JP2010042425A - Mold powder for continuously casting steel - Google Patents
Mold powder for continuously casting steel Download PDFInfo
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- JP2010042425A JP2010042425A JP2008207866A JP2008207866A JP2010042425A JP 2010042425 A JP2010042425 A JP 2010042425A JP 2008207866 A JP2008207866 A JP 2008207866A JP 2008207866 A JP2008207866 A JP 2008207866A JP 2010042425 A JP2010042425 A JP 2010042425A
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- 239000000843 powder Substances 0.000 title claims abstract description 64
- 229910000831 Steel Inorganic materials 0.000 title claims description 40
- 239000010959 steel Substances 0.000 title claims description 40
- 238000005266 casting Methods 0.000 title claims description 12
- 238000009749 continuous casting Methods 0.000 claims abstract description 25
- 239000000126 substance Substances 0.000 claims abstract description 10
- 229910052796 boron Inorganic materials 0.000 claims abstract description 9
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 9
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 27
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 10
- ODINCKMPIJJUCX-UHFFFAOYSA-N calcium oxide Inorganic materials [Ca]=O ODINCKMPIJJUCX-UHFFFAOYSA-N 0.000 claims description 9
- 239000002994 raw material Substances 0.000 claims description 9
- 238000001514 detection method Methods 0.000 abstract description 11
- 239000010960 cold rolled steel Substances 0.000 abstract description 8
- 230000007547 defect Effects 0.000 abstract description 4
- 238000011109 contamination Methods 0.000 abstract 1
- 239000002893 slag Substances 0.000 description 30
- 230000000694 effects Effects 0.000 description 16
- 238000007711 solidification Methods 0.000 description 11
- 230000008023 solidification Effects 0.000 description 11
- 229910052782 aluminium Inorganic materials 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 6
- 230000008018 melting Effects 0.000 description 6
- 238000002844 melting Methods 0.000 description 6
- 238000005336 cracking Methods 0.000 description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 4
- 230000003247 decreasing effect Effects 0.000 description 4
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 3
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 3
- 238000002156 mixing Methods 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 229910000655 Killed steel Inorganic materials 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 238000005461 lubrication Methods 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 230000000704 physical effect Effects 0.000 description 2
- 230000009257 reactivity Effects 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 238000004781 supercooling Methods 0.000 description 2
- 229910004261 CaF 2 Inorganic materials 0.000 description 1
- BVKZGUZCCUSVTD-UHFFFAOYSA-L Carbonate Chemical compound [O-]C([O-])=O BVKZGUZCCUSVTD-UHFFFAOYSA-L 0.000 description 1
- KRHYYFGTRYWZRS-UHFFFAOYSA-M Fluoride anion Chemical compound [F-] KRHYYFGTRYWZRS-UHFFFAOYSA-M 0.000 description 1
- 229910018068 Li 2 O Inorganic materials 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
- 230000008859 change Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 230000003301 hydrolyzing effect Effects 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 239000010410 layer Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 230000001050 lubricating effect Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000010422 painting Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000004044 response Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000007788 roughening Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- 238000004017 vitrification Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
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- Continuous Casting (AREA)
Abstract
Description
本発明は鋼の連続鋳造において鋳型内に添加して使用する連続鋳造用パウダーに関し、薄板鋼板用特に冷間圧延鋼板用の鋼の鋳造に使用することにより鋼板の表面疵を低減し、また円滑な鋳造作業ができるものを提供する。 The present invention relates to a powder for continuous casting which is used by being added to a mold in continuous casting of steel, and is used for casting steel for a thin steel plate, particularly a cold-rolled steel plate. That can be easily cast.
