JPH0741382B2 - Casting method for ultra low carbon titanium killed steel - Google Patents
Casting method for ultra low carbon titanium killed steelInfo
- Publication number
- JPH0741382B2 JPH0741382B2 JP63272618A JP27261888A JPH0741382B2 JP H0741382 B2 JPH0741382 B2 JP H0741382B2 JP 63272618 A JP63272618 A JP 63272618A JP 27261888 A JP27261888 A JP 27261888A JP H0741382 B2 JPH0741382 B2 JP H0741382B2
- Authority
- JP
- Japan
- Prior art keywords
- gas
- low carbon
- killed steel
- carbon titanium
- nozzle
- 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 - Lifetime
Links
- 238000005266 casting Methods 0.000 title claims description 18
- 238000000034 method Methods 0.000 title claims description 15
- 229910000655 Killed steel Inorganic materials 0.000 title claims description 14
- CYKMNKXPYXUVPR-UHFFFAOYSA-N [C].[Ti] Chemical compound [C].[Ti] CYKMNKXPYXUVPR-UHFFFAOYSA-N 0.000 title claims description 14
- 239000011148 porous material Substances 0.000 claims description 18
- 239000011261 inert gas Substances 0.000 claims description 15
- 239000000463 material Substances 0.000 claims description 12
- 238000007599 discharging Methods 0.000 claims description 9
- 239000010936 titanium Substances 0.000 claims description 8
- 239000007789 gas Substances 0.000 description 29
- 229910000831 Steel Inorganic materials 0.000 description 14
- 239000010959 steel Substances 0.000 description 14
- 230000007547 defect Effects 0.000 description 6
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 5
- 239000010960 cold rolled steel Substances 0.000 description 4
- 238000007654 immersion Methods 0.000 description 4
- 238000005097 cold rolling Methods 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 238000009826 distribution Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 2
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- 238000002806 Stokes method Methods 0.000 description 2
- 238000000137 annealing Methods 0.000 description 2
- 238000007664 blowing Methods 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 238000002347 injection Methods 0.000 description 2
- 239000007924 injection Substances 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 230000001133 acceleration Effects 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 239000011449 brick Substances 0.000 description 1
- 239000003575 carbonaceous material Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000007598 dipping method Methods 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 150000002431 hydrogen Chemical class 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 239000011800 void material Substances 0.000 description 1
Landscapes
- Continuous Casting (AREA)
Description
【発明の詳細な説明】 産業上の利用分野 本発明は極低炭素チタンキルド鋼の鋳造方法に関する。Description: FIELD OF THE INVENTION The present invention relates to a method for casting ultra low carbon titanium killed steel.
従来技術 近年、冷延鋼板、冷延メッキ鋼板における加工性向上の
要求が強まっており、この要求に応えるために極低炭素
チタンキルド鋼に対する需要もますます増大している。2. Description of the Related Art In recent years, demands for improving workability of cold-rolled steel sheets and cold-rolled steel sheets have increased, and in order to meet these requirements, demand for ultra-low carbon titanium killed steel is also increasing.
冷延鋼板は一般に鋳片を熱間圧延したのち冷間圧延し、
ついで焼鈍する工程を経て製造されるが、焼鈍した鋼板
には隆起したフクレ疵の発生が見られることが多く、こ
うした欠陥は冷延鋼板製造工程の最終段階で発見される
ため原価上また工程上の被害が大きなものとなってい
た。Cold rolled steel sheet is generally cold rolled after hot rolling the slab,
Although it is manufactured through an annealing process, annealed steel sheets often show raised blistering flaws, and these defects are found at the final stage of the cold-rolled steel sheet manufacturing process. Was seriously damaged.
