JP3084850B2 - Ingot drawing type electroslag melting method - Google Patents
Ingot drawing type electroslag melting methodInfo
- Publication number
- JP3084850B2 JP3084850B2 JP03296670A JP29667091A JP3084850B2 JP 3084850 B2 JP3084850 B2 JP 3084850B2 JP 03296670 A JP03296670 A JP 03296670A JP 29667091 A JP29667091 A JP 29667091A JP 3084850 B2 JP3084850 B2 JP 3084850B2
- Authority
- JP
- Japan
- Prior art keywords
- ingot
- steel ingot
- steel
- slag
- drawing type
- 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.)
- Expired - Fee Related
Links
Description
【０００１】[0001]
【産業上の利用分野】本発明は、鋼塊引抜き型エレクト
ロスラグ溶解法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an ingot drawing type electroslag melting method.
【０００２】[0002]
【従来の技術】エレクトロスラグ溶解法（以下、ＥＳＲ
という。）は、溶融スラグの電気抵抗熱により消耗電極
を溶解し、水冷銅モールドの中で凝固させるもので、凝
固した鋼塊を下方に引き抜く鋼塊引抜き型ＥＳＲは、量
産鋼種に対して生産性が高いため、近年相ついで稼働す
るようになっている。2. Description of the Related Art Electroslag melting (hereinafter referred to as ESR)
That. ) Melts the consumable electrode by the electric resistance heat of the molten slag and solidifies it in a water-cooled copper mold. The steel ingot drawing type ESR, which pulls out the solidified steel ingot, has a high productivity for mass-produced steel types. Due to its high cost, it has been operating in recent years.
【０００３】[0003]
【発明が解決しようとする課題】ところが、鋼塊引抜き
型ＥＳＲによって得られた鋼塊は、鋼塊肌が悪く、湯流
れによる二重肌になったり、凹凸肌になったりするとい
う問題があり、その発生のメカニズムが判明していな
い。したがって、良好な鋼塊肌を有するものを常に得よ
うという要求は満たされていなかった。本発明は、従来
の技術における上記のような実情に鑑みてなされたもの
であって、その目的は、良好な鋼塊肌を有する鋼塊を得
ることが可能な鋼塊引抜き型エレクトロスラグ溶解法を
提供することにある。However, the steel ingot obtained by the steel ingot drawing type ESR has a problem that the steel ingot has a bad skin and has a double skin due to the flow of molten metal, or has an uneven skin. , The mechanism of its occurrence is unknown. Therefore, the demand for always obtaining a steel having good ingot surface has not been satisfied. The present invention has been made in view of the above-described circumstances in the related art, and has as its object to provide a steel ingot drawing type electroslag melting method capable of obtaining a steel ingot having a good steel ingot surface. Is to provide.
【０００４】[0004]
【課題を解決するための手段】本発明者は、検討の結
果、鋼塊肌の形成は、鋼塊の溶融点、即ち鋼塊が凝固し
始める温度とスラグの凝固点との差、および鋼塊の凝固
点、即ち凝固が完了する温度とスラグの凝固点との差に
関係があることを見出だし、本発明を完成するに至っ
た。即ち、本発明は、鋼塊引抜き型エレクトロスラグ溶
解法により造塊するに際して、消耗電極を構成する鋼塊
とスラグとを、（ａ）鋼塊の溶融点がスラグの凝固点よ
りも高く、かつ、（ｂ）鋼塊の凝固点がスラグの凝固点
よりも６５℃以上高くない、の２つの条件を満足するよ
うに選択して、造塊を行うことを特徴とする。As a result of investigation, the present inventor has found that the formation of the steel ingot surface depends on the melting point of the steel ingot, that is, the difference between the temperature at which the steel ingot solidifies and the slag solidification point, and the steel ingot. It has been found that there is a relationship between the solidification point of the slag, ie, the difference between the temperature at which solidification is completed and the solidification point of the slag, and the present invention has been completed. That is, in the present invention, when ingot is formed by the ingot drawing type electroslag melting method, (a) the melting point of the steel ingot is higher than the solidification point of the slag, and (B) The ingot is selected to satisfy the following two conditions: the solidification point of the steel ingot is not higher than the solidification point of the slag by 65 ° C. or more, and the ingot is formed.