溶鋼の連続鋳造においては粉末または顆粒状態のパウダーが鋳型内の湯面に散布される。このパウダーは溶鋼表面で溶解してスラグの溶融層を形成し、溶鋼の保温、酸化防止および非金属介在物の吸収を行なうとともに、鋼の凝固シェルと鋳型との間に流れ込んでスラグフィルムを形成する。この鋳型と鋳片の凝固シェル間に流入するスラグフィルムは潤滑作用を行なうとともに鋳片よりの抜熱を制御し、優れた表面性状の鋳片を得ると共に清浄で良好な鋳片を製造する作用をする。 In the continuous casting of molten steel, powder or granular powder is sprayed on the molten metal surface in the mold. This powder melts on the surface of the molten steel to form a molten layer of slag that keeps the molten steel warm, prevents oxidation and absorbs non-metallic inclusions, and flows between the solidified shell of steel and the mold to form a slag film. To do. The slag film flowing between the mold and the solidified shell of the slab performs lubrication and controls the heat removal from the slab, thereby obtaining a slab having excellent surface properties and producing a clean and good slab. do.
鋼の連続鋳造は、品質要求が厳しい冷間圧延鋼板の素材である極低炭素鋼、低炭アルミキルド鋼に適用が拡大されてきた。冷間圧延鋼板は表面に非金属介在物が露出するとスリバー疵と称する線状の疵となり、電気製品や自動車などの製品の塗装によっても覆い隠すことは困難となる。ところが冷間圧延鋼板は厚さが数ミリメートル以下まで圧延されるので、鋳片の状態に比較して表面積が非常に拡大されることになる。したがって冷間圧延鋼板用の鋳片は表面品位のみならず、冷間圧延鋼板において表面となるべき鋳片の内質部分が優れていることが要求され、特にスラグの巻き込みがなく介在物の少ない鋳片を製造する必要がある。 The continuous casting of steel has been widely applied to ultra-low carbon steel and low-carbon aluminum killed steel, which are cold-rolled steel materials with strict quality requirements. When the non-metallic inclusions are exposed on the surface of the cold-rolled steel sheet, it becomes a linear ridge called a sliver ridge, and it is difficult to cover it even by painting products such as electric products and automobiles. However, since the cold-rolled steel sheet is rolled to a thickness of several millimeters or less, the surface area is greatly expanded as compared with the state of the slab. Therefore, slabs for cold-rolled steel sheets are required not only to have surface quality, but also to be excellent in the quality of the slabs that should be the surface of cold-rolled steel sheets, especially without slag entrainment and few inclusions It is necessary to produce a slab.
特開2006−192440号公報(特許文献1)には、自動車用鋼板のような高品質が要求される鋼板を製造する場合に適したモールドパウダーについて記載されている。この目的のためには溶鋼内部へのモールドパウダーの巻き込みを防止することが必要であるところ、モールドパウダー溶融物の溶鋼中アルミニウムとの反応性が巻き込みと関連していることを見出したとしている。そして溶鋼中のアルミニウムの酸化源となるSiO2、Na2O、Li2Oのパウダー中の含有量を、スラグの粘度と関連して制限することにより溶鋼中へのパウダー巻き込みが顕著に低減し、圧延後のコイル表面疵をコイル当たり1個以下まで減少できたとしている。 Japanese Patent Application Laid-Open No. 2006-192440 (Patent Document 1) describes a mold powder suitable for manufacturing a steel plate that requires high quality such as a steel plate for automobiles. For this purpose, it is necessary to prevent the entrainment of mold powder inside the molten steel, and the inventors have found that the reactivity of the mold powder melt with aluminum in the molten steel is related to entrainment. And by restricting the content of SiO 2 , Na 2 O, Li 2 O, which is the oxidation source of aluminum in the molten steel, in relation to the viscosity of the slag, the entrainment of the powder in the molten steel is significantly reduced. The coil surface defects after rolling can be reduced to 1 or less per coil.
