, Al: more than 0.8 mass% and 3.5 mass% or less, with the balance being Ni and inevitable impurities. When continuously casting these molten alloys, the slab drawing speed is 600 to 900 mm / min, and the molten metal superheat is 5 to 50 ° C. It is possible to control the amount of Al 2 O 3 pickup in the powder to 30 mass% or less when the continuous casting is performed using the above powder under such conditions, and as a result, surface defects are eliminated. 90% or more of the yield associated with slab grinding can be secured. Below, the limitation reason is demonstrated about each casting condition.

合金成分については、Cは、材料の強度を保つために有用であるが、1.0mass%を超えると、脆くなってしまう。Si、Mnは、脱酸に有用な元素であり、それぞれ2.0mass%を超えると、割れ感受性が高くなってしまう。Cuは、耐食性向上のために添加するものであり、20mass%未満ではその効果が小さく、一方、40mass%を超えると室温での強度が低下してしまう。また、Crは、耐食性、耐熱性に有用な元素であり、その効果を得るために20〜30mass%の範囲内で添加する。Alは、耐熱性、対高温酸化性あるいは脱酸に有用な元素であり、0.8mass%を超えて3.5mass%以下の範囲内で添加する。その他、Mo、Vは耐食性や結晶粒径制御のために有用であり、必要に応じて添加する。なお、Niは、組織をオーステナイトに保つために有用である。   Regarding the alloy component, C is useful for maintaining the strength of the material, but when it exceeds 1.0 mass%, it becomes brittle. Si and Mn are elements useful for deoxidation, and if they exceed 2.0 mass%, the cracking sensitivity becomes high. Cu is added to improve the corrosion resistance. If the amount is less than 20 mass%, the effect is small. On the other hand, if it exceeds 40 mass%, the strength at room temperature decreases. Cr is an element useful for corrosion resistance and heat resistance, and is added within a range of 20 to 30 mass% in order to obtain the effect. Al is an element useful for heat resistance, resistance to high-temperature oxidation or deoxidation, and is added in the range of more than 0.8 mass% and not more than 3.5 mass%. In addition, Mo and V are useful for controlling corrosion resistance and crystal grain size, and are added as necessary. Ni is useful for keeping the structure austenite.

引抜き速度:600〜900mm/分
スラブの引抜き速度が600mm/分未満の場合は、スラブの鋳型内の滞在時間が長くなり、強冷却になるとともに、溶融パウダーの更新が遅くなり、デプレション、縦割れ、ブリーディング等の表面欠陥を発生しやすくなる。一方、引抜き速度が900mm/分を超えると、鋳型内でシェルの成長速度が追いつかず、ブリーディングやブレークアウトを引き起こす。そのため、引抜き速度は600〜900mm/分に限定する。
Drawing speed: 600 to 900 mm / min When the slab drawing speed is less than 600 mm / min, the residence time in the mold of the slab becomes longer, strong cooling is performed, and the renewal of the molten powder is slowed down. Surface defects such as cracks and bleeding are likely to occur. On the other hand, if the drawing speed exceeds 900 mm / min, the growth speed of the shell cannot catch up within the mold, causing bleeding and breakout. Therefore, the drawing speed is limited to 600 to 900 mm / min.

溶湯の過熱度:5〜50℃
溶湯の過熱度が5℃未満になると、溶湯が浸漬ノズル内で凝固してノズル閉塞を起し、操業停止を招くことがある。一方、過熱度が50℃を超えると、上記(1)式の反応が活発となり、Alピックアップが激しくなる。そのピックアップ量が30mass%を超えると物性値が鋳造の適性範囲を逸脱してしまう。その結果、デプレッション、縦割れ、ブリーディング等の表面欠陥が発生するようになる。そのため、溶湯の過熱度は5〜50℃に限定する。
Molten metal superheat: 5-50 ° C
When the degree of superheat of the molten metal is less than 5 ° C., the molten metal may solidify in the immersion nozzle to cause nozzle clogging, resulting in operation stoppage. On the other hand, if the degree of superheat exceeds 50 ° C., the reaction of the above formula (1) becomes active and the Al 2 O 3 pickup becomes intense. If the pick-up amount exceeds 30 mass%, the physical property value deviates from the suitable range of casting. As a result, surface defects such as depletion, vertical cracking, and bleeding are generated. Therefore, the degree of superheat of the molten metal is limited to 5 to 50 ° C.