発明が解決しようとする課題 本発明者らは上述のフクレ疵が生ずる原因について検討
を行ったところ、フクレ疵が発生する原因の一つに、製
鋼段階においてノズル閉塞防止のため吹込まれる不活性
ガスが鋳型内の溶鋼中に混入することによることが分か
った。すなわち鋼の連続鋳造においては、タンディッシ
ュノズルを介して溶鋼を鋳型内に注入するが、この場
合、溶鋼中に懸濁した酸化物がタンディッシュノズルに
堆積してノズル閉塞を来たし易い。従ってノズル交換を
頻繁に行う必要が生じた。そこで連続鋳造においては一
般に、ノズル閉塞を防止するためタンディッシュノズル
を構成する上ノズル、スライディングノズル、下ノズ
ル、浸漬ノズル等に多孔質部若しくは細孔を設け、ここ
からアルゴンガスのような不活性ガスを溶鋼中にパージ
してノズル表面への脱酸生成物の堆積を軽減するように
している。パージされたガスは浮上分離されるが、極低
炭素チタンキルド鋼のように粘性の高い鋼種では浮上分
離されにくゝ、溶鋼中に混入したまゝの状態となる。こ
の状態で侵入したガスは鋳片中に取り残され空隙部とな
り易い。鋳片がこうした空隙を含有する状態で圧延工程
を経て焼鈍されると、焼鈍雰囲気ガス中から鋼板に侵入
した水素が空隙部に集まり、水素ガスとなる。そして冷
却時に水素の溶解度が低下する際、空隙部内のH2分圧が
上昇し、その結果軟らかいマトリックスを膨張させてフ
クレ疵を現出させるようになる。DISCLOSURE OF THE INVENTION Problems to be Solved by the Invention When the present inventors have studied the cause of the above-mentioned blistering flaw, one of the causes of the blistering flaw is an inert gas blown for preventing nozzle clogging in the steelmaking stage. It was found that the gas was mixed in the molten steel in the mold. That is, in continuous casting of steel, molten steel is injected into the mold through a tundish nozzle. In this case, however, oxides suspended in the molten steel tend to be deposited on the tundish nozzle and cause nozzle clogging. Therefore, it became necessary to frequently replace the nozzle. Therefore, in continuous casting, generally, in order to prevent nozzle clogging, a porous portion or pores are provided in an upper nozzle, a sliding nozzle, a lower nozzle, a dipping nozzle, etc. which constitute a tundish nozzle, and an inert gas such as argon gas is provided from here. The gas is purged into the molten steel to reduce the accumulation of deoxidation products on the nozzle surface. The purged gas is float-separated, but it cannot be floated-separated in steel types with high viscosity such as ultra-low carbon titanium killed steel, and remains in the state of being mixed in the molten steel. The gas that has entered in this state is likely to remain in the cast slab and become voids. When the slab is annealed through the rolling process in the state of containing such voids, hydrogen that has entered the steel sheet from the annealing atmosphere gas is collected in the voids and becomes hydrogen gas. Then, when the solubility of hydrogen decreases during cooling, the H 2 partial pressure in the void increases, and as a result, the soft matrix expands and blister defects appear.
上記の問題は溶鋼中に吹込む不活性ガスの量を少なくす
れば軽減することができるが、タンディッシュノズルが
閉塞し易くなって鋳造時間が短くなり、生産性が低下す
る。The above problem can be reduced by reducing the amount of the inert gas blown into the molten steel, but the tundish nozzle is likely to be clogged, the casting time is shortened, and the productivity is reduced.
本発明の目的は、不活性ガスが混入することによって生
ずるフクレ疵の発生を防止し、かつノズル交換頻度を増
加させることなく鋳造することができるようにするもの
である。An object of the present invention is to prevent the occurrence of blistering defects caused by the mixing of an inert gas, and to enable casting without increasing the nozzle replacement frequency.
課題の解決手段 本発明はそのためノズル閉塞防止のため使用している不
活性ガスの気泡径に着目し、これを大きくすることによ
り溶鋼中にとゞまるガス量を少なくできるようにしたも
のである。すなわち本発明はＣ≦0.010重量％、Ti≧0.0
1重量％を含有する極低炭素チタンキルド鋼を鋳造する
方法において、タンディッシュノズルより気泡径が0.6m
m以上の不活性ガスを吐出させるようにしたことを特徴
とするものである。Therefore, the present invention focuses on the bubble diameter of the inert gas used for preventing nozzle clogging, and by enlarging it, the amount of gas retained in the molten steel can be reduced. . That is, in the present invention, C ≦ 0.010% by weight, Ti ≧ 0.0
In the method of casting ultra low carbon titanium killed steel containing 1% by weight, the bubble diameter was 0.6 m from the tundish nozzle.
It is characterized in that an inert gas of m or more is discharged.