また、特開2006−175472号公報(特許文献2)には、Al、Tiの少なくとも一方を含有する鋼を連続鋳造するためのモールドパウダーについて記載されている。そして鋼中にAlやTiを含有すると、パウダー中のSiO2が溶鋼中のAlやTiと反応してパウダーの物性値が変化し、パウダーの潤滑性や鋼へのパウダーの巻き込みが悪化するとしている。そこで特許文献2においては1550℃におけるSiO2の活量を0.4以下に制限している。上記の活量は当該成分の濃度に、他の共存成分との相互作用で定まる活量係数を乗じたものであって化学反応性を示すが、第一義的には当該成分の濃度に依存するものである。事実、特許文献2の実施例を見ると、本発明例のモールドパウダーのSiO2が18.8〜33.0%であるところ、比較例のSiO2は38.3〜40.1%になっている。
本発明者らは品質要求が厳しい鋼において、鋳片へのモールドパウダーの巻き込みの問題に対処するためにSiO2の含有量を従来の約40質量%(以下、%と記載)から32%以下に低減したパウダーを製造した。その結果、パウダーの巻き込みの問題は改善されたがブレークアウトの検知が度々発生するようになった。ブレークアウトの検知は鋳型の一定高さ位置に複数の温度センサを間隔を置いて取り付け、これの温度が異常に変化すると警報を発するものである。このため実際にはブレークアウトに至らないまでも鋳型温度の推移に乱れがあればブレークアウトの検知が発生することになる。本発明はこのようなブレークアウトの検知が発生しないようなモールドパウダーを提供することを目的とする。 In order to cope with the problem of entrainment of mold powder in a slab, the present inventors have changed the content of SiO 2 from about 40% by mass (hereinafter referred to as “%”) to 32% or less in steels with strict quality requirements. A reduced powder was produced. As a result, the problem of powder entrainment has been improved, but breakout detection has occurred frequently. To detect breakout, a plurality of temperature sensors are mounted at regular intervals on the mold at intervals, and an alarm is issued when the temperature of these sensors changes abnormally. For this reason, even if the breakout is not actually reached, the breakout is detected if there is a disturbance in the transition of the mold temperature. An object of this invention is to provide the mold powder which does not generate | occur | produce such a breakout detection.
本発明は前記課題を課題を解決するものであって、化学成分として、SiO2、CaO、Al2O3、Na2O、B2O3、FおよびCを含有する鋼の連続鋳造用モールドパウダーにおいて、SiO2が20〜32%、Al2O3が5〜15%、Na2Oが1〜8%、B2O3が1〜10%、Fが3〜11%であることを特徴とする鋼の連続鋳造用パウダーである。
ここにおいて、上記の鋼の連続鋳造用パウダーは1300℃における粘度が0.5〜5.0poiseであること、また、C以外の化学成分のうち、少なくとも2種類の成分についてはプリメルトされた配合原料を使用すること、また、薄板鋼板用の鋼を鋳造するためのものであることも特徴とする。またさらに化学成分が、CaO:30〜50%、C:0.3〜5%であることも特徴とする。
The present invention has been made to solve the problems the above problems, as chemical components, SiO 2, CaO, Al 2 O 3, Na 2 O, B 2 O 3, F and continuous casting mold of steel containing C in powders, SiO 2 is 20 to 32% Al 2 O 3 is 5 to 15% Na 2 O is 1 to 8% B 2 O 3 is 1-10%, the F is 3-11% It is a featured powder for continuous casting of steel.
Here, the above-mentioned steel continuous casting powder has a viscosity at 1300 ° C. of 0.5 to 5.0 poise, and among chemical components other than C, at least two types of components are pre-melted blended raw materials It is also characterized by being for casting steel for a thin steel plate. Furthermore, the chemical component is characterized by CaO: 30 to 50% and C: 0.3 to 5%.