パウダー中のAlピックアップ量:30mass%以下
上述したように、Alのピックアップ量は30mass%を超えると、物性値が本発明で目指す鋳造条件の範囲を逸脱するようになる。その結果、上述した各種の表面欠陥が発生して、スラブの研削量が増加して、歩留りが低下する。最悪の場合は、ブレークアウトを引き起す。このことから、パウダー中のAlのピックアップ量は、30mass%以下に制限する。好ましくは25mass%以下とする。なお、この連続鋳造の際、鋳造開始のごく初期に、溶融を助ける意味合いで、発熱パウダーを添加してもよい。このAlピックアップ量は、パウダーの塩基度を0.5〜1.0にすることにより、30mass%以下にできる。
Al 2 O 3 pickup amount in powder: 30 mass% or less As described above, when the Al 2 O 3 pickup amount exceeds 30 mass%, the physical property value deviates from the range of casting conditions aimed at by the present invention. As a result, the various surface defects described above occur, the amount of slab grinding increases, and the yield decreases. In the worst case, it will cause a breakout. For this reason, the amount of Al 2 O 3 pickup in the powder is limited to 30 mass% or less. Preferably it is 25 mass% or less. In this continuous casting, exothermic powder may be added at the very beginning of casting to help melting. The Al 2 O 3 pickup amount can be reduced to 30 mass% or less by setting the basicity of the powder to 0.5 to 1.0.

表1a、表2aに示した成分組成をもつNi基合金溶湯を溶製し、この表に示す連続鋳造パウダーを用いて連続鋳造機にて鋳造した。溶製は、電気炉で鉄屑、純ニッケル、フェロクロム、ステンレス屑等の原料を溶解し、AODあるいはVODのいずれか一方または両方を用いて精錬し、表1a、表2aに示す所定の成分とした。溶製した合金種は、NCF601、NW5500であり、前者を表1a、表1bに示し、後者を表2a、表2bに示した。   Ni-base alloy melts having the component compositions shown in Table 1a and Table 2a were melted and cast with a continuous casting machine using the continuous casting powder shown in this table. For melting, raw materials such as iron scrap, pure nickel, ferrochrome, and stainless steel scrap are melted in an electric furnace and refined using one or both of AOD and VOD, and the predetermined components shown in Table 1a and Table 2a are used. did. The melted alloy types are NCF601 and NW5500, the former are shown in Table 1a and Table 1b, and the latter are shown in Table 2a and Table 2b.

なお、合金溶湯成分、パウダー成分およびパウダー物性値は、以下の方法で評価した。
(1)合金溶湯成分:蛍光X線分析装置により定量分析した。表1aに示した成分の残部は、Feおよび不可避的不純物であり、その他に少量のSi、Mn、P等を含んでいる。
(2)パウダー成分:Cは燃焼法によりその他の成分は化学分析により定量した。表1a、表2aの中に示す各成分の合計が93.3〜99.3mass%となっているのは、これら成分以外にもFe23等の不可避的不純物を含むためである。
(3)粘度:回転円筒法により測定した。すなわち、鉄ルツボ中にパウダーを入れ、縦型抵抗炉内で溶解し、その後、鉄製ローターを挿入し、回転させることで、粘度を測定した。
(4)凝固温度:上記粘度測定の際、温度を降下していくと急激に粘度の値が立ち上がる点が求まるので、この変曲点を凝固温度とした。
The molten alloy component, powder component, and powder physical properties were evaluated by the following methods.
(1) Molten alloy component: Quantitative analysis was performed using a fluorescent X-ray analyzer. The balance of the components shown in Table 1a is Fe and unavoidable impurities, and also contains a small amount of Si, Mn, P and the like.
(2) Powder component: C was determined by a combustion method and other components were quantified by chemical analysis. The total of each component shown in Table 1a and Table 2a is 93.3 to 99.3 mass% because it contains unavoidable impurities such as Fe 2 O 3 in addition to these components.
(3) Viscosity: measured by the rotating cylinder method. That is, the powder was put in an iron crucible and melted in a vertical resistance furnace, and then the viscosity was measured by inserting and rotating an iron rotor.
(4) Solidification temperature: Since the point at which the viscosity value suddenly rises as the temperature is lowered during the viscosity measurement, this inflection point is taken as the solidification temperature.

