JPH01197049A - Method for continuously casting strip - Google Patents
Method for continuously casting stripInfo
- Publication number
- JPH01197049A JPH01197049A JP2302988A JP2302988A JPH01197049A JP H01197049 A JPH01197049 A JP H01197049A JP 2302988 A JP2302988 A JP 2302988A JP 2302988 A JP2302988 A JP 2302988A JP H01197049 A JPH01197049 A JP H01197049A
- Authority
- JP
- Japan
- Prior art keywords
- coating
- coating agent
- solidified shell
- area ratio
- metal
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 238000005266 casting Methods 0.000 title claims abstract description 16
- 238000000034 method Methods 0.000 title claims abstract description 11
- 239000011248 coating agent Substances 0.000 claims abstract description 43
- 238000000576 coating method Methods 0.000 claims abstract description 22
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 19
- 239000010959 steel Substances 0.000 claims abstract description 19
- 229910052751 metal Inorganic materials 0.000 claims description 41
- 239000002184 metal Substances 0.000 claims description 41
- 239000002245 particle Substances 0.000 claims description 14
- 238000009749 continuous casting Methods 0.000 claims description 13
- 239000000843 powder Substances 0.000 description 11
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 9
- 238000010586 diagram Methods 0.000 description 8
- 229910000954 Medium-carbon steel Inorganic materials 0.000 description 7
- 238000001816 cooling Methods 0.000 description 6
- 238000004519 manufacturing process Methods 0.000 description 6
- 238000007711 solidification Methods 0.000 description 5
- 230000008023 solidification Effects 0.000 description 5
- 239000000498 cooling water Substances 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 4
- 239000011247 coating layer Substances 0.000 description 3
- 238000010583 slow cooling Methods 0.000 description 3
- 230000008646 thermal stress Effects 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 2
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 2
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 2
- 239000011230 binding agent Substances 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 239000012141 concentrate Substances 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 239000004071 soot Substances 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910052581 Si3N4 Inorganic materials 0.000 description 1
- 229910026551 ZrC Inorganic materials 0.000 description 1
- OTCHGXYCWNXDOA-UHFFFAOYSA-N [C].[Zr] Chemical compound [C].[Zr] OTCHGXYCWNXDOA-UHFFFAOYSA-N 0.000 description 1
- HSFWRNGVRCDJHI-UHFFFAOYSA-N alpha-acetylene Natural products C#C HSFWRNGVRCDJHI-UHFFFAOYSA-N 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 238000010924 continuous production Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 125000002534 ethynyl group Chemical group [H]C#C* 0.000 description 1
- 230000008020 evaporation Effects 0.000 description 1
- 238000001704 evaporation Methods 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 230000005499 meniscus Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 229910010271 silicon carbide Inorganic materials 0.000 description 1
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical compound N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 description 1
- 238000005507 spraying Methods 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000010792 warming Methods 0.000 description 1
- ZVWKZXLXHLZXLS-UHFFFAOYSA-N zirconium nitride Chemical compound [Zr]#N ZVWKZXLXHLZXLS-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0637—Accessories therefor
- B22D11/0665—Accessories therefor for treating the casting surfaces, e.g. calibrating, cleaning, dressing, preheating
- B22D11/0668—Accessories therefor for treating the casting surfaces, e.g. calibrating, cleaning, dressing, preheating for dressing, coating or lubricating
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
この発明は、無端状金属ベルトを使用した薄鋳片の連続
鋳造方法に関する。DETAILED DESCRIPTION OF THE INVENTION (Industrial Application Field) The present invention relates to a continuous casting method for thin slabs using an endless metal belt.
（従来の技術およびその課題）
近年、鉄鋼産業においては、省資源、省エネルギーを目
指し、製鉄から成品製造に到るあらゆる製造部門におい
て、製造設備あるいは生産工程の省略または簡素化が図
られつつあり、鋼板製造においてもその例外ではない。(Conventional technology and its challenges) In recent years, in the steel industry, with the aim of conserving resources and energy, efforts have been made to omit or simplify manufacturing equipment or production processes in all manufacturing departments, from steelmaking to finished product manufacturing. Steel sheet manufacturing is no exception.
