JPH04107239A - Method for melting silicon steel stock - Google Patents
Method for melting silicon steel stockInfo
- Publication number
- JPH04107239A JPH04107239A JP22235790A JP22235790A JPH04107239A JP H04107239 A JPH04107239 A JP H04107239A JP 22235790 A JP22235790 A JP 22235790A JP 22235790 A JP22235790 A JP 22235790A JP H04107239 A JPH04107239 A JP H04107239A
- Authority
- JP
- Japan
- Prior art keywords
- silicon steel
- ladle
- slag
- molten steel
- content
- 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.)
- Granted
Links
- 229910000976 Electrical steel Inorganic materials 0.000 title claims abstract description 38
- 238000000034 method Methods 0.000 title claims description 13
- 238000002844 melting Methods 0.000 title claims description 6
- 230000008018 melting Effects 0.000 title claims description 6
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 37
- 239000010959 steel Substances 0.000 claims abstract description 37
- 239000002893 slag Substances 0.000 claims abstract description 29
- 239000000463 material Substances 0.000 claims abstract description 13
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 6
- 239000000203 mixture Substances 0.000 claims description 24
- 229910045601 alloy Inorganic materials 0.000 claims description 19
- 239000000956 alloy Substances 0.000 claims description 19
- 238000004519 manufacturing process Methods 0.000 abstract description 9
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 abstract description 8
- 230000004907 flux Effects 0.000 abstract description 7
- 229910052782 aluminium Inorganic materials 0.000 abstract description 6
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract description 3
- 229910052593 corundum Inorganic materials 0.000 abstract description 3
- 229910001845 yogo sapphire Inorganic materials 0.000 abstract description 3
- 235000012239 silicon dioxide Nutrition 0.000 abstract description 2
- 229910017082 Fe-Si Inorganic materials 0.000 abstract 3
- 229910017133 Fe—Si Inorganic materials 0.000 abstract 3
- 230000001105 regulatory effect Effects 0.000 abstract 3
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 abstract 2
- 239000002994 raw material Substances 0.000 abstract 2
- 229910052681 coesite Inorganic materials 0.000 abstract 1
- 229910052906 cristobalite Inorganic materials 0.000 abstract 1
- 239000000377 silicon dioxide Substances 0.000 abstract 1
- 229910052682 stishovite Inorganic materials 0.000 abstract 1
- 229910052905 tridymite Inorganic materials 0.000 abstract 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical group [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 16
- 229910005347 FeSi Inorganic materials 0.000 description 14
- ODINCKMPIJJUCX-UHFFFAOYSA-N Calcium oxide Chemical compound [Ca]=O ODINCKMPIJJUCX-UHFFFAOYSA-N 0.000 description 12
- 229910052742 iron Inorganic materials 0.000 description 8
- 239000000292 calcium oxide Substances 0.000 description 6
- 235000012255 calcium oxide Nutrition 0.000 description 6
- 238000011109 contamination Methods 0.000 description 5
- 239000012535 impurity Substances 0.000 description 5
- 230000000694 effects Effects 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- OGIDPMRJRNCKJF-UHFFFAOYSA-N titanium oxide Inorganic materials [Ti]=O OGIDPMRJRNCKJF-UHFFFAOYSA-N 0.000 description 4
- 238000005275 alloying Methods 0.000 description 3
- 239000002826 coolant Substances 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 229910052717 sulfur Inorganic materials 0.000 description 3
- MYMOFIZGZYHOMD-UHFFFAOYSA-N Dioxygen Chemical compound O=O MYMOFIZGZYHOMD-UHFFFAOYSA-N 0.000 description 2
- BYFGZMCJNACEKR-UHFFFAOYSA-N aluminium(i) oxide Chemical compound [Al]O[Al] BYFGZMCJNACEKR-UHFFFAOYSA-N 0.000 description 2
- 238000000137 annealing Methods 0.000 description 2
- 229910052787 antimony Inorganic materials 0.000 description 2
- 229910052785 arsenic Inorganic materials 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 229910052797 bismuth Inorganic materials 0.000 description 2
- 239000003795 chemical substances by application Substances 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 238000007872 degassing Methods 0.000 description 2
- 229910001882 dioxygen Inorganic materials 0.000 description 2
- 229910052745 lead Inorganic materials 0.000 description 2
- 230000001590 oxidative effect Effects 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 229910052711 selenium Inorganic materials 0.000 description 2
- 229910052718 tin Inorganic materials 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical group [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- 238000007664 blowing Methods 0.000 description 1
- 229910052791 calcium Inorganic materials 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000005261 decarburization Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000005389 magnetism Effects 0.000 description 1
- 230000005415 magnetization Effects 0.000 description 1
- 230000005012 migration Effects 0.000 description 1
- 238000013508 migration Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 239000004575 stone Substances 0.000 description 1
Landscapes
- Treatment Of Steel In Its Molten State (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
この発明は２次再結晶粒を（１１０） ［００１Ｆ方位
すなわちゴス方位に高度に集積させた一方向性けい素鋼
板の製造に供するけい素鋼素材の溶製方法に関する。DETAILED DESCRIPTION OF THE INVENTION (Field of Industrial Application) This invention provides a silicon steel sheet for producing unidirectional silicon steel sheets in which secondary recrystallized grains are highly concentrated in the (110) [001F orientation, that is, the Goss orientation. Concerning a method for melting steel materials.