【０００５】以下、本発明について詳細に説明する。図
１は、鋼塊肌と、鋼塊およびスラグの物性との関係を示
すもので、縦軸が鋼塊の溶融点とスラグの凝固点との差
を表わし、横軸が鋼塊の凝固点とスラグの凝固点との差
を表わす。図において、斜線の部分（Ｂ）および（Ｃ）
は、本発明の上記の条件、即ち、（ａ）鋼塊の溶融点が
スラグの凝固点よりも高いという要件、および（ｂ）鋼
塊の凝固点がスラグの凝固点よりも６５℃以上高くない
という条件の両者を満たす範囲であって、許容される範
囲の鋼塊肌が生じる領域である。特に（Ｂ）の領域で
は、極めて良好な鋼塊肌が生じる。他方、（Ａ）および
（Ｄ）の領域では、本発明の上記（ａ）および（ｂ）の
条件を満たさず、（Ａ）の領域では、鋼塊肌が二重肌に
なり、（Ｄ）の領域では、鋼塊肌に凹凸が著しく発生す
る。Hereinafter, the present invention will be described in detail. FIG. 1 shows the relationship between the steel ingot surface and the physical properties of the steel ingot and the slag. The vertical axis represents the difference between the melting point of the steel ingot and the solidification point of the slag, and the horizontal axis represents the solidification point of the steel ingot and the slag. Represents the difference from the freezing point. In the figure, hatched portions (B) and (C)
Are the above-mentioned conditions of the present invention, that is, (a) the requirement that the melting point of the steel ingot is higher than the solidification point of the slag, and (b) the condition that the solidification point of the steel ingot is not higher than the solidification point of the slag by 65 ° C. or more. Is an area where the steel ingot surface in an allowable range occurs. Particularly in the region (B), an extremely good ingot surface occurs. On the other hand, in the regions (A) and (D), the above conditions (a) and (b) of the present invention are not satisfied, and in the region (A), the steel ingot has a double skin, and (D) In the region of, unevenness is significantly generated on the steel ingot skin.
【０００６】本発明における鋼塊肌の形成のメカニズム
について考察する。先ず、上記図１の（Ａ）の領域で
は、鋼塊肌に二重肌が生じるが、そのメカニズムとして
は、メニスカス部分において銅モールド近傍に溶融スラ
グが流入する隙間が生じてその中に溶融スラグが入り込
み、鋼塊を引抜く際に、溶鋼がこの隙間に流入して二重
肌が発生するものと推測される。一方、（Ｄ）の領域で
は、銅モールドが半凝固状態の溶鋼と接触する面積が大
きくなり、鋼塊肌に凹凸が生じて凹凸肌になるものと考
えられる。これに対して、（Ｂ）の領域では、メニスカ
ス部分において銅モールド近傍に溶融スラグが流入する
隙間が生じなく、また、半凝固状態の溶鋼とも接触しな
い。したがって、良好な鋼塊肌が生じるものと考えられ
る。なお（Ｃ）の領域でも溶融スラグが流入する隙間が
生じないが、半凝固状態の溶鋼と接触する部分が少し生
じるため、多少の凹凸が生じるが、その程度は低く許容
の範囲内となる。The mechanism of the formation of the steel ingot skin in the present invention will be considered. First, in the region of FIG. 1A, a double skin is formed on the steel ingot, and the mechanism is as follows. In the meniscus portion, a gap where molten slag flows in the vicinity of the copper mold is generated, and the molten slag is formed therein. It is presumed that when steel enters and the steel ingot is pulled out, molten steel flows into this gap and double skin occurs. On the other hand, in the region (D), it is considered that the area where the copper mold comes into contact with the molten steel in the semi-solidified state becomes large, and irregularities are generated on the steel ingot surface, resulting in irregular surfaces. On the other hand, in the region (B), there is no gap where the molten slag flows in the vicinity of the copper mold in the meniscus portion, and there is no contact with the molten steel in a semi-solid state. Therefore, it is considered that a good steel ingot surface is generated. Although there is no gap in the region (C) into which the molten slag flows, there is a small portion in contact with the molten steel in a semi-solid state, so that some unevenness occurs, but the degree is low and within an allowable range.