従来、鋼板は水冷銅鋳型内に溶鋼を連続的に供給し、冷
却・凝固して厚２００〜３００ｍｌ１１、幅１５００〜
２０００＋ｎ＋ａ程度のスラブを製造し、このスラブを
熱間圧延機および冷間圧延機により圧延し製造している
。しかし、前記熱間圧延工程における消費エネルギーが
極めて大きいところから、熱間圧延設備に代替し得る省
エネルギー型鋼板製造設備の実現が望まれていた。Conventionally, steel plates are produced by continuously supplying molten steel into a water-cooled copper mold, cooling and solidifying it to a thickness of 200 to 300 ml11 and a width of 1,500 to 1,500 ml.
A slab of approximately 2000+n+a is manufactured, and this slab is rolled using a hot rolling mill and a cold rolling mill. However, since the energy consumption in the hot rolling process is extremely large, it has been desired to realize an energy-saving steel sheet manufacturing facility that can replace the hot rolling facility.
このような状況下にあって、溶鋼から直接薄鋳片あるい
は薄板を製造する技術が数々提案されている。例えば、
本出願人が提案した特開昭６１−１８０６２３号公報に
開示した発明も一つである。この装置は第１図に示すよ
うに、駆動ローラ１によって循環される無端状ベルト２
を僅かに傾けて対向配置し、やはり無端状の２つのダム
ブロック３を前記両金属ベルトの両幅端部で挟持して、
上下一対の金属ベルトと左右一対のダムブロックとで包
囲された鋳造空間を形成するよう構成されている。Under these circumstances, a number of techniques have been proposed for directly producing thin cast slabs or thin plates from molten steel. for example,
The invention disclosed in Japanese Patent Laid-Open No. 180623/1983 proposed by the present applicant is one such invention. As shown in FIG. 1, this device consists of an endless belt 2 which is circulated by a driving roller 1.
are arranged facing each other with a slight inclination, and two dam blocks 3, which are also endless, are sandwiched between both width ends of both metal belts,
It is configured to form a casting space surrounded by a pair of upper and lower metal belts and a pair of left and right dam blocks.
そして、駆動ローラ１によって金属ベルト２を図中矢印
方向に循環させると金属ベルト２と共にダムブロック３
も同時に循環する。このような状態において、給湯機４
から溶［５を注入すると、溶鋼５は上下の金属ベルト２
の鋳造表面に凝固シェル６を形成し始める。両金属ベル
ト２の裏面には、多量の冷却水７が噴射されているから
、凝固シェル２は段々と成長し鋳片８が製造されて行く
のである。When the metal belt 2 is circulated in the direction of the arrow in the figure by the driving roller 1, the dam block 3 is rotated together with the metal belt 2.
also circulates at the same time. In such a state, water heater 4
When the molten steel 5 is injected from the
A solidified shell 6 begins to form on the casting surface. Since a large amount of cooling water 7 is injected onto the back surfaces of both metal belts 2, the solidified shell 2 gradually grows and the slab 8 is manufactured.
ところで、前述のような薄鋳片連続鋳造装置を使用し、
溶鋼中（Ｃ）が０．０９〜０．１６％の中炭素鋼の薄鋳
片を製造する場合、鋳片表面に縦割れが発生することが
多い。この縦割れが発生すると、後の圧延工程の前に疵
取りをせねばならず、手入れ作業と温度低下の為に連続
鋳造の優れた経済性は半減してしまう。By the way, using the thin slab continuous casting equipment as mentioned above,
When producing thin slabs of medium carbon steel containing 0.09 to 0.16% (C) in molten steel, vertical cracks often occur on the slab surface. When this longitudinal crack occurs, it must be removed before the subsequent rolling process, and the excellent economic efficiency of continuous casting is halved due to the cleaning work and temperature drop.