表1aに示した溶湯を同表のパウダーを使って連続鋳造した際の、パウダー中のAl濃度変化と連続鋳造における欠陥の有無および得られたスラブに表面品質と研削後のスラブ歩留りの結果を表1b、表2bにまとめて示した。ここで、それぞれの評価は以下の方法で行った。
(1)パウダー中のAl濃度の変化:鋳型内からサンプルを採取し、化学分析により定量分析した。
(2)表面欠陥:鋳込み後のスラブを観察して特定した。
(3)スラブ研削歩留り:研削前後での重量変化より測定した。
When the molten metal shown in Table 1a is continuously cast using the powder of the same table, the Al 2 O 3 concentration change in the powder, the presence or absence of defects in continuous casting, the surface quality of the obtained slab and the slab yield after grinding The results are summarized in Tables 1b and 2b. Here, each evaluation was performed by the following method.
(1) Change in Al 2 O 3 concentration in powder: A sample was taken from the mold and quantitatively analyzed by chemical analysis.
(2) Surface defect: identified by observing the slab after casting.
(3) Slab grinding yield: Measured from weight change before and after grinding.

(A)NCF601合金
表1bに示すように、パウダー中のAl濃度の変化が30mass%以下であり、本発明例1〜5では、トラブルなく連続鋳造を行うことができた。また、得られたスラブも表面欠陥を全く発生することなく、スラブ研削歩留りも94.7%以上と良好な結果であった。これに対して、比較例No.6〜12は、パウダー成分、パウダー物性値および鋳造条件のいずれかが本発明の制限範囲を外れているため、連続鋳造において、ブレークアウト、ノズル詰まりによる操業停止等のトラブルが発生するか、あるいは完鋳しても、縦割れ、ブリーディング、デプレッション等の表面欠陥を引き起す結果となった。表面欠陥が発生したため、完鋳してもスラブ研削歩留りが90%未満となってしまい、製造コストの上昇を招いた。
(A) NCF601 alloy As shown in Table 1b, the change in the Al 2 O 3 concentration in the powder was 30 mass% or less, and in Examples 1 to 5 of the present invention, continuous casting could be performed without any trouble. Also, the obtained slab did not generate any surface defects, and the slab grinding yield was a good result of 94.7% or more. In contrast, Comparative Example No. 6-12, since any of powder components, powder physical properties and casting conditions are outside the limits of the present invention, troubles such as breakout and operation stoppage due to nozzle clogging occur in continuous casting, or Even when it was completely cast, surface defects such as vertical cracks, bleeding, and depletion were caused. Since surface defects occurred, the slab grinding yield was less than 90% even after complete casting, leading to an increase in manufacturing costs.