一方向性けい素鋼板は主にトランス等の電気機器の鉄芯
として使用されるもので、磁化特性並びに鉄損特性に優
れることか要求される。特に近年電気機器の小型化の要
請から、通常ＢＩｏ値で代表される磁束密度の高い、具
体的にはＢ１０値で１．９１Ｔを越える一方向性けい素
鋼板に対する要求はとりわけ強い。Unidirectional silicon steel sheets are mainly used as iron cores in electrical equipment such as transformers, and are required to have excellent magnetization characteristics and iron loss characteristics. Particularly in recent years, due to the demand for downsizing of electrical equipment, there is a particularly strong demand for grain-oriented silicon steel sheets that usually have a high magnetic flux density represented by the BIo value, specifically, a B10 value exceeding 1.91T.
例えはＢ１０値か１．８９Ｔを越えるけい素鋼板の製造
方法に関して特開昭５４−３５８１７号公報には、Ｔ１
及び酸可溶性ＡＩ （以下、Ａ１．。１と略記する）
をそれぞれ０．００３ ｗｔ％ （以下単に％と示す）
以下とし、Ｃ：０．０６！％以下、Ｓｉ ： ２． （
１−４，０％、Ｍｎ０１Ｏ１〜０．２０９’６、Ｓｅ若
しくはＳの何れか少なくとも１種を合計てｏ、 ｏｏｓ
〜ｏ、 １ｏｏ６、Ｓｂ、 Ａｓ、 Ｂｉ、 Ｐｂ及
びＳｎのうちから選はれる１種又は２種以上を合計で０
．００５〜０．１０％含有し、残部実質的にＦｅよりな
るけい素鋼素材を、熱間圧延と４０〜８０％の圧下率の
最終冷延を含む圧延工程によって最終板厚の冷延板を得
て、この冷延板に対し脱炭を兼ねた１次再結晶焼鈍を施
した後、８００〜９２０ ’Ｃの温度で（１１０） ［
００１Ｆ方位の２次再結晶粒を十分成長させ、引続き１
０００°Ｃ以上の温度で不純物を除去する最終焼鈍を施
す工程からなる製造方法についての開示かある。For example, Japanese Patent Application Laid-Open No. 54-35817 describes a method for manufacturing silicon steel sheets with a B10 value exceeding 1.89T.
and acid-soluble AI (hereinafter abbreviated as A1..1)
0.003 wt% (hereinafter simply referred to as %)
As below, C: 0.06! % or less, Si: 2. (
1-4.0%, Mn01O1-0.209'6, at least one of Se or S in total o, oos
~o, 1oo6, Sb, As, Bi, Pb, and Sn or more selected from 0 in total
．． A silicon steel material containing 0.005 to 0.10% and the remainder substantially consisting of Fe is processed into a cold-rolled plate of final thickness through a rolling process including hot rolling and final cold rolling with a rolling reduction of 40 to 80%. This cold-rolled sheet was subjected to primary recrystallization annealing which also served as decarburization, and then (110) [
The secondary recrystallized grains with the 001F orientation are grown sufficiently, and then 1
There is also a disclosure of a manufacturing method comprising a final annealing step to remove impurities at a temperature of 000° C. or higher.
