JPH06297089A - Method for continuously casting low carbon sulfur and sulfur complex type free cutting steel - Google Patents
Method for continuously casting low carbon sulfur and sulfur complex type free cutting steelInfo
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- JPH06297089A JPH06297089A JP10976793A JP10976793A JPH06297089A JP H06297089 A JPH06297089 A JP H06297089A JP 10976793 A JP10976793 A JP 10976793A JP 10976793 A JP10976793 A JP 10976793A JP H06297089 A JPH06297089 A JP H06297089A
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Abstract
Description
【0001】[0001]
【産業上の利用分野】本発明は、硫黄快削鋼または硫黄
複合快削鋼を連続鋳造するに際し使用するパウダーの組
織に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to the structure of powder used in continuous casting of sulfur free-cutting steel or sulfur composite free-cutting steel.
【0002】[0002]
【従来の技術】C≦0.15%、Si≦0.03%、M
n0.80〜1.30%、P0.040〜0.080
%、S0.200〜0.350%、Al<0.003
%、T―O0.015〜0.025%を含有する低炭硫
黄快削鋼(JIS規格SUM22など)や、それに更に
Pbを0.100〜0.300%添加した低炭硫黄鉛複
合快削鋼(JIS規格SUM22Lなど)は、優れた被
削性の要求される部品に使用される。2. Description of the Related Art C≤0.15%, Si≤0.03%, M
n 0.80 to 1.30%, P 0.040 to 0.080
%, S0.200 to 0.350%, Al <0.003
%, T-O 0.015 to 0.025%, low carbon sulfur free cutting steel (JIS standard SUM22, etc.) and low carbon sulfur lead free cutting with 0.10 to 0.300% Pb added. Steel (JIS standard SUM22L, etc.) is used for parts requiring excellent machinability.
【0003】これらの鋼種では、C含有量は低く抑え、
SiやAlなどの硬質な酸化物系介在物を生成する脱酸
元素は添加しないでO含有量を高くする。MnはMnS
を形成するために、PやNは被削性向上のために添加さ
れる。In these steel types, the C content is kept low,
The O content is increased without adding a deoxidizing element that forms a hard oxide inclusion such as Si or Al. Mn is MnS
P and N are added to improve the machinability.
【0004】これらの鋼種は、低炭素高酸素濃度が特微
であり鋼中には自由酸素及びMnOやFeOを主体とす
る酸化物を多く含有している。These steel types are characterized by low carbon and high oxygen concentrations, and the steel contains a large amount of free oxygen and oxides mainly composed of MnO and FeO.
【0005】これらの自由酸素や酸化物は、鋼材の被削
性向上のためにはMnSなどの硫化物と並んで有用であ
るが、連続鋳造によるブルーム・ビレットの製造に際し
ては、凝固時の気泡発生や耐火物の溶損などの有害な影
響を及ぼす。These free oxygen and oxides are useful along with sulfides such as MnS for improving the machinability of steel materials, but in the production of bloom billets by continuous casting, bubbles during solidification Harmful effects such as generation and melting of refractory materials.
【0006】本鋼種に関する連続鋳造法に関しては、鉄
と鋼67(1981)8,P1041には連鋳化につい
て、鉄と鋼67(1981)2,A85には酸素コント
ロール並びに浸漬ノズルの材質改善について述べられて
いる。Regarding the continuous casting method for this steel type, regarding iron and steel 67 (1981) 8, P1041 regarding continuous casting, regarding iron and steel 67 (1981) 2, A85 regarding oxygen control and improvement of the material of the immersion nozzle. Stated.
【0007】[0007]
【発明が解決しようとする課題】低炭硫黄及び硫黄複合
快削鋼は、SiやAlなどの脱酸元素を含まないため、
タンデイッシュ内溶鋼中には約50〜100ppmの自
由酸素(Of)と、100〜250ppmのトータル酸
素(T―O)を含有している。Since low carbon sulfur and sulfur composite free-cutting steel do not contain deoxidizing elements such as Si and Al,
The molten steel in the tundish contains about 50 to 100 ppm of free oxygen (Of) and 100 to 250 ppm of total oxygen (TO).