本発明の連続鋳造用パウダーは、SiO2の含有量を低減することにより鋳片へのパウダーの巻き込みの問題が改善されている一方、従来のこのような成分のパウダーに見られるブレークアウトの検知が度々発生する問題も無い。このため品質要求が厳しい冷間圧延鋼板の素材である極低炭素鋼、低炭アルミキルド鋼の連続鋳造において良好な品質の鋳片が得られるとともに、円滑な鋳造作業ができる。 While the powder for continuous casting of the present invention has improved the problem of entrainment of powder in the slab by reducing the content of SiO 2 , it detects breakouts found in conventional powders of such components. There is no problem that often occurs. For this reason, it is possible to obtain a slab of good quality in continuous casting of ultra-low carbon steel and low-carbon aluminum killed steel, which are raw materials for cold-rolled steel sheets with strict quality requirements, and smooth casting work can be performed.
本発明の連続鋳造用パウダーは板厚3.2mm以下である薄板鋼板、特に冷間圧延鋼板用の鋼を鋳造するためのものであって、鋳片へのモールドパウダーの巻き込みの防止のためSiO2の含有量を32%以下まで低減することを特徴点の一つとしている。本発明者らは、このようなSiO2の含有量を低減したパウダーを使用した場合に度々発生するブレークアウト検知を防止する手段について種々検討した。その結果SiO2の含有量を低減したパウダーに対して、B2O3を1%以上含有させることによりブレークアウト検知の発生を顕著に低減できることが判明した。 The powder for continuous casting of the present invention is for casting a thin steel plate having a thickness of 3.2 mm or less, particularly a steel for cold rolling steel plate, and is used to prevent the entrainment of mold powder into a slab. One of the features is to reduce the content of 2 to 32% or less. The inventors of the present invention have studied various means for preventing breakout detection that frequently occurs when such a powder having a reduced content of SiO 2 is used. As a result, it has been found that the occurrence of breakout detection can be significantly reduced by adding 1% or more of B 2 O 3 to the powder having a reduced content of SiO 2 .
連続鋳造用パウダーは鋳型内に添加することにより溶融してスラグとなって鋳型と鋳片間に流入し、鋳型からは常に冷却を受ける。このために流入したスラグは鋳型側では凝固して固体状態のフィルム状となって鋳型に接しており、また鋳片側では凝固シェルにより溶融した液体状態のフィルム状となっている。したがってたとえば鋳型と鋳片の間へのスラグの流入が不具合になったり、また鋳型で急冷されたガラス状のフィルムが部分的に結晶化して熱伝導率が低くなってスラグフィルムの伝熱のばらつきが発生し凝固不均一になったりすると、鋳型の温度のばらつきが過大となってブレークアウト検知の警報が発生することになる。 The powder for continuous casting is melted by adding it into the mold to form a slag and flows between the mold and the slab, and is always cooled from the mold. For this reason, the slag that has flowed in is solidified on the mold side to form a solid film and is in contact with the mold, and on the slab side is a liquid film melted by the solidified shell. Therefore, for example, the inflow of slag between the mold and the slab becomes a problem, or the glassy film rapidly cooled by the mold is partially crystallized to lower the thermal conductivity, resulting in variations in heat transfer of the slag film. If this occurs and the solidification becomes uneven, the temperature variation of the mold becomes excessive and a breakout detection alarm is generated.
上記のことからブレークアウト検知の発生には溶融スラグの粘度や凝固温度が関係することが判る。しかしながら本発明者らの知見によると、B2O3の添加によるブレークアウト検知の発生の低減効果は、単なる粘度や凝固温度の適正化ではなくB2O3に特有の作用に基くものと考えられる。すなわち、もしスラグの粘度が係っているのなら、B2O3以外の成分、例えば弗化物の量を変えることによっても粘度を調節し得るので、これにより同様の効果を得ることができる筈である。凝固温度についても同様であって、B2O3を添加しなくても他の成分の量を変えたり、さらには連続鋳造用パウダーの成分として常に一般的に使用されるものではないMgOやTiO2などの添加によっても調節し得る。 From the above, it can be seen that the occurrence of breakout detection is related to the viscosity of the molten slag and the solidification temperature. However, according to the findings of the present inventors, the effect of reducing the occurrence of breakout detection by the addition of B 2 O 3 is considered based on the effect unique to the B 2 O 3 rather than optimizing just the viscosity and solidification temperature It is done. That is, if the viscosity of the slag is related, the viscosity can be adjusted by changing the amount of components other than B 2 O 3 , such as fluoride, so that the same effect can be obtained. It is. The same applies to the solidification temperature, and the amount of other components can be changed without addition of B 2 O 3, and it is not always used as a component of powder for continuous casting. It can also be adjusted by adding 2 or the like.