（従来の技術）
上記の製造に供するけい素鋼素材を溶製するには、溶銑
を転炉で脱炭吹錬したのち出鋼し、取鍋内若しくはＲＨ
脱ガス装置内で金＠Ｓｌ若しくはＦｅＳｉ合金、さらに
Ｓｅ若しくはＳの合金、又はＳｂ、 Ａｓ。(Prior art) In order to melt the silicon steel material used in the above manufacturing process, hot metal is decarburized and blown in a converter, then tapped and heated in a ladle or at RH.
In the degasser, gold@Sl or FeSi alloys, as well as alloys of Se or S, or Sb, As.
Ｂｉ、 Ｐｂ及びＳｎのうちから選はれる１種又は２種
以上を含む合金を添加することによって成分調整を行い
、清浄な溶鋼とする手順か通例である。The usual procedure is to adjust the composition by adding an alloy containing one or more selected from Bi, Pb, and Sn to produce clean molten steel.
（発明か解決しようとする課題）
上記けい素鋼素材の溶製方法においては、（１）合金剤
特に金属Ｓｉ若しくはＦｅＳｉ合金はＴｉ及びＡＩを多
量に含むため、けい素鋼素材にＴｉ及びＡ１か混入する
、
（２）金属Ｓｉ若しくはＦｅＳｉ合金を溶鋼に添加する
と取鍋スラグのＴｉＯ２及びＡｌ２Ｏ３か還元され、Ｔ
ｉ及びＡＩとして溶鋼中に混入する、
のか不可避に生じる。(Problems to be Solved by the Invention) In the above-mentioned method for melting a silicon steel material, (1) since the alloying agent, especially metal Si or FeSi alloy, contains a large amount of Ti and AI, the silicon steel material contains Ti and Al. (2) When metallic Si or FeSi alloy is added to molten steel, TiO2 and Al2O3 in the ladle slag are reduced, and T
The following will inevitably occur: i and AI will be mixed into molten steel.
すなわちけい素鋼素材中の（Ｔｊ＋Ａ１．。１）の混入
量は２０ｐｐｍを下回ることはなく、このような不純物
の多いけい素鋼素材から磁束密度の高いけい素鋼板を製
造するのは極めて難しい。That is, the amount of (Tj+A1..1) mixed in the silicon steel material never falls below 20 ppm, and it is extremely difficult to manufacture a silicon steel sheet with a high magnetic flux density from such a silicon steel material with many impurities.
一方（Ｔｉ＋Ａ Ｉ 、、Ｉ）の和を２０ｐｐｍ未満と
するには、極めて純度の高い金属Ｓｉを必要とするため
不経済で、したかってＢ１０値の高いものを工業的に得
ることは困難であった。On the other hand, making the sum of (Ti+A I,, I) less than 20 ppm requires extremely pure metal Si, which is uneconomical, and it is therefore difficult to industrially obtain one with a high B10 value. Ta.
この発明は上記問題点を解決するために成されたもので
、溶鋼に添加するＦｅＳｉ合金さらに合金剤添加後の溶
鋼の成分を調整することによって、不純物の少ないけい
素鋼素材を溶製し得る方法について提案することを目的
とする。This invention was made to solve the above problems, and by adjusting the FeSi alloy added to molten steel and the composition of molten steel after adding alloying agents, it is possible to melt silicon steel material with few impurities. The purpose is to propose methods.
（課題を解決するための手段）
この発明は、取鍋に収容したけい素鋼用溶鋼に、７０〜
８０％のＳｉを含有しかつ、Ｔｉ・０．０２０％以下及
びＡｔ ： ０．０５０％以下に抑制した成分組成のＦ
ｅＳ ｉ合金を添加し、取鍋内のスラグ成分を
Ａｌ２Ｏ，］： ８８％以
下ｉＯ２： ０．５％以下でかつ
Ｃａｂ／ ５Ｉ０２ ： ０．６〜２．０の範囲に調整
することを特徴とするけい素鋼素材の溶製方法である。(Means for Solving the Problems) This invention provides molten steel for silicon steel housed in a ladle with a
F with a component composition containing 80% Si and suppressing Ti to 0.020% or less and At: 0.050% or less
eSi alloy is added and the slag component in the ladle is adjusted to Al2O, ]: 88% or less, iO2: 0.5% or less, and Cab/5I02: 0.6 to 2.0. This is a method for melting silicon steel materials.