そして気泡径が0.6mm以上の不活性ガスを吐出させるた
めに気泡径３μ以上の気孔を総気孔体積の13体積％以上
含有する材質を通して不活性ガスを吐出させるようにし
たことを特徴とするものである。In order to discharge an inert gas having a bubble diameter of 0.6 mm or more, the inert gas is discharged through a material containing pores having a bubble diameter of 3 μ or more of 13 volume% or more of the total pore volume. Is.
作用 本発明者らは行った水モデルを使ったテストによれば、
溶鋼の下降流速と浸漬ノズルの吐出孔角度とは第１図に
示すような関係にあり、吐出孔角度が大きくなると下降
流速も大きくなるが、一般に使用されている浸漬ノズル
の吐出孔角度は30°以内であり、下降流速も最高が30cm
/sec程度であることが分かった。Effect According to the tests performed by the inventors using the water model,
The descending flow velocity of the molten steel and the discharge hole angle of the immersion nozzle have a relationship as shown in FIG. 1, and as the discharge hole angle increases, the descending flow velocity also increases. Within °, and the maximum descending velocity is 30 cm
It was found to be about / sec.
一方、ストークスの方式によれば、ガス気泡の浮上速度
Vfは、 Vf＝ｇ（ρFe−ρｇ）dg2/18μ として表わされる。ここで g:重力加速度（980cm/sec2） μ：溶鋼粘度（5.0×10-2g/cm・sec） ρFe：溶鋼密度（7.0g/cm3） ρg:ガス密度（g/cm3ρFe》ρｇ） dg:ガス気泡直径（cm） である。On the other hand, according to the Stokes method, the floating speed of gas bubbles
V f is expressed as V f = g (ρ Fe −ρg) dg 2 / 18μ. Where g: Gravity acceleration (980 cm / sec 2 ) μ: Molten steel viscosity (5.0 × 10 -2 g / cm ・ sec) ρ Fe : Molten steel density (7.0 g / cm 3 ) ρ g: Gas density (g / cm 3 ρ Fe >> ρg) dg: Gas bubble diameter (cm).
第２図は上記の式を使って計算したガス気泡径とガス気
泡の浮上速度との関係を示すもので、同図から気泡径が
0.6mm以上になると、気泡の浮上速度が30cm/sec以上と
なって上述する溶鋼の最大の下降流速よりも大きくな
り、浮上すると考えられる。Figure 2 shows the relationship between the gas bubble diameter calculated using the above equation and the floating speed of the gas bubble.
When it is 0.6 mm or more, the floating rate of bubbles becomes 30 cm / sec or more, which is higher than the maximum downward flow velocity of molten steel described above, and it is considered that the bubbles float.
また水モデルを使って、以下に示すような気孔径分布を
有する材質を通して不活性ガスを吹き込み、写真撮影を
行って発生する気泡のうち、気泡径0.6mm以上の気泡の
割合を測定した。その結果を以下の表に示す。Further, using a water model, an inert gas was blown through a material having a pore size distribution as shown below, and photographs were taken to measure the ratio of bubbles having a bubble diameter of 0.6 mm or more among the bubbles generated. The results are shown in the table below.
上記の表から見られるように、気孔径３μ以上の気孔を
13％有する材質の資料No.1を通して不活性ガスを吹き込
むと、発生する気泡のうち、大半（96％）が気泡径0.6m
m以上の気泡となることが見出された。因にこのときの
フクレ疵発生指数は30であり、0.6mm以上の気泡が76％
となるNo.3の資料の場合100であった。 As can be seen from the table above, pores with a pore size of 3μ or more
When an inert gas is blown through the material No. 1 which has 13% of the material, most of the bubbles (96%) are 0.6m in diameter.
It was found that bubbles of m or more were formed. By the way, the blistering flaw occurrence index at this time is 30, and the bubbles of 0.6 mm or more are 76%.
In the case of the No. 3 material, which was, it was 100.