【0008】このため、ブルーム・ビレット鋳片にはピ
ンホールなどの気泡性欠陥が、凝固過程でのC―O反応
に起因して発生し易い。For this reason, bubble defects such as pinholes are likely to occur in the bloom billet slab due to the CO reaction in the solidification process.
【0009】また、本鋼種がC≦0.15%以下の包晶
反応鋼であることに起因して、ディプレッションやディ
プレッション起因の縦割れが発生し易いのが特徴であ
る。Further, the present steel type is a peritectic reaction steel having C ≦ 0.15% or less, which is characterized in that depletion and vertical cracks due to depletion are likely to occur.
【0010】発明者らの知見によれば、低炭硫黄及び硫
黄複合快削鋼の連続鋳造においては、鋳型内から採取し
た溶融パウダー中のMnOやFeOを分析すると、鋳造
前のパウダー中濃度よりも高くなっている。According to the knowledge of the inventors, in continuous casting of low carbon sulfur and sulfur composite free-cutting steel, when MnO and FeO in the molten powder sampled from the mold were analyzed, it was found that the concentration in the powder before casting was higher than that in the powder. Is also getting higher.
【0011】この現象は、溶鋼中の(MnO)や(Fe
O)が鋳造中に鋳型内で浮上して、溶融パウダー中へ吸
収されるためと考えられる。This phenomenon is caused by (MnO) and (Fe in molten steel.
It is considered that O) floats in the mold during casting and is absorbed into the molten powder.
【0012】MnOやFeOの濃化は、パウダーの酸化
ポテンシャルを高めるので、下記[1]式[2]式によ
りパウダー中のCと反応してCO気泡を発生せしめ問題
である。Concentration of MnO and FeO raises the oxidation potential of the powder, and therefore it is a problem that CO bubbles are generated by reacting with C in the powder according to the following formulas [1] and [2].
【0013】[0013]
【化1】 (MnO)+C=CO(g)+Mn ・・・[1]Embedded image (MnO) + C = CO (g) + Mn ... [1]
【0014】[0014]
【化2】 (FeO)+C=CO(g)+Fe ・・・[2]Embedded image (FeO) + C = CO (g) + Fe ... [2]
【0015】また、パウダー中のMnOやFeOの増加
は、後述する如く溶融パウダーの融点及び粘性を低下さ
せ不均一流入を引き起こすので鋳型内の抜熱を変化さ
せ、ディプレッションなどの鋳片表面欠陥を増加させた
りブレークアウトを発生させるので問題である。Further, the increase of MnO and FeO in the powder lowers the melting point and viscosity of the molten powder and causes non-uniform inflow as will be described later, so that heat removal in the mold is changed to cause slab surface defects such as depletion. This is a problem because it increases the number and causes breakouts.
【0016】言うまでもなく、パウダーの粘性は、鋳型
〜鋳片間への均一な流入を保つために最も重要な特性で
あり、鋳造中に粘性が過度に低下することは操業上問題
である。中野らは、鉄と鋼69(1983),S103
6の中で、安定な抜熱を確保し健全な凝固を行わせるた
めのパウダー粘性(η)は、鋳造速度(Vc)によって
統一的に整理出来るとして[3]式を与えている。Needless to say, the viscosity of the powder is the most important characteristic for maintaining a uniform inflow between the mold and the slab, and excessive reduction of the viscosity during casting is an operational problem. Nakano et al., Iron and Steel 69 (1983), S103.
In 6, the powder viscosity (η) for ensuring stable heat removal and performing sound solidification is given by the formula [3], which can be uniformly organized by the casting speed (Vc).