（作 用）
取鍋内のけい素鋼用溶鋼に添加するＦｅＳｉ合金さらに
合金元素添加後における取鍋内のスラグを、この発明に
従う成分組成の範囲内にそれぞれ保つ二とにより、けい
素鋼素材として用いる溶鋼中の（Ｔｉ＋Ａ１．。１）量
を２０ｐｐｍ未満にする二とかできる。(Function) By keeping the FeSi alloy added to the molten steel for silicon steel in the ladle and the slag in the ladle after adding alloying elements within the range of the composition according to the present invention, It is possible to reduce the amount of (Ti+A1..1) in the molten steel used as less than 20 ppm.
なせならＦｅＳｉ合金の成分組成を規制し溶鋼に添加す
るＦｅＳｉ合金から溶鋼中に持ち込まれるＴｉ及びＡ１
の混入量を減らした上て、取鍋内のスラグの成分調整を
行うことによって、取鍋スラグと溶鋼とは熱力学的に平
衡関係を保ち、取鍋スラグ中のＴｉ及びＡ１かスラグか
ら溶鋼中へ移行するのを防止し得るためである。Ti and A1 brought into the molten steel from the FeSi alloy are added to the molten steel by controlling the composition of the FeSi alloy.
By reducing the mixed amount of slag and adjusting the composition of the slag in the ladle, the ladle slag and molten steel maintain a thermodynamically balanced relationship, and the molten steel is removed from the Ti and A1 in the ladle slag or from the slag. This is because it can prevent migration into the interior.
以下にＦｅＳｉ合金及び取鍋スラグの組成範囲を限定す
る理由を説明する。The reason for limiting the composition ranges of the FeSi alloy and ladle slag will be explained below.
まずＦｅＳｉ合金中のＴｉ及びＡＩの含有量をそれぞれ
０．０２００ｔｉ以下及び０．０５０％以下にするのは
、これらの範囲をこえる含有は、取鍋スラグの組成を上
記の適合範囲に保ったとしても、例えば取鍋スラグ量が
極端に少ない場合などに溶鋼中の（Ｔｉ十Ａｌ５ｏｌ）
量が２０ｐｐｍ以上になることがあり、従ってＴｉ及び
ＡＩの含有量は上記の範囲内で極力低下させることが好
ましい。特にＴｉは溶鋼からの除去可能量となる取鍋ス
ラグ中での許容量が上述のように著しく低いため溶鋼中
のＴｉ量はより少ないこ七が好ましく 、０．０１５％
以下にすることで溶鋼中のＴｉ量を］Ｏｐｐｍ未満にす
ることができる。さらにＦｅＳｉ合金に含まれる不可避
的不純物としてはＣ２Ｍｎ、 Ｐ、 Ｓ、 Ｃｕ、
Ｎｉ、 Ｃｒ、 Ｃａ等があり、これらの含有量も少
ないほど製品の電磁特性に及ぼす影響は小さくなる。First, the content of Ti and AI in the FeSi alloy should be 0.0200ti or less and 0.050% or less, respectively, because the content exceeding these ranges should be maintained even if the composition of the ladle slag is kept within the above-mentioned compatible range. Also, for example, when the amount of ladle slag is extremely small, (Ti + Al 5 ol) in molten steel
The content of Ti and AI may be 20 ppm or more, therefore, it is preferable to reduce the content of Ti and AI as much as possible within the above range. In particular, since the amount of Ti in ladle slag that can be removed from molten steel is extremely low as described above, the amount of Ti in molten steel is preferably as low as 0.015%.
By doing the following, the amount of Ti in the molten steel can be made less than ]Oppm. Furthermore, unavoidable impurities contained in FeSi alloy include C2Mn, P, S, Cu,
These include Ni, Cr, Ca, etc., and the lower the content of these, the smaller the influence on the electromagnetic properties of the product.
なおこの発明に従う組成になるＦｅＳｉ合金は、純度の
高い珪石と前述の不純物濃度の低い厳選した鉄鉱石を電
気炉で還元、溶融し精錬することによって製造すること
ができる。Note that the FeSi alloy having the composition according to the present invention can be manufactured by reducing, melting, and refining highly pure silica stone and the above-mentioned carefully selected iron ore with a low impurity concentration in an electric furnace.