即ち、比較例No.6は、CaO、Al、Fの濃度が適性範囲から外れているため、塩基度が高く、凝固温度も高くなった。その結果、凝固シェルと鋳型との間への溶融パウダーの流入量が少なくなりデプレッション、ブリーディング等の表面欠陥が発生した。No.7は、CaO、Al、Fの濃度が範囲から外れ、粘度と凝固温度が高くなった。そのため、凝固シェルと鋳型との間への溶融パウダーの流入量が少なくなりブレークアウトしてしまった。No.8は、骨材としてのCが高すぎたため、溶融速度が遅くなりすぎて、流入が追いつかず、また、塩基度も低く凝固温度も低い。その結果、パウダーフイルムがガラス質になり、デプレッション、ブリーデイング等の表面欠陥が発生した。No.9、No.10は、パウダー成分が適性でなく、塩基度が高く、凝固温度も高いことから、表面欠陥が発生した。No.11は、パウダーは適性なものを用いたが、溶湯過熱度が低過ぎたため、ノズル詰まりを起こし鋳造停止となった。No.12は、パウダー組成は適性なものを用いたが、溶湯過熱度が高く、凝固シェルの成長が十分でなく、ブレークアウトしてしまった。 That is, Comparative Example No. In No. 6, since the concentrations of CaO, Al 2 O 3 , and F were outside the appropriate range, the basicity was high and the coagulation temperature was also high. As a result, the amount of molten powder flowing between the solidified shell and the mold decreased, and surface defects such as depletion and bleeding occurred. No. In No. 7, the concentrations of CaO, Al 2 O 3 and F were out of the range, and the viscosity and the solidification temperature were increased. As a result, the amount of molten powder flowing between the solidified shell and the mold was reduced, causing a breakout. No. In No. 8, since C as an aggregate was too high, the melting rate was too slow, the inflow could not catch up, and the basicity was low and the solidification temperature was low. As a result, the powder film became glassy, and surface defects such as depletion and bleeding were generated. No. 9, no. In No. 10, since the powder component was not suitable, the basicity was high, and the coagulation temperature was high, surface defects occurred. No. For No. 11, a suitable powder was used, but because the degree of superheated molten metal was too low, nozzle clogging occurred and casting stopped. No. No. 12 used an appropriate powder composition, but the degree of superheating of the melt was high, the growth of the solidified shell was not sufficient, and a breakout occurred.

(B)NW5500合金
表2bに示すように、パウダー中のAl濃度の変化が30mass%以下であり、本発明例13〜17では、パウダー中のAl濃度の変化が少なく、トラブルなく連続鋳造を行うことができた。また、得られたスラブも表面欠陥を全く発生することなく、スラブ研削歩留りも90%以上と良好な結果を示した。これに対して、比較例No.18〜24は、パウダー成分、パウダー物性値および鋳造条件のいずれかが本発明の制限範囲を外れているため、連続鋳造においてブレークアウト、ノズル詰まりによる操業停止等のトラブルが発生するか、あるいは完鋳しても、縦割れ、ブリーディング、デプレッション等の表面欠陥を引き起す結果となった。表面欠陥が発生したため、完鋳してもスラブ研削歩留りが90%未満となってしまい、製造コストの上昇を招いた。
(B) NW5500 alloy As shown in Table 2b, the change in the Al 2 O 3 concentration in the powder is 30 mass% or less, and in Examples 13 to 17 of the present invention, the change in the Al 2 O 3 concentration in the powder is small. Continuous casting was possible without any trouble. Further, the obtained slab did not generate any surface defects, and the slab grinding yield was 90% or more and showed a good result. In contrast, Comparative Example No. In Nos. 18 to 24, any of powder components, powder physical properties, and casting conditions is out of the limit range of the present invention. Therefore, troubles such as breakout and operation stoppage due to nozzle clogging occur in continuous casting, or completion. Casting resulted in surface defects such as vertical cracks, bleeding, and depression. Since surface defects occurred, the slab grinding yield was less than 90% even after complete casting, leading to an increase in manufacturing costs.