しかしながらB2O3以外の成分によってはブレークアウト検知の発生の低減効果は得られないことから、B2O3固有の作用効果に基くものと判断される。現象から見て、SiO2の含有量の低減によるブレークアウト検知の発生は、凝固して固体状態となって鋳型に接しているスラグフィルムの脱落によるものと本発明者らは考えており、B2O3はこのようなスラグフィルムの脱落を抑止する効果があると考えられる。すなわちSiO2はスラグをガラス質にする働きをしている成分であるが、これが減少するとスラグフィルムのガラス質の性状が劣化して脱落しやすくなるのに対し、B2O3を添加することによりガラス化が促進されてスラグフィルムを強化する作用をしているものと推定される。 However, since components other than B 2 O 3 cannot obtain the effect of reducing the occurrence of breakout detection, it is determined that the component is based on the operational effects unique to B 2 O 3 . From the viewpoint of the phenomenon, the present inventors consider that the occurrence of breakout detection due to the reduction in the content of SiO 2 is due to the slag film falling into solid state and in contact with the mold. 2 O 3 is considered to have an effect of preventing such slag film from falling off. In other words, SiO 2 is a component that works to make slag vitreous, but if this is reduced, the glassy properties of the slag film will be degraded and easily fall off, whereas B 2 O 3 should be added. It is presumed that vitrification is promoted by this to strengthen the slag film.
本発明の連続鋳造用モールドパウダーは、上記のSiO2およびB2O3を含めて、化学成分としてSiO2、CaO、Al2O3、Na2O、B2O3、FおよびCを含有するが、これら成分の限定理由について説明する。 The mold powder for continuous casting according to the present invention contains SiO 2 , CaO, Al 2 O 3 , Na 2 O, B 2 O 3 , F and C as chemical components including the above-mentioned SiO 2 and B 2 O 3. However, the reasons for limiting these components will be described.
SiO2はパウダーの主成分であるが、先に述べたように鋳片へのパウダーの巻き込みの防止のためSiO2の含有量を32%以下にする。しかし20%未満になるとスラグの粘度が低下し過ぎてしまう。したがってSiO2は20〜32%とする。 SiO 2 is the main component of the powder, but as described above, the content of SiO 2 is set to 32% or less in order to prevent the powder from being caught in the slab. However, when it is less than 20%, the viscosity of the slag is too low. Therefore, SiO 2 is a 20 to 32 percent.
Al2O3は凝固温度を下げる目的で使用するが、Al2O3が5%未満では凝固温度を充分に下げられない。また15%を超えると、凝固温度が極端に低くなり、鋳造条件に合致しなくなると共にアルミナ系介在物が多くなるおそれがある。したがってAl2O3は5〜15%とする。 Al 2 O 3 is used for the purpose of lowering the solidification temperature. However, if Al 2 O 3 is less than 5%, the solidification temperature cannot be lowered sufficiently. On the other hand, if it exceeds 15%, the solidification temperature becomes extremely low, which does not meet the casting conditions, and the alumina inclusions may increase. Thus Al 2 O 3 is 5 to 15%.
Na2Oは粘度を低下させる成分であり、規定粘度範囲に維持する目的で使用する。Na2Oの量1%未満では粘度低下の効果が不十分であり、一方8%を超えると粘度が下がり過ぎる。したがってNa2Oは1〜8%とする。 Na 2 O is a component that lowers the viscosity and is used for the purpose of maintaining the viscosity within a specified viscosity range. If the amount of Na 2 O is less than 1%, the effect of decreasing the viscosity is insufficient, while if it exceeds 8%, the viscosity is excessively decreased. Therefore, Na 2 O is 1 to 8%.