次に取鍋スラグの成分は、該スラグ中のＡ１□０゜及び
ＴｉＯ□が低ければ低いほど溶鋼中のＴｉ及びＡｌ量は
低くなる。Next, regarding the components of the ladle slag, the lower the A1□0° and TiO□ in the slag, the lower the amounts of Ti and Al in the molten steel.
すなわちＣａＯ／ＳｉＯ□比は低い方が溶鋼中のＡＩ。In other words, the lower the CaO/SiO□ ratio, the more AI is in the molten steel.
Ｔｉが低くなるが、ＣａＯ／ＳｉＯ□比が０．６未満に
なると取鍋スラグの流動性が悪くなり、有効なスラグと
溶鋼の反応が行えなくなるだけでなく溶鋼中の酸素が増
加し、磁性改善効果が得られない。一方ＣａＯ／ＳｉＯ
□比が高くなると溶鋼中のＡｌ、Ｔｉの混入率が高くな
るので２．０を上限とする。Although the Ti content decreases, if the CaO/SiO No improvement effect can be obtained. On the other hand, CaO/SiO
As the □ ratio increases, the mixing rate of Al and Ti in the molten steel increases, so the upper limit is set at 2.0.
しかしＣａＯ／５ｉＯｚが適正範囲でもＡ ｌ ｔｃｈ
が８％を越えるとＡＩ、。、を１０ｐｐｍ未満とするこ
とができないし、またＴｉ０ｚが０．５％を越えてもＴ
ｉを１０ｐｐｍ未満にできない。また、望ましくはＡ
ｌ ｔ（ｈを５％以下、ＴｉＯ２を０．１％以下にする
と（Ｔｉ＋Ａ Ｉ 、、Ｌ）≦１０ｐｐｍを達成するこ
とができる。However, even if CaO/5iOz is within the appropriate range, Al tch
If it exceeds 8%, AI. , cannot be made less than 10 ppm, and even if Ti0z exceeds 0.5%, T
i cannot be less than 10 ppm. Also, preferably A
When l t(h is 5% or less and TiO2 is 0.1% or less, (Ti+A I ,,L)≦10 ppm can be achieved.
なお取鍋スラグ中に不可避的に含まれるＭｇＯ。Furthermore, MgO is unavoidably contained in the ladle slag.
ＦｅＯ及びＭｎＯは低い方が望ましいが、これらの総和
が１５％以下なら実質的な影響は無視し得る。It is desirable that FeO and MnO be low, but if their total is 15% or less, the substantial effect can be ignored.
上記に加えてより一層Ｔｉ、Ａ Ｉレベルを低下させた
い場合や、何らかのトラブルで処理前のＴｉ、ＡＩレベ
ルが２０ｐｐｍ以上になった場合や、転炉出鋼時に転炉
内スラグ（塩基度が３．０〜７．０と高い）が取鍋内に
大量（≧１５ｋｇ／ｌ）に流入した場合などは、取鍋内
の溶鋼に対して酸素ガスを０．００５Ｎｍ’／１−ＩＮ
Ｉ１３／ｌの範囲で吹き込むことにより、溶鋼中のＴｉ
やＡ１を酸化除去すると共に、Ｓｉを酸化させることで
必然的に取鍋内スラグ中の塩基度をより一層低下させ、
従来不可能とされている脱Ｔｉ、ＡＩを実施できる。In addition to the above, if you want to further reduce the Ti and AI levels, or if the Ti and AI levels before treatment are over 20 ppm due to some trouble, or if you want to reduce the slag in the converter (basicity 3.0 to 7.0) flows into the ladle in large quantities (≧15 kg/l), the molten steel in the ladle should be treated with oxygen gas at 0.005 Nm'/1-IN.
By blowing in the range of I13/l, Ti in the molten steel is
By oxidizing and removing A1 and oxidizing Si, the basicity in the slag in the ladle is inevitably further reduced,
It is possible to perform Ti removal and AI, which were previously considered impossible.
次に溶鋼に供給する酸素量について説明する。Next, the amount of oxygen supplied to molten steel will be explained.