即ち、比較例No.18は、CaO、Al、Fの濃度が適性範囲から外れているため、塩基度が高く、凝固温度も高くなった。その結果、凝固シェルと鋳型との間への溶融パウダーの流入量が少なくなりブレークアウトしてしまった。No.19は、CaO、Al、Fの濃度が範囲から外れ、粘度と凝固温度が高く、Alのピックアップ量が30mass%を過ぎた。その結果、凝固シェルと鋳型との間への溶融パウダーの流入量が少なくなりブレークアウトしてしまった。No.20は、骨材としてのCが高すぎたため、溶融速度が遅くなりすぎて、流入が追いつかず、また、塩基度も低く凝固温度も低い。その結果、パウダーフイルムがガラス質になり、デプレッション、縦割れ、ブリーディング等の表面欠陥が発生した。No.21、No.22は、パウダー成分が適性でなく、塩基度が高く、凝固温度も高いことから、表面欠陥が発生した。No.23は、パウダーは適性なものを用いたが、溶湯過熱度が低過ぎたため、ノズル詰まりを起こし鋳造停止となった。No.24は、パウダー組成は適性なものを用いたが、溶湯過熱度が高く、凝固シェルの成長が十分でなく、ブレークアウトしてしまった。 That is, Comparative Example No. No. 18 had a high basicity and a high solidification temperature because the concentrations of CaO, Al 2 O 3 and F were out of the proper range. As a result, the amount of molten powder flowing between the solidified shell and the mold was reduced, causing a breakout. No. In No. 19, the concentrations of CaO, Al 2 O 3 and F were out of the range, the viscosity and the solidification temperature were high, and the pickup amount of Al 2 O 3 exceeded 30 mass%. As a result, the amount of molten powder flowing between the solidified shell and the mold was reduced, causing a breakout. No. In No. 20, since C as an aggregate was too high, the melting rate was too slow, the inflow could not catch up, and the basicity was low and the solidification temperature was low. As a result, the powder film became glassy, and surface defects such as depletion, vertical cracking, and bleeding occurred. No. 21, no. No. 22 had surface defects because the powder component was not suitable, the basicity was high, and the coagulation temperature was high. No. For No. 23, an appropriate powder was used, but since the degree of superheating of the melt was too low, nozzle clogging occurred and casting was stopped. No. For No. 24, an appropriate powder composition was used, but the degree of superheating of the molten metal was high, the growth of the solidified shell was not sufficient, and a breakout occurred.

Figure 2006312200
Figure 2006312200

Figure 2006312200
Figure 2006312200

Figure 2006312200
Figure 2006312200

Figure 2006312200
Figure 2006312200

本発明は、Ni基合金に関し、とくに、高耐食性を求められる水溶性、海洋中の分野、あるいは、耐熱性を求められる炉材の分野で好適に用いられるAl含有Ni基合金の製造に有用な技術である。この技術はまた、耐熱の分野で用いられるステンレス鋼の連続鋳造技術にも適用できる。   The present invention relates to a Ni-based alloy, and is particularly useful for the production of an Al-containing Ni-based alloy that is suitably used in the water-soluble and marine fields where high corrosion resistance is required or in the field of furnace materials where heat resistance is required. Technology. This technique can also be applied to the stainless steel continuous casting technique used in the field of heat resistance.

Claims (6)