【0017】[0017]
【化3】η・Vc=2.0〜3.0 ・・・[3][Chemical formula 3] η · Vc = 2.0 to 3.0 ... [3]
【0018】上記[3]式は、例えば鋳造速度がVc=
0.75m/minである場合は、粘性はη=2.7〜
4.0poiseに調整する必要があることを示すもの
である。In the above equation [3], for example, the casting speed is Vc =
When 0.75 m / min, the viscosity is η = 2.7-
This indicates that it needs to be adjusted to 4.0 poise.
【0019】[0019]
【課題を解決するための手段】本発明は、前記課題を解
決するものである。即ち、前記低炭硫黄または硫黄複合
快削鋼の連続鋳造に用いる鋳型内パウダーの塩基度(%
CaΟ/%SiΟ2)を1.0以上とすることにより、
鋳造時の溶鋼中からの(MnΟ)や(FeΟ)の吸収を
抑制せしめるものである。The present invention solves the above-mentioned problems. That is, the basicity (%) of the powder in the mold used for continuous casting of the low-carbon sulfur or sulfur composite free-cutting steel.
By setting Ca Ο /% Si Ο 2 ) to 1.0 or more,
It suppresses the absorption of (MnΟ) and (FeΟ) from the molten steel during casting.
【0020】また、前記塩基度を1.0以上としたパウ
ダーにMnΟを予め6%以下の範囲で含有せしめること
により、(MnΟ)や(FeΟ)の吸収を抑制するもの
である。Further, the powder having the basicity of 1.0 or more contains MnO in a range of 6% or less in advance, thereby suppressing absorption of (MnO) and (FeO).
【0021】発明者らの測定によれば、鋳造中における
パウダー中のMnΟやFeΟの濃度は、図1に示すよう
に添加パウダーの塩基度(%CaΟ/%SiΟ2)が低
いほど増加することが判明した。According to the measurement of the inventors, the concentration of MnΟ and FeΟ in powder during the casting, the base of the additive powder as shown in FIG. 1 (% CaΟ /% SiΟ 2 ) that increases the lower the There was found.
【0022】一方、所定のパウダーにMnOを追加して
MnO含有量を増加せしめ1,300℃での該パウダー
の粘性について、4種類のパウダーについて測定した結
果、図2に示したように、いずれのパウダーにおいても
MnO含有量の増加と共に粘性が低下することが判明し
た。On the other hand, MnO was added to a predetermined powder to increase the MnO content, and the viscosity of the powder at 1,300 ° C. was measured for four kinds of powders. As a result, as shown in FIG. It was found that the viscosity of the powder also decreased with the increase of the MnO content.
【0023】低炭硫黄または硫黄複合快削鋼において
も、図1に示したようにパウダーの塩基度が低いほど、
鋳造中にMnOやFeOの吸収量が多く、そして図2か
ら明らかなようにMnO濃度が増加すると共に粘性は低
下する。Also in low carbon sulfur or sulfur composite free cutting steel, the lower the basicity of the powder, as shown in FIG.
The amount of MnO and FeO absorbed during casting is large, and as is clear from FIG. 2, the viscosity decreases as the MnO concentration increases.
【0024】このように、鋳造前のパウダー粘性を適正
な範囲内に設定しても、塩基度が低いパウダーの場合に
は鋳造中に粘性が低下し前記適性範囲から外れる問題が
ある。As described above, even if the powder viscosity before casting is set within an appropriate range, there is a problem that the powder has a low basicity, the viscosity is lowered during casting and the powder falls outside the appropriate range.
【0025】粘性の低下を防止するには、溶鋼中(Mn
O)の吸収によるパウダー中のMnO濃化を所定の範囲
内に抑制することが必須であり、鋳造中におけるパウダ
ー中MnO濃度6%以内とする必要がある。In order to prevent the decrease of the viscosity, in molten steel (Mn
It is essential to suppress the concentration of MnO in the powder due to the absorption of (O) within a predetermined range, and it is necessary to keep the MnO concentration in the powder during casting within 6%.