さて、前記縦割れ発生の原因であるが、次の２つのこと
が考えられる。すなわち
（１）中炭素鋼の凝固組織上の問題、
（２）鋳造装置の冷却上の問題、
である、以下、それぞれについて説明する。Now, the following two reasons can be considered for the occurrence of the above-mentioned vertical cracks. That is, (1) problems regarding solidification structure of medium carbon steel, and (2) problems regarding cooling of casting equipment. Each of these will be explained below.
（１）中炭素鋼の凝固組織上の問題
溶鋼中（Ｃ）が０．０９〜０．１６％の中炭素鋼の鋳造
鋳片に縦割れが発生し易いのは、この炭素量域の綱は包
晶組織であり、凝固に際し包晶凝固となってオーステナ
イトが粗大化し、また、凝固時の収縮量が大きいため平
均−厚さの凝固シェルが生成する。そして、凝固シェル
の薄い部分に熱応力が集中して縦割れの原因になると考
えられる。(1) Problems with the solidification structure of medium carbon steel The reason why longitudinal cracks are likely to occur in cast slabs of medium carbon steel where (C) in the molten steel is 0.09 to 0.16% is in this range of carbon content. is a peritectic structure, and austenite becomes coarse during solidification due to peritectic solidification, and since the amount of shrinkage during solidification is large, a solidified shell with an average thickness is generated. It is thought that thermal stress concentrates on the thin portion of the solidified shell, causing vertical cracks.
（２）鋳造装置の冷却上の問題
金属ベルトを使用する連続鋳造装置では、金属ベルトの
鋳造面は約１６００°Ｃの溶鋼に接し、その裏面には多
量の冷却水が噴射されているから、金属ベルトの厚さ方
向に著しい熱勾配を生じ金属ベルトは大きく変形する。(2) Problems with cooling casting equipment In continuous casting equipment that uses metal belts, the casting surface of the metal belt is in contact with molten steel at approximately 1600°C, and a large amount of cooling water is sprayed onto the back surface. A significant thermal gradient is generated in the thickness direction of the metal belt, and the metal belt is greatly deformed.
具体的に説明すると、金属ベルトの変形は、第２図（ａ
）に示すように金属ベルトの幅方向にも、同図（ｂ）の
ように金属ベルトの鋳込み方向にも変形する。このよう
に金属ベルトが変形すると鋳造面の冷却能に差が生ずる
ため、平均−厚さの凝固シェルが形成される。その理由
は、第３図（ａ）に示すように、金属ベルト２の裏面か
ら冷却水７が噴射され冷却されているため、鋳造空間に
溶鋼５が注入されると、金属ベルト、２の鋳造面に凝固
シェル６が形成される。そして、メニスカスから離れる
につれて、成長する凝固シェル６が金属ベルト２への抜
熱に対する抵抗となって、金属ベルト２の温度上昇が軽
減される上、金属ベルト２が冷却されているために、金
属ベルトの熱間変形が低下し、金属ベルト２が局所的に
凝固シェル６から離反するようになる。そうすると、第
３図（ロ）のように凝固シェル６の厚さの不均一度が益
々増長されるのである。To explain specifically, the deformation of the metal belt is shown in Figure 2 (a
), the metal belt is deformed in the width direction, and as shown in (b), the metal belt is deformed in the casting direction. This deformation of the metal belt causes a difference in the cooling capacity of the casting surface, resulting in the formation of a solidified shell of average thickness. The reason for this is that, as shown in FIG. 3(a), since the cooling water 7 is injected from the back side of the metal belt 2 to cool it down, when the molten steel 5 is injected into the casting space, the metal belt 2 is A solidified shell 6 is formed on the surface. As the distance from the meniscus increases, the solidified shell 6 that grows acts as a resistance to heat removal to the metal belt 2, reducing the temperature rise of the metal belt 2, and since the metal belt 2 is cooled, the metal The hot deformation of the belt is reduced, and the metal belt 2 becomes locally separated from the solidified shell 6. As a result, the non-uniformity of the thickness of the solidified shell 6 increases as shown in FIG. 3(b).