実施例１ 浸漬ノズル内壁部から気泡径0.6mm以上のArガスを10l/m
in吐出しながらｃ≦0.01重量％、Ti≧0.03重量％の極低
炭素チタンキルド鋼を鋳造した。この方法で鋳造した鋳
片と、比較の為気泡径が0.6mm以下のものを50体積％以
上含むArガスを同様に吐出して鋳造した鋳片の冷延工程
におけるフクレ疵発生件数を比較したところ、本発明に
よる方法の方が約80％フクレ疵発生件数が低減された。Example 1 Ar gas having a bubble diameter of 0.6 mm or more was supplied from the inner wall of the immersion nozzle at 10 l / m.
While discharging, an extremely low carbon titanium killed steel with c ≦ 0.01% by weight and Ti ≧ 0.03% by weight was cast. For comparison, the number of blister defects in the cold rolling process of the slab cast by this method and the slab cast by similarly discharging Ar gas containing 50% by volume or more of a bubble diameter of 0.6 mm or less was compared. However, the method according to the present invention reduced the number of blistering defects by about 80%.
実施例２ 浸漬ノズル内壁部から気泡径0.6mm以上のArガスを10l/m
in吐出しながらｃ≦0.01重量％、Ti≧0.03重量％の極低
炭素チタンキルド鋼を鋳造した。この方法で鋳造した鋳
片と、比較の為ガス吐出しないで鋳造した鋳片の冷延工
程におけるフクレ疵発生件数を比較したところほぼ同等
であった。Example 2 10 l / m of Ar gas having a bubble diameter of 0.6 mm or more was fed from the inner wall of the immersion nozzle.
While discharging, an extremely low carbon titanium killed steel with c ≦ 0.01% by weight and Ti ≧ 0.03% by weight was cast. For comparison, a slab cast by this method and a slab cast without gas discharge were compared in terms of the number of blistering defects in the cold rolling process and found to be almost the same.
一方、鋳造時間に関しては、ガス吐出しない場合は本発
明に比較して約60％の鋳造時間しか鋳造できなかった。On the other hand, regarding the casting time, when the gas was not discharged, the casting time was only about 60% as compared with the present invention.
実施例３ タンディッシュ上プレートにガス吹き込み用の0.5mmの
貫通孔を８ケ設け、この部位よりArガスを20l/minと0l/
min吐出しながらｃ≦0.01重量％、Ti≧0.03重量％の極
低炭素チタンキルド鋼を鋳造した。このときプレートの
ガス吹き込み部の材質はAl2O395％の焼成品煉瓦であ
る。Example 3 Eight 0.5 mm through holes for gas injection were provided in the tundish upper plate, and Ar gas was supplied from this portion at 20 l / min and 0 l / min.
While discharging min, ultra-low carbon titanium killed steel with c ≦ 0.01 wt% and Ti ≧ 0.03 wt% was cast. At this time, the material of the gas blowing portion of the plate is a baked brick made of Al 2 O 3 95%.
この時の鋳造時間指数と、フクレ疵の発生指数を表２に
示す。Table 2 shows the casting time index and the blistering flaw occurrence index at this time.
表２よりガスを吐出しない場合は、フクレ疵の発生指数
は低いが、ノズル閉塞が発生して鋳造時間が短い。これ
に比較して20l/minガスを吐出した場合は、フクレ疵発
生指数は、ガスを流さない場合と同等で、かつ鋳造時間
も延長できた。From Table 2, when the gas is not discharged, the index of occurrence of blistering flaws is low, but nozzle clogging occurs and the casting time is short. In comparison with this, when 20 l / min gas was discharged, the blistering flaw generation index was equivalent to that when no gas was flown, and the casting time could be extended.
尚、0.5mmの貫通孔から吐出する気泡径の大きさは、水
モデルを使って写真撮影を行った結果、表３に示す通り
で、0.6mm以上であることが確認された。The size of the bubble discharged from the 0.5 mm through hole was photographed using a water model, and as shown in Table 3, it was confirmed that the size was 0.6 mm or more.
実施例４ タンディッシュ上プレートにガス吹き込み用の0.3mmの
貫通孔を８ケ設け、この部位よりArガスを20l/minと0l/
min吐出しながらｃ≦0.01重量％、Ti≧0.03重量％の極
低炭素チタンキルド鋼を鋳造した。このときプレートの
ガス吹き込み部の材質は、不焼成のアルミナ・カーボン
質である。（Al2O391％、C3％） この時の鋳造時間指数とフクレ疵発生指数を表４に示
す。表４よりガスを吐出しない場合はフクレ疵の発生指
数は20l/min流した時と同等であるが、ノズル閉塞が発
生して鋳造時間が短い。これに比ベガスを20l/min吐出
すると、ノズル閉塞が起きず鋳造時間の延長が図られ
た。 Example 4 Eight 0.3 mm through holes for gas injection were provided in the upper plate of the tundish, and Ar gas was supplied from this site at 20 l / min and 0 l / min.