【0026】この理由は、鋳造中におけるパウダー中M
nO濃度が6%以内であれば、粘性の低下率を実操業で
問題にならない30%以内に抑制できるからである。The reason for this is that M in the powder during casting
This is because if the nO concentration is within 6%, the rate of decrease in viscosity can be suppressed within 30%, which is not a problem in actual operation.
【0027】以上の観点から、本発明では硫黄複合快削
鋼のパウダーの塩基度(%CaO/%SiO2)を1.
0以上と規定するものである。From the above viewpoint, in the present invention, the basicity (% CaO /% SiO 2 ) of the powder of the sulfur composite free-cutting steel is 1.
It is defined as 0 or more.
【0028】また、図1に示した関係は、パウダーの塩
基度と(MnO)の溶解度の関係を示すものと考えるこ
とも出来る。The relationship shown in FIG. 1 can be considered to indicate the relationship between the basicity of powder and the solubility of (MnO).
【0029】図1から明らかなように、塩基度を1.0
以上とし且つパウダー中にMnOを予め6%以下の範囲
で含有せしめ、更に、鋳造中のパウダー粘性が適性値と
なるよう他の成分の含有率を調整すれば、溶鋼中(Mn
O)の吸収を抑制することが可能となりパウダー中Mn
O濃度が鋳造前と鋳造中とで殆ど変動しないほぼ一定の
適正な粘性を確保することが可能である。As is apparent from FIG. 1, the basicity is 1.0
If MnO is contained in the powder in the range of 6% or less in advance, and if the content ratio of other components is adjusted so that the powder viscosity during casting becomes an appropriate value, the MnO content in the molten steel (Mn
O) can be suppressed and Mn in the powder can be suppressed.
It is possible to secure a substantially constant and proper viscosity in which the O concentration hardly changes before and during casting.
【0030】[0030]
【作用】本発明によれば、高酸素鋼である硫黄複合快削
鋼の連続鋳造において、溶鋼中(MnO)や(FeO)
の吸収を抑制することが出来るので、パウダー中のMn
OやFeOなどの酸化物とパウダー中のCとの反応によ
るCO気泡の生成防止が図れる。According to the present invention, in continuous casting of sulfur composite free-cutting steel which is a high oxygen steel, in molten steel (MnO) or (FeO)
Since it can suppress the absorption of
It is possible to prevent generation of CO bubbles due to the reaction of oxides such as O and FeO with C in the powder.
【0031】同時に、鋳造中のパウダーの溶融特性(粘
性)の低下を防止可能であり、パウダーの流入量を一定
に保てるので、ディプレッションやブレークアウトなど
を回避することが出来る。At the same time, the melting property (viscosity) of the powder during casting can be prevented from deteriorating, and the inflow amount of the powder can be kept constant, so that depletion and breakout can be avoided.
【0032】[0032]
【実施例】実施例について以下に詳細に示す。EXAMPLES Examples will be described in detail below.
【0033】270T転炉にて硫黄複合快削鋼を溶製
し、曲率半径12mRの4ストランド湾曲型連鋳機で、
鋳片断面サイズが350mm×560mmのブルーム
を、鋳造速度Vc=0.75m/minで鋳造した。In a 270T converter, sulfur composite free-cutting steel was smelted, and a 4-strand curved continuous casting machine with a radius of curvature of 12 mR
Bloom having a slab cross-sectional size of 350 mm × 560 mm was cast at a casting speed Vc = 0.75 m / min.
【0034】タンディッシュ内溶鋼の成分は、0.08
%C―1.02%Mn―0.069%P―0.325%
S―90ppmOf―157ppmT.Oであり、S
i、Alは皆無であった。The composition of molten steel in the tundish is 0.08.