このように、金属ベルトの変形によっても平均−厚さの
凝固シェルが形成され、凝固シェルの薄い部分に熱応力
が集中して縦割れの原因となるのである。In this way, the deformation of the metal belt also forms a solidified shell with an average thickness, and thermal stress concentrates in the thin portion of the solidified shell, causing longitudinal cracks.
（課題を解決するための手段）
以上のことから、中炭素鋼の連続鋳造方法において鋳片
表面の縦割れを防止するには、いかにして均一厚さの凝
固シェルを形成させるかが問題点解決の最も重要な手段
であり、そのためには局所的な急冷を避は全体を緩冷却
することが必要である、とのｖ２＊に立って鋭意研究を
進めた結果、本発明をするに到ったのである。(Means for solving the problem) From the above, the problem is how to form a solidified shell with a uniform thickness in order to prevent vertical cracks on the slab surface in the continuous casting method for medium carbon steel. This is the most important means of solving the problem, and as a result of intensive research based on the idea that it is necessary to cool the whole body slowly while avoiding localized rapid cooling, we have arrived at the present invention. That's what happened.
すなわち、本発明は「駆動ローラーにより循環される無
端状金属ベルトを所定の間隔をなすように対向配置し、
これら両金属ベルトの両幅端部近傍で両ベルトに挟持さ
れ、金属ベルトと共に循環するダムブロックを備え、前
記両金属ベルトとダムブロックで包囲される鋳造空間に
溶鋼を供給して薄鋳片を連続的に製造する連続鋳造方法
において、金属ベルト表面に粒径が５００ ｐ ｍ以下
の塗布剤をコーティングし、かつ前記塗布剤のコーティ
ング面積率を８０％以上とすることを特徴とする薄鋳片
の連続鋳造方法」にある。That is, the present invention proposes ``endless metal belts that are circulated by a drive roller to be disposed facing each other at a predetermined interval,
A dam block is provided near both width ends of these metal belts and circulates together with the metal belts, and molten steel is supplied to a casting space surrounded by the metal belts and the dam block to form a thin slab. A thin slab characterized in that the surface of the metal belt is coated with a coating agent having a particle size of 500 pm or less, and the coating area ratio of the coating agent is 80% or more, in a continuous casting method for continuous production. Continuous casting method”.
上記のように、本発明の要旨は、金属ベルトの表面に特
定粒径の塗布剤を、かつ特定の面積率でコーティングし
、そのコーティング層によって緩冷却を行い、均一厚さ
の凝固シェルを形成させるものである。そして、凝固シ
ェルの厚さが均一であるため、凝固シェル内部に不均等
な熱応力が生じないから、鋳片表面の縦割れが発生しな
い。As mentioned above, the gist of the present invention is to coat the surface of a metal belt with a coating agent having a specific particle size and a specific area ratio, and to perform slow cooling using the coating layer to form a solidified shell with a uniform thickness. It is something that makes you Furthermore, since the thickness of the solidified shell is uniform, uneven thermal stress does not occur inside the solidified shell, so vertical cracks do not occur on the surface of the slab.
（作用）
第４図は薄鋳片連続鋳造装置の上下金属ベルトのリター
ン側鋳造面に塗布剤のコーティング装置９−ｔ−設けた
場合を示している。(Function) FIG. 4 shows a case where a coating agent 9-t- is provided on the return side casting surfaces of the upper and lower metal belts of the thin slab continuous casting apparatus.