Ｉ Ｎｍ’／ｌをこえる酸素ガスの吹き込みを行うと、
溶鋼中のＳｉのロスが大きくなって追加するＳｉ合金鉄
量も増加し製造コストの増大をまねく。加えて発熱量も
太きく（１０°Ｃ以上の昇温）なり、それを冷却するに
は、冷却材を溶鋼に投入せざるを得なくなる不利も生じ
る。この冷却材の添加により、逆に冷却材からＴｉやＡ
Ｉがピックアップされ、かえってＴｉやＡＩ含有量が上
昇する問題も生じる上、前述の様に溶鋼中の酸素が増加
することで磁性改善効果が得られなくなる。When oxygen gas is injected in excess of I Nm'/l,
The loss of Si in the molten steel increases, and the amount of Si alloy iron added also increases, leading to an increase in manufacturing costs. In addition, the amount of heat generated increases (temperature rise of 10° C. or more), and in order to cool it, a coolant must be added to the molten steel, which is disadvantageous. By adding this coolant, Ti and A are removed from the coolant.
There is also the problem that I is picked up and the contents of Ti and AI increase, and as mentioned above, the effect of improving magnetism cannot be obtained due to the increase in oxygen in the molten steel.
（実施例）
実施炎上
１８０ｔの溶鋼を転炉から取鍋に出鋼中、表１に示す成
分組成のＦｅＳｉ合金８．８ｔを添加し、引続き表２の
組成を有する合成フラックス２ｔを添加した。(Example) While 180 tons of molten steel was being tapped from a converter to a ladle, 8.8 tons of FeSi alloy having the composition shown in Table 1 was added, followed by 2 tons of synthetic flux having the composition shown in Table 2.
この合成フラツクスは転炉から流出した約３ｔのスラグ
及びＦｅＳ ｉ合金の一部が酸化されて生成しりＳｉＯ
２などと溶解し合い、次の組成を有するほぼ均質な取鍋
スラグを生成した。This synthetic flux is produced by the oxidation of approximately 3 tons of slag flowing out from the converter and a portion of the FeSi alloy.
2 and others to form a substantially homogeneous ladle slag having the following composition:
〈取鍋スラグ組成〉
ＣａＯ／５ｉＯｚ ： ０．８０
Ａ１□０３ ：３．２％
ＴｉＯ□ ： ０．０９％
（ＭｎＯ＋ＦｅＯ＋Ｍｇ０） ： ３．８％Ｆ
：ｏ、ｓ％
その後溶鋼に１５５０°Ｃで約２０分間ＯＲＨ脱ガス処
理を施し、連続鋳造法にて鋳造しけい素綱スラブを得た
。このスラブの化学成分組成は次の通りであり、（Ｔｉ
十八へ ５ｏｔ）の混入量は７ ｐｐｍであった。<Ladle slag composition> CaO/5iOz: 0.80 A1□03: 3.2% TiO□: 0.09% (MnO+FeO+Mg0): 3.8%F
: o, s% Thereafter, the molten steel was subjected to ORH degassing treatment at 1550°C for about 20 minutes, and a silicon steel slab was obtained by continuous casting. The chemical composition of this slab is as follows: (Ti
The amount of contamination (18 to 5 ot) was 7 ppm.
くけい素鋼スラブの化学成分組成〉
Ｃ１０，０４％、Ｓｉ／３．５１％、Ｍｎ１０．０５％
、５ｅ１０．０３０％、５ｂ１０．０２５ ％、 ＡＩ
１０．０００２％、Ｔｉ７０．０００５％、Ｏｌｏ、
００１２％、
次いでこのけい素綱スラブを用いて上述の特開昭５４−
３５８１７号公報に従う手順で方向性けい素鋼板とした
。かくして得られた板厚０．２〜Ｑ、３ｍｍの製品の磁
気特性はＢ１０値の平均値が１．９３Ｔ以上で１．９５
Ｔを越える製品が得られ、鉄損−５，７，。値も０．９
Ｗ／ｋｇ以下のものが得られた。Chemical composition of silicon steel slab> C10.04%, Si/3.51%, Mn10.05%
, 5e10.030%, 5b10.025%, AI
10.0002%, Ti70.0005%, Olo,
0012%, and then using this silicon steel slab, the above-mentioned JP-A-54-
A grain-oriented silicon steel sheet was prepared using the procedure according to Publication No. 35817. The magnetic properties of the thus obtained product with a plate thickness of 0.2 to Q, 3 mm are 1.95 when the average B10 value is 1.93T or more.