【０００７】[0007]
【実施例】以下に、本発明を実施例で説明する。 実施例１ 鋼種として、ＮＡＫ（Ｃ：０．１１２％、Ｓｉ：０．０
３０％、Ｍｎ：１．５８％、Ｐ：０．０１２％、Ｓ：
０．００４％、Ｃｕ：０．９７％、Ｎｉ：３．２１％、
Ｃｒ：０．１０％、Ｍｏ：０．２８％、Ａｌ：１．００
％、Ｏ：０．０００６％、Ｎ：０．００８４％、Ｈ：
１．４％、残部Ｆｅよりなるもの）（溶融温度：１５０
０℃、凝固温度１４３０℃）を用い、スラグとして、Ｃ
ａＦ2 −Ａｌ2 Ｏ3 −ＣａＯの組成が２０％−４０％−
４０％（凝固温度：１４２５℃）のものを使用した。こ
の鋼種について、鋼塊引抜き型ＥＳＲ炉を用いて造塊を
行った。使用したＥＳＲ条件は、次の通りであった。銅
モールド径：５５０ｍｍ，電極径：３８０ｍｍ、スラグ
重量：９０ｋｇ、電流および電圧：１５．９ＫＡおよび
５０Ｖ、引抜き条件：６３０ｋｇ／ｈｒ。その結果、良
好な鋼塊肌を有する鋼塊が得られた。（図１中、１）EXAMPLES The present invention will be described below with reference to examples. Example 1 As a steel type, NAK (C: 0.112%, Si: 0.0
30%, Mn: 1.58%, P: 0.012%, S:
0.004%, Cu: 0.97%, Ni: 3.21%,
Cr: 0.10%, Mo: 0.28%, Al: 1.00
%, O: 0.0006%, N: 0.0084%, H:
1.4%, the balance being Fe) (melting temperature: 150)
0 ° C, solidification temperature 1430 ° C), and as slag, C
The composition of aF 2 -Al 2 O 3 -CaO is 20% -40%-
40% (coagulation temperature: 1425 ° C.) was used. For this steel type, ingot making was performed using an ingot drawing type ESR furnace. The ESR conditions used were as follows. Copper mold diameter: 550 mm, electrode diameter: 380 mm, slag weight: 90 kg, current and voltage: 15.9 KA and 50 V, extraction condition: 630 kg / hr. As a result, a steel ingot having a good steel ingot surface was obtained. (1 in FIG. 1)
【０００８】実施例２ 鋼種として、ＳＵＳ４４０Ｃ（Ｃ：１．００％、Ｓｉ：
０．５８％、Ｍｎ：０．４９％、Ｐ：０．０２０％、
Ｓ：０．０１２％、Ｃｕ：０．０１％、Ｎｉ：０．３０
％、Ｃｒ：１７．０４％、Ｍｏ：０．６０％、残部Ｆｅ
よりなるもの（溶融温度：１４１５℃、凝固温度１２６
０℃）を用い、スラグとして、ＣａＦ2−Ａｌ2 Ｏ3 −
ＣａＯの組成が、４０％−３０％−３０％（凝固温度：
１３２５℃）を使用し、実施例１と同様に処理した。そ
の結果、凹凸の発生は少なく、良好な鋼塊肌を有する鋼
塊が得られた（図１中、２）。Example 2 SUS440C (C: 1.00%, Si:
0.58%, Mn: 0.49%, P: 0.020%,
S: 0.012%, Cu: 0.01%, Ni: 0.30
%, Cr: 17.04%, Mo: 0.60%, balance Fe
(Melting temperature: 1415 ° C, solidification temperature 126)
0 ° C.) and CaF 2 —Al 2 O 3 —
When the composition of CaO is 40% -30% -30% (solidification temperature:
1325 ° C.) and treated as in Example 1. As a result, there was little occurrence of irregularities, and a steel ingot having a good steel ingot surface was obtained (2 in FIG. 1).
【０００９】比較例１ 鋼種として、実施例１と同様のものを用い、スラグとし
て、ＣａＦ2 −Ａｌ2 Ｏ3 −ＣａＯの組成が、４０％−
３０％−３０％（凝固温度：１３２５℃）のものを使用
した以外は、実施例１と同様に処理した。その結果、鋼
塊表面に湯流れが発生し、二重肌の鋼塊肌を有するもの
となった。（図１中、３）Comparative Example 1 The same steel type as in Example 1 was used, and the composition of CaF 2 —Al 2 O 3 —CaO was 40% -as slag.
The processing was carried out in the same manner as in Example 1 except that 30% -30% (solidification temperature: 1325 ° C) was used. As a result, molten metal flow was generated on the surface of the steel ingot, and the steel ingot had a double ingot surface. (3 in FIG. 1)
【００１０】比較例２ 鋼種として、ＳＫＨ５１（Ｃ：０．８５％、Ｓｉ：０．
３５％、Ｍｎ：０．２５％、Ｃｒ：４．１０％、Ｍｏ：
５．０５％、Ｗ：６．２０％、Ｖ：２．０６％、残部Ｆ
ｅよりなるもの）（溶融温度：１３９０℃、凝固温度１
２３０℃）を用い、スラグとして、ＣａＦ2 −Ａｌ2 Ｏ
3 −ＣａＯの組成が、２０％−４０％−４０％（凝固温
度：１４２５℃）を使用し、実施例１と同様に処理し
た。その結果、凹凸の発生は大であり、好ましくない鋼
塊肌を有する鋼塊が得られた（図１中、４）。Comparative Example 2 As a steel type, SKH51 (C: 0.85%, Si: 0.