塗布剤としては、耐熱性を有し、溶鋼との濡れ性の良く
ないものであれば何でも良いが、酸化物（例えば、アル
ミナ粉、ジルコニア粉、シリカ粉）、炭化物（例えば、
炭化ジルコニウム、炭化珪素）、窒化物（例えば、窒化
ジルコニウム、窒化珪素）粉状炭素物質（例えば、煤）
等がある。Any coating agent may be used as long as it has heat resistance and does not have good wettability with molten steel, but oxides (e.g. alumina powder, zirconia powder, silica powder), carbides (e.g.
zirconium carbide, silicon carbide), nitrides (e.g. zirconium nitride, silicon nitride) powdered carbon substances (e.g. soot)
etc.
例えば、煤をコーティングする場合には、アセチレンガ
スをコーティング装置９から吹き出すと同時に不完全燃
焼させてコーティング層を形成させるのである。また、
アルミナ粉を使用する場合には、アルミナ粉をアルコー
ルをバインダーとしてコーティング装置９からスプレー
すれば、コーティング層を形成できる。For example, when coating soot, acetylene gas is blown out from the coating device 9 and at the same time is incompletely combusted to form a coating layer. Also,
When using alumina powder, a coating layer can be formed by spraying the alumina powder with alcohol as a binder from the coating device 9.
次に、本発明の塗布剤の粒径および塗布剤のコーティン
グ面積率の限定理由について説明する。Next, the reason for limiting the particle size of the coating agent of the present invention and the coating area ratio of the coating agent will be explained.
第５図はアルミナ粉の粒径を変化させ、凝固シェル厚さ
の不均一度を調査したものである。この図から粒径が５
００μｍを越えると急速に不均一度が増大していること
が分かる。５００μｍ以下であれば、第６図に示すよう
に、アルミナ粉１８間に大気の巻き込みやバインダーの
アルコールの蒸発により生じた微細な気泡２ａが存在し
、この気泡２ａは溶鋼５の表面張力によっても破壊され
ずに存在するため、アルミナ粉１ａとこの気泡２ａとに
より断熱による緩冷却効果が生じ、均一厚さの凝固シェ
ルが形成されると考えられる。FIG. 5 shows an investigation of the non-uniformity of the solidified shell thickness by changing the particle size of the alumina powder. From this figure, the particle size is 5
It can be seen that the degree of non-uniformity increases rapidly beyond 00 μm. If the diameter is less than 500 μm, as shown in FIG. 6, there are fine bubbles 2a between the alumina powders 18 caused by the entrainment of air or evaporation of alcohol in the binder, and these bubbles 2a are also caused by the surface tension of the molten steel 5. Since the alumina powder 1a and the bubbles 2a exist without being destroyed, it is thought that a slow cooling effect due to heat insulation is produced, and a solidified shell with a uniform thickness is formed.
しかし、アルミナ粉の粒径が５００μｍを越えると、溶
鋼の表面張力が破れて気泡が存在しなくなって緩冷却効
果が無くなり、不均一度さの凝固シェルが形成されると
考えられる。このことから、塗布剤の粒径は５００μｍ
以下と限定した。However, when the particle size of the alumina powder exceeds 500 μm, the surface tension of the molten steel is broken and no air bubbles are present, resulting in the loss of the slow cooling effect and the formation of a non-uniform solidified shell. From this, the particle size of the coating agent is 500 μm.
Limited to the following.
なお、凝固シェル厚さの不均一度とは、凝固シェル厚さ
の変動量を示す標準偏差で定められるもので、この値が
大きいほど、凝固シェル厚さの不均一度が大きいことに
なる。ここでは、不均一度Ｙは次の式に依った。The degree of non-uniformity in the thickness of the solidified shell is determined by the standard deviation indicating the amount of variation in the thickness of the solidified shell, and the larger this value is, the greater the degree of non-uniformity in the thickness of the solidified shell. Here, the degree of non-uniformity Y was determined by the following formula.
ここで、ｎは凝固シェル厚さの測定点数、Ｘ、は一定間
隔で測定した凝固シェル厚さ、７は凝固シェル厚さの平
均値、である。Here, n is the number of measurement points of the solidified shell thickness, X is the solidified shell thickness measured at regular intervals, and 7 is the average value of the solidified shell thickness.