% C-1.02% Mn-0.069% P-0.325%
S-90 ppm Of-157 ppm T.I. O and S
There was no i or Al.
【0035】使用したパウダーの鋳造前及び鋳造中の化
学成分と粘性を、比較例と共に第1表に示す。The chemical composition and viscosity of the powder used before and during casting are shown in Table 1 together with comparative examples.
【0036】本発明1では、鋳造前のパウダーの塩基度
を1.09としているので、鋳造中の(MnO)や(F
eO)の吸収量が少ない。In the present invention 1, since the basicity of the powder before casting is 1.09, (MnO) and (F
There is little absorption of eO).
【0037】このため、粘性低下も小さく鋳造前η=
3.5poiseが鋳造中η=2.7poiseとなっ
ており、前記[3]式で与えられる適正範囲内に入って
いる。Therefore, the decrease in viscosity is small and η before casting =
The value of 3.5 poise is η = 2.7 poise during casting, which is within the proper range given by the formula [3].
【0038】また、本発明2では、パウダーの塩基度を
1.06とすると共に予め4.5%のMnOを添加して
いるので、鋳造中における(MnO)の吸収が殆どない
ので、粘性の変化が認められず良好である。Further, in the present invention 2, since the basicity of the powder is set to 1.06 and 4.5% MnO is added in advance, there is almost no absorption of (MnO) during casting, so that the viscosity of No change is observed and it is good.
【0039】これに対して、比較例1及び比較例2の場
合は、塩基度が1.0よりも低いので、鋳造中の(Mn
O)の吸収量が多く粘性低下が非常に大きい。On the other hand, in the case of Comparative Example 1 and Comparative Example 2, since the basicity is lower than 1.0, (Mn during casting)
The amount of O) absorbed is large and the viscosity is greatly reduced.
【0040】このため、比較例1では鋳造前の粘性を適
正範囲よりも高く設定せざるを得ず、また比較例2の場
合には、鋳造前に適正範囲内に設定しても鋳造中には低
めに大きく外れてしまっており問題である。Therefore, in Comparative Example 1, the viscosity before casting must be set higher than the proper range, and in Comparative Example 2, even if the viscosity is set within the proper range before casting, the viscosity during casting is still high. Is a problem because it is off by a large amount.
【0041】以上より、得られた鋳片の表面性状は本発
明実施の場合が極めて良好であった。From the above, the surface properties of the obtained slab were extremely good in the case of carrying out the present invention.
【0042】[0042]
【表1】 [Table 1]
【0043】[0043]
【発明の効果】低炭硫黄および硫黄複合快削鋼のよう
な、低炭高酸素の鋼を鋳造するに際して、パウダーの塩
基度を適正に調整し、また予めMnOを添加することに
より、安定した操業の実施及び良好な鋳片の確保が可能
であり、その適用効果は極めて大きい。EFFECTS OF THE INVENTION When casting low-carbon high-oxygen steels such as low-carbon sulfur and sulfur composite free-cutting steels, the basicity of the powder is properly adjusted, and MnO is added in advance to stabilize the stability. It is possible to carry out operations and secure good slabs, and its application effect is extremely large.
【図1】パウダーの塩基度とMnO及びFeOの濃度の
関係を示す図。FIG. 1 is a diagram showing the relationship between the basicity of powder and the concentrations of MnO and FeO.