While discharging min, ultra-low carbon titanium killed steel with c ≦ 0.01 wt% and Ti ≧ 0.03 wt% was cast. At this time, the material of the gas blowing portion of the plate is unfired alumina / carbon material. (Al 2 O 3 91%, C 3%) Table 4 shows the casting time index and blistering flaw occurrence index at this time. From Table 4, when gas is not discharged, the blistering flaw generation index is the same as when 20 l / min was flowed, but the nozzle clogging occurred and the casting time was short. On the other hand, when Vegas was discharged at 20 l / min, nozzle clogging did not occur and the casting time was extended.
尚0.3mmの貫通孔から吐出する気泡の大きさは、水モデ
ルによると表５に示す通りで、全て0.6mm以上である。The sizes of the bubbles discharged from the 0.3 mm through holes are shown in Table 5 according to the water model and are all 0.6 mm or more.
実施例５ 浸漬ノズルの内壁部の第３図に示すような気孔径分布を
もつ２種類の材質表面からArガスを10l/min吐出しなが
らｃ≦0.01重量％、Ti≧0.03重量％の極低炭素チタンキ
ルド鋼を鋳造した。この鋳片の冷延工程におけるフクレ
疵発生指数を表６に示す。 Example 5 An extremely low level of c ≦ 0.01% by weight and Ti ≧ 0.03% by weight while discharging Ar gas at 10 l / min from the surface of two kinds of materials having a pore size distribution as shown in FIG. 3 on the inner wall of the immersion nozzle. Carbon titanium killed steel was cast. Table 6 shows the blistering flaw generation index in the cold rolling process of this slab.
これを見ると、ガス吐出部の材質の３μ以上の孔径が総
気孔体積の13体積％含有するＡ材質の方が、３μ以上の
気孔径が総気孔体積の７体積％含有するＢ材質と比較し
てフクレ疵の発生指数が低い。 It can be seen that the A material containing 3% or more pore diameter of the gas discharge part contains 13% by volume of the total pore volume, and the B material contains 3% or more pore diameter of 7% by volume of the total pore volume. And the index of occurrence of blistering flaws is low.
発明の効果 本発明は以上のように構成され、次のような効果を奏す
る。EFFECTS OF THE INVENTION The present invention is configured as described above and has the following effects.
請求項１記載の方法によれば、タンディッシュノズルよ
り気泡径が0.6mm以上の不活性ガスを吐出させることに
よりノズル閉塞によって鋳造時間を短くすることなくフ
クレ疵の発生を減少させることができる。According to the method of the first aspect, the generation of blistering flaws can be reduced without shortening the casting time due to nozzle clogging by discharging an inert gas having a bubble diameter of 0.6 mm or more from the tundish nozzle.
請求項２記載の方法によれば、不活性ガスを気孔径３μ
以上の気孔を総気孔体積の13体積％以上含有する材質を
通して吐出させることにより大半を気泡径0.6mm以上の
気泡とすることができ，以ってノズル閉塞によって鋳造
時間を短くすることなくフクレ疵の発生を減少させるこ
とができる。According to the method of claim 2, the inert gas is used in a pore size of 3 μm.
By discharging the above pores through a material containing 13% by volume or more of the total pore volume, the majority of the bubbles can be bubbles with a diameter of 0.6 mm or more. Therefore, the nozzle blockage does not shorten the casting time and causes blistering. Can be reduced.
第１図は水モデルによる吐出孔角度と下降流速の関係を
示す図、第２図はストークスの方式による気泡径と浮上
速度との関係を示す図、第３図は気孔分布を示す図であ
る。FIG. 1 is a diagram showing the relationship between the discharge hole angle and the descending flow velocity according to the water model, FIG. 2 is a diagram showing the relationship between the bubble diameter and the floating velocity by the Stokes method, and FIG. 3 is a diagram showing the pore distribution. .