次に、塗布剤のコーティング面積率について説明する。Next, the coating area ratio of the coating agent will be explained.
第７図はコーティング面積率と凝固シェル厚さ不均一度
との関係を示したものである。FIG. 7 shows the relationship between coating area ratio and solidified shell thickness non-uniformity.
この図からコーティング面積率が小さいと凝固シェル厚
さの不均一度は極めて大きいが、面積率が増加するにつ
れて凝固シェル厚さの不均一度は段々と低下して行き、
面積率が８０％以上になると大きく改善されることが分
かる。This figure shows that when the coating area ratio is small, the non-uniformity of the solidified shell thickness is extremely large, but as the area ratio increases, the non-uniformity of the solidified shell thickness gradually decreases.
It can be seen that when the area ratio becomes 80% or more, there is a great improvement.
この改善は、塗布剤の粒径のところで述べたと同様に、
金属ベルト表面の気泡の存在によるものと考えられる。This improvement is similar to that mentioned in the particle size of the coating agent.
This is thought to be due to the presence of air bubbles on the surface of the metal belt.
以上はアルミナ粉を使用した場合を述べたが、他の塗布
剤の場合でも同じ結果が得られた。なお、コーティング
面積率とは、第８図に示すように、金属ヘルド２の単位
面積（１０ｍｍＸ１０■）に塗布剤ｍが付着した面積を
、前記単位面積で除した値を百分率で表したものである
。The above description was based on the use of alumina powder, but the same results were obtained with other coating agents. As shown in Fig. 8, the coating area ratio is the value obtained by dividing the area to which the coating agent m has adhered to the unit area (10 mm x 10 cm) of the metal heald 2 by the unit area, expressed as a percentage. be.
（実施例）
第４回に示すｍ鋳片連続鋳造装置により重量％テＣ：０
．１１Ｘ、Ｓｉ ： ０．０３Ｘ 、Ｍｎ ： １．２
０χ、Ｐ：０．０１６χ、Ｓ：０．００８χ、残部Ｆｅ
の中炭素鋼の溶鋼を用い、鋳込速度３．０〜６．０ ｍ
／ｍｉｎで、鋳片寸法１０００ ｍｎ＋幅、５０ｍｍ厚
さの鋳片を製造した。その際、塗布剤にアルミナ粉を使
用し、その粒径と面積率を種々変えてコーティングした
。そして、それぞれの場合について、鋳片表面１ ｍ”
（１０００ｍｍ幅Ｘ １０００ｍｍ長さ）当たりに発
生した縦割れの総長さＬ （ｍｍ）を調査した。その結
果を第９図に示しており、同図中ＯはＬが１００ｍｍ以
下、ＣはＬが１００〜１０００ｍｍ、・はＬが１０００
ｍｍ以上を表している。(Example) Weight% TeC: 0 using the m slab continuous casting apparatus shown in the 4th
．． 11X, Si: 0.03X, Mn: 1.2
0χ, P: 0.016χ, S: 0.008χ, remainder Fe
Using molten medium carbon steel, casting speed 3.0 to 6.0 m
/min, a slab with a slab size of 1000 mm + width and a thickness of 50 mm was produced. At that time, alumina powder was used as a coating agent, and coatings were performed with various particle sizes and area ratios. And in each case, the slab surface 1 m”
The total length L (mm) of vertical cracks that occurred per (1000 mm width x 1000 mm length) was investigated. The results are shown in Figure 9, in which O indicates L of 100 mm or less, C indicates L of 100 to 1000 mm, and . indicates L of 1000 mm or less.
It represents mm or more.