35%, Mn: 0.25%, Cr: 4.10%, Mo:
5.05%, W: 6.20%, V: 2.06%, balance F
e) (melting temperature: 1390 ° C., solidification temperature 1)
230 ° C.) and CaF 2 —Al 2 O
The treatment was performed in the same manner as in Example 1 except that the composition of 3- CaO was 20% -40% -40% (solidification temperature: 1425 ° C.). As a result, the occurrence of irregularities was large, and a steel ingot having an undesirable steel ingot surface was obtained (4 in FIG. 1).
【００１１】[0011]
【発明の効果】本発明によれば、鋼塊引抜き型エレクト
ロスラグ溶解法により造塊するに際して、鋼種およびス
ラグを、上記の条件を満足するように選択することによ
り、常に良好な鋼塊肌の鋼塊を得ることができる。According to the present invention, when ingot is formed by the ingot drawing type electroslag melting method, the steel type and the slag are selected so as to satisfy the above conditions, so that a good ingot surface is always obtained. A steel ingot can be obtained.
【図１】図１は、鋼塊肌と、鋼塊およびスラグの物性と
の関係を示す図である。FIG. 1 is a diagram illustrating a relationship between a steel ingot surface and physical properties of an ingot and slag.
Ａ 二重肌の鋼塊肌が形成される領域 Ｂ 良好な鋼塊肌が形成される領域 Ｃ 許容される鋼塊肌が形成される領域 Ｄ 凹凸の大きな鋼塊肌が形成される領域 １ 本発明の実施例１ ２ 本発明の実施例２ ３ 比較例１ ４ 比較例２ A A region where a double-strength steel ingot skin is formed B A region where a good steel ingot skin is formed C A region where an acceptable steel ingot skin is formed D A region where a highly uneven steel ingot skin is formed Inventive Example 1 2 Inventive Example 2 3 Comparative Example 1 4 Comparative Example 2
───────────────────────────────────────────────────── フロントページの続き (58)調査した分野(Int.Cl.7，ＤＢ名) B22D 11/041 C22B 9/18 ＪＩＣＳＴファイル（ＪＯＩＳ）（エレ クトロスラグ溶解)──────────────────────────────────────────────────続 き Continued on the front page (58) Field surveyed (Int. Cl. 7 , DB name) B22D 11/041 C22B 9/18 JICST file (JOIS) (electroslag dissolution)
Claims (1)
より造塊するに際して、消耗電極を構成する鋼塊とスラ
グとを、（ａ）鋼塊の溶融点がスラグの凝固点よりも高
く、かつ、（ｂ）鋼塊の凝固点がスラグの凝固点よりも
６５℃以上高くない、の２つの条件を満足するように選
択して、造塊を行うことを特徴とするエレクトロスラグ
溶解法。When a steel ingot is formed by an ingot drawing type electroslag melting method, a steel ingot and a slag constituting a consumable electrode are separated by: (a) a melting point of the steel ingot higher than a solidification point of the slag; b) Ingot making, wherein the solidification point of the steel ingot is not higher than the solidification point of the slag by 65 ° C. or more, and the ingot is selected to satisfy the two conditions.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP03296670A JP3084850B2 (en) | 1991-10-17 | 1991-10-17 | Ingot drawing type electroslag melting method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP03296670A JP3084850B2 (en) | 1991-10-17 | 1991-10-17 | Ingot drawing type electroslag melting method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH05104207A JPH05104207A (en) | 1993-04-27 |
| JP3084850B2 true JP3084850B2 (en) | 2000-09-04 |
Family
ID=17836562
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP03296670A Expired - Fee Related JP3084850B2 (en) | 1991-10-17 | 1991-10-17 | Ingot drawing type electroslag melting method |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3084850B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102994769A (en) * | 2012-12-19 | 2013-03-27 | 洛阳双瑞特种装备有限公司 | Remelting process of Ni-Cr-Mo anti-corrosion alloy stripping electroslag containing Ti |
-
1991
- 1991-10-17 JP JP03296670A patent/JP3084850B2/en not_active Expired - Fee Related
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102994769A (en) * | 2012-12-19 | 2013-03-27 | 洛阳双瑞特种装备有限公司 | Remelting process of Ni-Cr-Mo anti-corrosion alloy stripping electroslag containing Ti |
| CN102994769B (en) * | 2012-12-19 | 2014-05-07 | 洛阳双瑞特种装备有限公司 | Remelting process of Ni-Cr-Mo anti-corrosion alloy stripping electroslag containing Ti |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH05104207A (en) | 1993-04-27 |
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