B2O3は前記のようにブレークアウト検知の発生の低減効果を得るためには1%以上必要であるが、その効果を確実にするためには2%以上添加することが好ましい。一方、10%を超えて添加すると溶融スラグから硼素が還元されて鋳片表層部に硼素が含有され、鋳片の割れ感受性を増大させるおそれがある。また価格的にも高価であり、5%を超えて添加しても効果が飽和してくるので5%以下とするのが好ましい。したがってB2O3は1〜10%とするが、特に好ましくは下限は2%、上限は5%とする。 B 2 O 3 needs to be 1% or more in order to obtain the effect of reducing the occurrence of breakout detection as described above, but it is preferable to add 2% or more in order to ensure the effect. On the other hand, if added over 10%, boron is reduced from the molten slag and boron is contained in the slab surface layer, which may increase the cracking susceptibility of the slab. Moreover, it is expensive in terms of price, and even if added over 5%, the effect is saturated, so it is preferable to make it 5% or less. Therefore, B 2 O 3 is 1 to 10%, and particularly preferably, the lower limit is 2% and the upper limit is 5%.
Fは粘度を低下させる成分であり、規定粘度範囲に維持する目的で使用する。Fの量が3%未満では粘度低下の効果が不十分であり、一方11%を超えると粘度が下がり過ぎる。したがってFは3〜11%とする。なおF量はCaF2やNaFなどのF化合物のF当量である。 F is a component that lowers the viscosity and is used for the purpose of maintaining the viscosity within a specified range. If the amount of F is less than 3%, the effect of decreasing the viscosity is insufficient, while if it exceeds 11%, the viscosity is excessively decreased. Therefore, F is 3 to 11%. Note F amount is F equivalent of F compounds such as CaF 2 or NaF.
またCaOはSiO2とともにパウダーの主成分であり、含有量は30〜50%が好ましく、特にSiO2量との関連においてCaO/SiO2が0.9〜1.8の範囲になるように含有させるのが好ましい。CaO/SiO2が0.9未満では粘度が高くなり物性の調整が困難であり、1.8を超えると所定の粘度が得られ難いと共にスラグフィルムのガラス質の性状が劣化しやすくなる。 Also CaO is a main component of the powder with SiO 2, the content is preferably 30-50%, containing in particular as CaO / SiO 2 in relation to the amount of SiO 2 is in the range of 0.9 to 1.8 It is preferable to do so. If CaO / SiO 2 is less than 0.9, the viscosity becomes high and it is difficult to adjust the physical properties. If it exceeds 1.8, it is difficult to obtain a predetermined viscosity and the glassy properties of the slag film are likely to deteriorate.
またCは炭素粉などの状態で添加され、添加量に応じてパウダーの溶融速度を遅くする作用がある。含有量は1〜5%が好ましく、0.3%未満では溶融速度が速すぎ、5%を超えると溶融速度が遅くなるため溶融プール厚が薄くなり、潤滑機能が阻害される。なおこのCには配合原料としてCaの炭酸塩などを使用した場合など、化合物として含有するCは入らない。 C is added in the form of carbon powder or the like, and has the effect of slowing the melting rate of the powder according to the amount added. The content is preferably 1 to 5%. If the content is less than 0.3%, the melting rate is too fast, and if it exceeds 5%, the melting rate becomes slow, so that the melt pool thickness becomes thin and the lubricating function is hindered. This C does not contain C contained as a compound, such as when a carbonate of Ca is used as a blending raw material.