第９図から、塗布剤の粒径が５００μｍ以下で、かつコ
ーティング面積率が８０以上である本発明の場合は、鋳
片表面の縦割れ総長さしは、すべて１００ｍ＋ｗ以下で
あり、鋳片の表面性状は良好であることが分かる。しか
し、塗布剤粒径、コーティング面積率の両方は勿論、何
れか一方が本発明範囲を外れた場合には、縦割れ総長さ
しが増大しており、鋳片表面が荒れていることが分かる
。From FIG. 9, in the case of the present invention in which the particle size of the coating agent is 500 μm or less and the coating area ratio is 80 or more, the total length of vertical cracks on the slab surface is all 100 m+w or less, and the It can be seen that the surface quality is good. However, if either of the coating agent particle size or the coating area ratio is out of the range of the present invention, the total length of vertical cracks increases and the surface of the slab becomes rough. .
（発明の効果）
以上説明したように、本発明によれば、熱間圧延設備を
使用しなくとも薄鋳片が製造でき、しかも中炭素鋼の場
合であっても、鋳片表面の縦割れの無い薄鋳片が製造で
きるので、鋳造後の手入れをすることな（次工程の圧延
を行うことができ、省資源、省工゛ネルギー化に寄与す
るところが極めて大きい。(Effects of the Invention) As explained above, according to the present invention, thin slabs can be manufactured without using hot rolling equipment, and even in the case of medium carbon steel, vertical cracks on the surface of the slab can be produced. Since it is possible to produce thin slabs without any blemishes, there is no need for maintenance after casting (rolling can be carried out in the next process), which greatly contributes to saving resources and saving energy.
第１図は金属ベルトを使用した薄鋳片連続鋳造装置の概
略図、
第２図（ａ）（ｂ）は金属ベルトの変形状態を示す模式
第３図（ａ）■）は下側金属ベルトに凝固シェルが生成
し、成長してゆく状態を示す図、
第４図はコーティング装置を備えた薄鋳片連続鋳造装置
の概略図、
第５図は塗布剤の粒径と凝固シェル厚さの不均一度との
関係を示す図、
第６図は塗布剤の暖冷作用を説明する図、第７図はコー
ティング面積率と凝固シェル厚さ不均一度との関係を示
す図、
第８図はコーティング面積率の定め方を説明する図、
第９図はコーティング面積率、塗布剤粒径および表面割
れ総長さとの関係を示す図、である。
１は駆動ローラー、２は金属ベルト、３はダムブロック
、４は給湯機、５は溶鋼、６は凝固シェル、７は冷却水
、８は鋳片、９はコーティング装置出願人 住友金属
工業株式会社
代理人 弁理士 穂上照忠（ほか１名）第１図
第２図
” （ｂ）
第３図
第４図
第６図
第５図 第７図
第８図
ｍ
第９図
コーティング凌し積率（％）
手続補正書
昭和６３年６月１０ぐ葛
特許庁長官 小 川 邦 夫 殿
１、事件の表示
昭和６３年特許願第２３０２９号
２、発明の名称
薄鋳片の連続鋳造方法
３、補正をする者
事件との関係 特許出願人
住所 大阪市東区北浜５丁目１５番地
氏名 （２１１）住友金属工業株式会社４、代理人
５、補正命令の日付 自発
７、補正の内容
（１）明細書第２頁６行目に「厚」とあるのを「厚さ」
と訂正する。
（２）明細書箱９頁６行目に
ｒｙ＝４−扁〒ｇｔｘ７−ｘｔ”〒」とあるのをする。
（３）明細書箱１０頁２０行目に「８０Ｊとあるのを「
８０％Ｊと訂正する。
（４）第５図および第７図を別紙のように訂正する。
以上Figure 1 is a schematic diagram of a continuous thin slab casting machine using a metal belt. Figure 2 (a) and (b) are schematic diagrams showing the deformed state of the metal belt. Figure 3 (a) ■) is the lower metal belt. Fig. 4 is a schematic diagram of a thin slab continuous casting machine equipped with a coating device, and Fig. 5 shows the relationship between the particle size of the coating agent and the thickness of the solidified shell. Figure 6 is a diagram showing the relationship between the degree of non-uniformity, Figure 6 is a diagram explaining the warming and cooling effect of the coating agent, Figure 7 is a diagram showing the relationship between the coating area ratio and the degree of non-uniformity of the solidified shell thickness, Figure 8 9 is a diagram illustrating how to determine the coating area ratio, and FIG. 9 is a diagram showing the relationship between the coating area ratio, coating agent particle size, and surface crack length. 