【図2】パウダー中MnO濃度と粘性の関係を示す図。FIG. 2 is a diagram showing a relationship between MnO concentration in powder and viscosity.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 菅原 健 室蘭市仲町12番地 新日本製鐵株式会社室 蘭製鐵所内 (72)発明者 鈴木 功夫 室蘭市仲町12番地 新日本製鐵株式会社室 蘭製鐵所内 (72)発明者 吉満 卓 福岡県豊前市八屋1808―3 ─────────────────────────────────────────────────── ─── Continuation of front page (72) Inventor Ken Sugawara 12 Nakamachi, Muroran City Muroran Works, Nippon Steel Co., Ltd. Steelworks (72) Inventor Takashi Yoshimitsu 1808-3 Hachiya, Buzen, Fukuoka Prefecture
Claims (2)
3重量%以下、Alが0.003重量%未満、Tota
l Oが0.015以上0.025以下重量%を含有す
る硫黄快削鋼または硫黄複合快削鋼を連続鋳造するに際
し、塩基度(CaO/SiO2重量%比)が1.0以上
のパウダーを鋳型内溶鋼上に添加することを特徴とする
低炭硫黄および硫黄複合快削鋼の連続鋳造法。1. C is 0.15% by weight or less and Si is 0.0
3% by weight or less, Al less than 0.003% by weight, Tota
A powder having a basicity (CaO / SiO 2 weight% ratio) of 1.0 or more when continuously casting a sulfur free-cutting steel or a sulfur composite free-cutting steel containing 10% by weight or more and 0.025% or less by weight. Continuous casting method for low-carbon sulfur and sulfur composite free-cutting steels, characterized by adding to the molten steel in the mold.
3重量%以下、Alが0.003重量%未満、Tota
l Oが0.015以上0.025以下重量%を含有す
る硫黄快削鋼または硫黄複合快削鋼を連続鋳造するに際
し、塩基度(CaO/SiO2重量%比)が1.0以上
であり、且つMnOが6重量%以下を含有するパウダー
を鋳型内溶鋼上に添加することを特徴とする低炭硫黄お
よび硫黄複合快削鋼の連続鋳造法。2. C is 0.15% by weight or less and Si is 0.0
3% by weight or less, Al less than 0.003% by weight, Tota
When continuously casting a sulfur free-cutting steel or a sulfur composite free-cutting steel containing 10% by weight or more and 0.025 or less by weight, the basicity (CaO / SiO 2 weight% ratio) is 1.0 or more. And a powder containing MnO in an amount of 6% by weight or less is added onto the molten steel in the mold to continuously cast low carbon sulfur and sulfur composite free-cutting steel.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP5109767A JP3049460B2 (en) | 1993-04-14 | 1993-04-14 | Continuous casting of low carbon sulfur and sulfur composite free cutting steel. |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP5109767A JP3049460B2 (en) | 1993-04-14 | 1993-04-14 | Continuous casting of low carbon sulfur and sulfur composite free cutting steel. |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH06297089A true JPH06297089A (en) | 1994-10-25 |
JP3049460B2 JP3049460B2 (en) | 2000-06-05 |
Family
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Family Applications (1)
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JP5109767A Expired - Fee Related JP3049460B2 (en) | 1993-04-14 | 1993-04-14 | Continuous casting of low carbon sulfur and sulfur composite free cutting steel. |
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JP (1) | JP3049460B2 (en) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN101982257A (en) * | 2010-10-15 | 2011-03-02 | 河南通宇冶材集团有限公司 | Specific crystallizer casting powder for sulphur free-cutting steel and production method thereof |
JP2016507382A (en) * | 2013-01-25 | 2016-03-10 | 宝山鋼鉄股▲分▼有限公司 | Fluorine-free continuous casting mold flux for ultra-low carbon steel |
-
1993
- 1993-04-14 JP JP5109767A patent/JP3049460B2/en not_active Expired - Fee Related
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN101982257A (en) * | 2010-10-15 | 2011-03-02 | 河南通宇冶材集团有限公司 | Specific crystallizer casting powder for sulphur free-cutting steel and production method thereof |
JP2016507382A (en) * | 2013-01-25 | 2016-03-10 | 宝山鋼鉄股▲分▼有限公司 | Fluorine-free continuous casting mold flux for ultra-low carbon steel |
Also Published As
Publication number | Publication date |
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JP3049460B2 (en) | 2000-06-05 |
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