溶融スラグの粘度は鋳造速度に応じて適正な値とすることが必要である。本発明の連続鋳造用パウダーにおいては1300℃における粘度が0.5〜5.0poiseであることが好ましい。0.5poise未満では溶融スラグの過剰流入による鋳片表面の肌荒れが発生するおそれがあり、一方、粘度が5.0poiseより高いと溶融スラグの不均一流入による鋳片の割れが発生するおそれがある。なお凝固スラグの凝固温度は1000〜1250℃が適当であって、これより低いと過冷却による鋳片の割れが発生するおそれがあり、高いと鋳型の潤滑が不良になるおそれがある。 The viscosity of the molten slag needs to be an appropriate value depending on the casting speed. In the continuous casting powder of the present invention, the viscosity at 1300 ° C. is preferably 0.5 to 5.0 poise. If it is less than 0.5 poise, the surface of the slab may be rough due to excessive inflow of molten slag. On the other hand, if the viscosity is higher than 5.0 poise, the slab may be cracked due to non-uniform inflow of molten slag. . The solidification temperature of the solidified slag is suitably 1000 to 1250 ° C. If it is lower than this, there is a risk of cracking of the slab due to supercooling, and if it is high, the mold may be poorly lubricated.
また、連続鋳造の高速化に対応してパウダーの迅速かつ均一な溶融を図るため、溶融速度調整剤であるC以外の化学成分のうち、少なくとも2種類の成分、たとえばSiO2とCaOについてはプリメルトされた配合原料を使用することが好ましい。またプリメルトされた原料はパウダー全体の40%以上使用するのがその効果を発揮するために好ましい。プリメルト原料は、成分をアーク炉などで溶融した後、ジェット水流により水滓化して製造される。 In addition, in order to achieve rapid and uniform melting of the powder in response to the high speed of continuous casting, at least two kinds of chemical components other than C, which is a melting rate adjusting agent, such as SiO 2 and CaO, are pre-melted. It is preferable to use the formulated raw material. Moreover, it is preferable to use 40% or more of the premelted raw material in order to exhibit the effect. The pre-melt raw material is manufactured by melting components in an arc furnace or the like and then hydrolyzing them with a jet water stream.
以下、実施例により本発明を詳細に説明する。
表1に示す化学成分の連続鋳造用モールドパウダーを各種試作して冷間圧延板を製造するための極低炭素鋼(炭素量0.03%)の連続鋳造に使用した。このときの鋳造結果と溶融スラグの粘度と凝固温度も表1にあわせて示す。なお記号AとCのパウダーについては配合原料のうち、Si酸化物とCa酸化物についてプリメルトした基材を使用した。
Hereinafter, the present invention will be described in detail by way of examples.
Various types of mold powders for continuous casting having the chemical components shown in Table 1 were prepared and used for continuous casting of ultra-low carbon steel (carbon content 0.03%) for producing cold rolled sheets. The casting results, the viscosity of the molten slag, and the solidification temperature are also shown in Table 1. In addition, about the powder of the symbols A and C, the base material which pre-melted about Si oxide and Ca oxide was used among the mixing | blending raw materials.
表1において「鋼板表面疵発生」は冷間圧延コイル1個当たりの表面疵が平均1個所以下を極めて良好として◎印、平均1を超えて2以下を良好として○印、2を超える場合を不良として×印とした。また連続鋳造は鋳造速度は1.7m/分で行なったが、200t鋳造してブレークアウト警報が1回も出なかった場合に「鋳型温度安定度」が極めて良好として◎印、1回警報が出た場合に良好として○印、2回を超える場合を不良として×印とした。 In Table 1, “steel surface flaw generation” means that the surface flaw per cold-rolled coil is extremely good when the average is 1 or less on average, the mark is ◎, the average is over 1 and 2 or less is good, and the mark is over 2 X was marked as defective. Continuous casting was performed at a casting speed of 1.7 m / min. However, when no breakout warning was issued after 200 tons, the "mold temperature stability" was very good, and a single alarm was given. When it came out, it was marked as “Good”, and when it exceeded 2 times, it was marked as “Poor” as bad.