1 is a drive roller, 2 is a metal belt, 3 is a dam block, 4 is a water heater, 5 is molten steel, 6 is a solidified shell, 7 is a cooling water, 8 is a slab, 9 is a coating device applicant Sumitomo Metal Industries, Ltd. Agent Patent attorney Terutada Hogami (and 1 other person) Figure 1 Figure 2 (b) Figure 3 Figure 4 Figure 6 Figure 5 Figure 7 Figure 8 m Figure 9 Coating coverage factor (%) Procedural amendment June 10, 1988 Kunio Ogawa, Director General of the Patent Office1, Indication of the case Patent Application No. 23029 of 19882, Name of the invention Continuous casting method for thin cast slabs 3, Amendment Relationship with the case of a person who does In the 6th line of page 2, "thickness" should be changed to "thickness".
I am corrected. (2) In the 6th line of page 9 of the specification box, read ry=4-b〒gtx7-xt''〒. (3) In the 20th line of page 10 of the statement box, change the word ``80J'' to
Correct it to 80%J. (4) Figures 5 and 7 should be corrected as shown in the attached sheet. that's all
Claims (1)
間隔をなすように対向配置し、これら両金属ベルトの両
幅端部近傍で両ベルトに挟持され、金属ベルトと共に循
環するダムブロックを備え、前記両金属ベルトとダムブ
ロックで包囲される鋳造空間に溶鋼を供給して薄鋳片を
連続的に製造する連続鋳造方法において、前記金属ベル
ト表面に粒径が５００μｍ以下の塗布剤をコーティング
し、かつ前記塗布剤のコーティング面積率を８０％以上
とすることを特徴とする薄鋳片の連続鋳造方法。Endless metal belts that are circulated by a drive roller are disposed facing each other at a predetermined interval, and a dam block that is sandwiched between both belts near both width ends of these metal belts and circulates together with the metal belts is provided. In a continuous casting method in which a thin slab is continuously produced by supplying molten steel to a casting space surrounded by both metal belts and a dam block, the surface of the metal belt is coated with a coating agent having a particle size of 500 μm or less, and A continuous casting method for thin slabs, characterized in that the coating area ratio of the coating agent is 80% or more.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2302988A JPH01197049A (en) | 1988-02-03 | 1988-02-03 | Method for continuously casting strip |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2302988A JPH01197049A (en) | 1988-02-03 | 1988-02-03 | Method for continuously casting strip |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH01197049A true JPH01197049A (en) | 1989-08-08 |
Family
ID=12099046
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2302988A Pending JPH01197049A (en) | 1988-02-03 | 1988-02-03 | Method for continuously casting strip |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH01197049A (en) |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59174254A (en) * | 1983-03-23 | 1984-10-02 | Sumitomo Metal Ind Ltd | Endless belt type continuous casting device |
| JPS60116756A (en) * | 1983-11-07 | 1985-06-24 | ヘイズレツト ストリツプ‐キヤステイング コーポレーシヨン | Matrix coating flexible casting belt, method and device therefor |
-
1988
- 1988-02-03 JP JP2302988A patent/JPH01197049A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59174254A (en) * | 1983-03-23 | 1984-10-02 | Sumitomo Metal Ind Ltd | Endless belt type continuous casting device |
| JPS60116756A (en) * | 1983-11-07 | 1985-06-24 | ヘイズレツト ストリツプ‐キヤステイング コーポレーシヨン | Matrix coating flexible casting belt, method and device therefor |
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