Al:0.8mass%を超えて3.5mass%以下含有するNi基合金の連続鋳造に用いるパウダーであって、このパウダーは、CaO:20〜30mass%、SiO:30〜40mass%、NaO:1〜10mass%、Al:0.5〜5mass%、F:10〜15mass%、MgO:0.1〜8mass%、MnO:0.5〜5mass%、BaO:4〜10mass%、LiO:4〜10mass%、C:0.5〜3mass%を含有する成分組成を有し、かつ、塩基度が0.5<CaO/SiO<1.0、1300℃における粘度が0.4〜2poiseおよび凝固温度が850〜1100℃の特性を有し、さらに鋳型と凝固シェルとの間に流入した時に鋳型に接する側に結晶相を晶出する特性を有することを特徴するAl含有Ni基合金用連続鋳造パウダー。 Al: Beyond 0.8 mass% is used in the continuous casting of a Ni-based alloy containing less 3.5 mass% a powder, this powder, CaO: 20~30mass%, SiO 2 : 30~40mass%, Na 2 O: 1~10mass%, Al 2 O 3: 0.5~5mass%, F: 10~15mass%, MgO: 0.1~8mass%, MnO: 0.5~5mass%, BaO: 4~10mass% , Li 2 O: 4 to 10 mass%, C: 0.5 to 3 mass%, and the basicity is 0.5 <CaO / SiO 2 <1.0, and the viscosity at 1300 ° C. A characteristic of 0.4 to 2 poise and a solidification temperature of 850 to 1100 ° C., and further, a crystal phase is crystallized on the side in contact with the mold when flowing between the mold and the solidified shell. Continuous casting powder for Al-containing Ni base alloy, comprising. 上記結晶相は、パウダー層全層の10〜80%に当たるの厚さを有することを特徴とする請求項1に記載のAl含有Ni基合金用連続鋳造パウダー。 2. The continuous casting powder for an Al-containing Ni-based alloy according to claim 1, wherein the crystal phase has a thickness corresponding to 10 to 80% of the entire powder layer. C≦1.0mass%、Si≦2.0mass%、Mn≦2.0mass%、Cu:20〜40mass%、Al:0.8mass%を超えて3.5mass%以下、Fe≦3.0mass%、残部がNiおよび不可避的不純物からなる合金溶湯を連続鋳造するに当たり、請求項1に記載の連続鋳造パウダーを用いることを特徴とするAl含有Ni基合金の連続鋳造方法。 C ≦ 1.0 mass%, Si ≦ 2.0 mass%, Mn ≦ 2.0 mass%, Cu: 20 to 40 mass%, Al: more than 0.8 mass% and 3.5 mass% or less, Fe ≦ 3.0 mass%, A continuous casting method for an Al-containing Ni-based alloy, wherein the continuous casting powder according to claim 1 is used when continuously casting a molten alloy consisting of Ni and inevitable impurities. C≦1.0mass%、Si≦2.0mass%、Mn≦2.0mass%、Cr:20〜30mass%、Al:0.8mass%を超えて3.5mass%以下、残部がNiおよび不可避的不純物からなる合金溶湯を連続鋳造するに当たり、請求項1に記載の連続鋳造パウダーを用いることを特徴とするAl含有Ni基合金の連続鋳造方法。 C ≦ 1.0 mass%, Si ≦ 2.0 mass%, Mn ≦ 2.0 mass%, Cr: 20 to 30 mass%, Al: more than 0.8 mass% and 3.5 mass% or less, the balance being Ni and inevitable impurities A continuous casting method for an Al-containing Ni-based alloy, wherein the continuous casting powder according to claim 1 is used in continuously casting a molten alloy comprising: 連続鋳造に当たっては、合金溶湯の過熱度を5〜50℃とし、引抜き速度を600〜900mm/分とする条件で鋳造を行うことを特徴とする請求項3または4に記載のAl含有Ni基合金の連続鋳造方法。 5. The Al-containing Ni-based alloy according to claim 3, wherein the continuous casting is performed under conditions where the superheat degree of the molten alloy is 5 to 50 ° C. and the drawing speed is 600 to 900 mm / min. Continuous casting method. 鋳型と凝固シェルとの間に形成されるパウダー層は、全厚の10〜80%に相当する厚みの結晶相を鋳型側に、生成するように鋳造することを特徴とする請求項3または4に記載のAl含有Ni基合金の連続鋳造方法。 The powder layer formed between the mold and the solidified shell is cast so as to produce a crystal phase having a thickness corresponding to 10 to 80% of the total thickness on the mold side. The continuous casting method of the Al-containing Ni-based alloy described in 1.
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