上記の鋼板表面疵発生、鋳型温度安定度の他に、表1の「その他」の欄に記載の点を併せて「総合評価」として極めて良好を◎印、良好を○印、不良を×印とした。記号A〜Dは本発明のパウダーであって鋼板表面疵発生状況、鋳型温度安定度とも良好で、特にB2O3が2%以上添加されている記号B〜Dのパウダーは鋳型温度安定度が極めて良好であった。またプリメルトした配合原料を使用した記号AとCのパウダーは、パウダーの鋳型内での溶融が迅速かつ円滑に行なわれ、高速の鋳造に適していることが確認された。 In addition to the occurrence of surface flaws on the steel sheet and the mold temperature stability, the points described in the “Others” column of Table 1 are combined, and “Comprehensive evaluation” indicates “very good”, “good”, and “bad”. It was. Symbols A to D are powders according to the present invention, both the state of occurrence of surface flaws on the steel sheet and the mold temperature stability are good. In particular, the powders of symbols B to D to which 2% or more of B 2 O 3 is added are mold temperature stability. Was very good. In addition, it was confirmed that the powders of symbols A and C using the pre-melted blended raw material were melted quickly and smoothly in the mold of the powder and were suitable for high-speed casting.
これに対して比較例である記号Eのパウダーは、B2O3含有量が低いので鋳型温度安定度が不良であった。また記号FのパウダーはB2O3含有量が高過ぎるので、鋳片の表面の硼素量が多くなり鋳片の割れが発生した。 On the other hand, the powder of symbol E, which is a comparative example, had a poor mold temperature stability because of its low B 2 O 3 content. Further, since the powder of symbol F has a B 2 O 3 content that is too high, the amount of boron on the surface of the slab increased and cracking of the slab occurred.
また比較例である記号GのパウダーはSiO2含有量が低過ぎるのでスラグの粘度が低く、溶融スラグの過剰流入による鋳片表面の肌荒れが発生した。一方、記号HのパウダーはSiO2含有量が高いのでパウダー巻き込みによる鋼板表面疵発生が多かった。 The powder symbol G is a comparative example the viscosity of the slag is low because SiO 2 content is too low, surface roughening slab surface due to excessive flow of molten slag occurs. On the other hand, since the powder of symbol H has a high SiO 2 content, there were many occurrences of surface flaws on the steel sheet due to the entrainment of the powder.
また比較例である記号IのパウダーはAl2O3含有量が低いので凝固温度が高く、潤滑不良による鋳片の割れが発生した。一方、記号JはAl2O3含有量が高過ぎるので凝固温度が低く過冷却による鋳片の割れが発生した。 Further, the powder of symbol I, which is a comparative example, had a low content of Al 2 O 3, so the solidification temperature was high, and cracking of the slab due to poor lubrication occurred. On the other hand, the symbol J had a too high Al 2 O 3 content, so the solidification temperature was low and cracking of the slab due to supercooling occurred.
また比較例である記号KのパウダーはNa2O含有量が低いので粘度が高く、溶融スラグの不均一流入のため鋳片表面疵が多かった。一方、記号LのパウダーはNa2O含有量が高過ぎるので粘度が低く、溶融スラグの過剰流入による鋳片表面の肌荒れが発生した。 Moreover, the powder of the symbol K which is a comparative example had a high viscosity because of its low Na 2 O content, and there were many slab surface defects due to the uneven flow of molten slag. On the other hand, the powder of symbol L had a low viscosity because the Na 2 O content was too high, and the slab surface was rough due to excessive inflow of molten slag.
また比較例である記号MのパウダーはF含有量が低いので粘度が高く、溶融スラグの不均一流入にのため鋳片表面疵が多かった。一方、記号NのパウダーはF含有量が高過ぎるので粘度が低く、溶融スラグの過剰流入による鋳片表面の肌荒れが発生した。 Moreover, the powder of the symbol M which is a comparative example has a high viscosity because the F content is low, and there are many slab surface defects due to uneven flow of molten slag. On the other hand, the powder of symbol N had a low viscosity because the F content was too high, and the slab surface was rough due to excessive inflow of molten slag.
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