Claims (2)
する極低炭素チタンキルド鋼を鋳造する方法において、
タンディッシュノズルより気泡径が0.6mm以上の不活性
ガスを吐出させるようにしたことを特徴とする極低炭素
チタンキルド鋼の鋳造方法1. A method for casting an ultra low carbon titanium killed steel containing C ≦ 0.010% by weight and Ti ≧ 0.01% by weight,
Casting method for ultra-low carbon titanium killed steel characterized by discharging an inert gas with a bubble diameter of 0.6 mm or more from a tundish nozzle
込んでＣ≦0.010重量％、Ti≧0.01重量％を含有する極
低炭素チタンキルド鋼を鋳造する方法において、気孔径
３μ以上の気孔を総気孔体積の13体積％以上含有する材
質を通して不活性ガスを吐出させるようにしたことを特
徴とする極低炭素チタンキルド鋼の鋳造方法2. A method for casting an ultra-low carbon titanium killed steel containing C ≦ 0.010% by weight and Ti ≧ 0.01% by weight by injecting an inert gas from a tundish nozzle, wherein the pores having a pore diameter of 3 μm or more have a total pore volume. Of ultra low carbon titanium killed steel, characterized in that an inert gas is discharged through a material containing 13% by volume or more of
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63272618A JPH0741382B2 (en) | 1988-10-27 | 1988-10-27 | Casting method for ultra low carbon titanium killed steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63272618A JPH0741382B2 (en) | 1988-10-27 | 1988-10-27 | Casting method for ultra low carbon titanium killed steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02117758A JPH02117758A (en) | 1990-05-02 |
| JPH0741382B2 true JPH0741382B2 (en) | 1995-05-10 |
Family
ID=17516444
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63272618A Expired - Lifetime JPH0741382B2 (en) | 1988-10-27 | 1988-10-27 | Casting method for ultra low carbon titanium killed steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0741382B2 (en) |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5527414A (en) * | 1978-08-16 | 1980-02-27 | Nippon Steel Corp | Continuous casting method of ti contained molten steel |
| JPS62130754A (en) * | 1985-12-02 | 1987-06-13 | Akechi Ceramics Kk | Gas blowing type immersion nozzle |
-
1988
- 1988-10-27 JP JP63272618A patent/JPH0741382B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH02117758A (en) | 1990-05-02 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP4815821B2 (en) | Continuous casting method of aluminum killed steel | |
| JPH0741382B2 (en) | Casting method for ultra low carbon titanium killed steel | |
| JP4240916B2 (en) | Tundish upper nozzle and continuous casting method | |
| JP2001113347A (en) | Hot water supply device and continuous casting method for steel | |
| JP2003251438A (en) | Continuous casting method of slab with few bubble defects and steel material processed from the slab | |
| JP3365362B2 (en) | Continuous casting method | |
| JP2991881B2 (en) | Immersion nozzle for continuous casting | |
| JP2898296B2 (en) | Continuous casting method of slab for thin steel plate | |
| JP3348988B2 (en) | Cleaning method for molten steel in tundish | |
| JP2718608B2 (en) | Steel continuous casting method | |
| JP4595186B2 (en) | Continuous casting method | |
| JPH02187240A (en) | Submerged nozzle for high speed continuous casting | |
| JP4474948B2 (en) | Steel continuous casting method | |
| JP7711755B2 (en) | Tundish and continuous casting method using the same | |
| JPH0324296B2 (en) | ||
| JP2003205349A (en) | Continuous casting method of cast slab with few bubble defects and manufactured cast slab | |
| JPS6264461A (en) | Device for accelerating flotation of inclusion in molten steel | |
| JP2000202602A (en) | Inclusion removal method in tundish for continuous casting | |
| JP2002361378A (en) | Continuous casting method of cast slab with few bubble defects | |
| JP3238090B2 (en) | Continuous casting method of steel slab | |
| JP3642015B2 (en) | Stainless steel continuous casting method | |
| JP3570337B2 (en) | Steel continuous casting method | |
| JP3412955B2 (en) | Continuous casting method | |
| JPH0494850A (en) | Submerged nozzle | |
| JP2003285146A (en) | Continuous casting method |