A product exceeding T was obtained, with an iron loss of -5.7. The value is also 0.9
W/kg or less was obtained.
１呈１
実施例１と同様に、１８０ｔの溶鋼を転炉から取鍋に出
鋼中、表１に示した成分組成のＦｅＳｉ合金約９ｔを添
加し、引続き焼石灰を５００ｋｇ加えた後、１５５０°
Ｃで２０分間ＯＲＨ脱ガス処理を施し、取鍋スラグを次
に示す組成に調整した。1 Presentation 1 As in Example 1, while 180 tons of molten steel was being tapped from a converter to a ladle, about 9 tons of FeSi alloy having the composition shown in Table 1 was added, and then 500 kg of burnt lime was added, and then 1550 tons of molten steel was poured into a ladle. °
The ladle slag was subjected to ORH degassing treatment at C for 20 minutes, and the ladle slag was adjusted to the composition shown below.
〈取鍋スラグ組成〉
Ｃａｂ／ ５ｉＯｚ ： １．１４
Ａ Ｉ ｚ０３： ５．６％
ＴｉＯ□ ：０．１３％
（ＭｎＯ＋ＦｅＯ＋Ｍｇ０） ： ９．４１％その後連
続鋳造法にて鋳造しけい素鋼スラブを得た。このスラブ
の化学成分組成は次の通りであり、（Ｔｉ ＋ Ａ Ｉ
＄６１）の混入量はｌ０ｐｐ−であった。<Ladle slag composition> Cab/5iOz: 1.14 AI z03: 5.6% TiO□: 0.13% (MnO+FeO+Mg0): 9.41% After that, a cast silicon steel slab was obtained by continuous casting method. Ta. The chemical composition of this slab is as follows: (Ti + A I
The amount of contamination ($61) was 10 pp-.
くけい素鋼スラブの化学成分組成〉
Ｃ１０，０４％、Ｓｉ／３．４８％、Ｍｎ１０．０６％
、５ｅ１０．０３０％、５ｂ１０．０２５ ％、 Ａ
１ ｓｏＬ １０．０００３％、Ｔｉ１０．０００７％
、Ｏ１０，００１０％、
次いでこのけい素鋼スラブを用いて実施例１と同様特開
昭５４−３５８１７号公報に従う手順で方向性けい素鋼
板とした。かくして得られた板厚０．２〜０．３閣の製
品の磁気特性はＢ、。値の平均値が１．９１Ｔ以上で１
．９４Ｔを越える製品が得られ、鉄損−１７／、。Chemical composition of silicon steel slab> C10.04%, Si/3.48%, Mn10.06%
, 5e10.030%, 5b10.025%, A
1 soL 10.0003%, Ti 10.0007%
, O10,0010%.Then, this silicon steel slab was used to prepare a grain-oriented silicon steel plate in the same manner as in Example 1 according to the procedure described in JP-A-54-35817. The magnetic properties of the thus obtained product with a plate thickness of 0.2 to 0.3 mm are B. 1 if the average value is 1.91T or more
．． A product with a strength exceeding 94T was obtained, with an iron loss of -17/.
値は０．８〜１．０Ｗ／ｋｇ以下のものが得られた。Values of 0.8 to 1.0 W/kg or less were obtained.
比較■
また比較として、実施例２と同様の処理を、添加するＦ
ｅＳｉ合金の成分組成のうちＡ１：０．０５２％及びＴ
ｉ：０．０２１％に変更して行った場合の取鍋スラグ組
成は次の通りであり、得られた連鋳スラブの（Ｔｉ十Ａ
ｌ ５ｏｔ）混入量は２１ｐｐｍであった。Comparison■ Also, as a comparison, the same treatment as in Example 2 was carried out with the addition of F.
A1: 0.052% and T in the component composition of eSi alloy
The ladle slag composition when changing i to 0.021% is as follows, and the obtained continuous cast slab (Ti + A
15ot) The amount of contamination was 21 ppm.
〈取鍋スラグ組成〉
Ｃａｂ／ Ｓｉｎｇ ： ２．１０
Ａ Ｉ 、０． ： ７．５％
ＴｉＯ□ ： ０．６０％
（ＭｎＯ＋ ＦｅＯ±Ｍｇ０） ： ９．６％次いでこ
の連鋳スラブを上記実施例と同様に方向性けい素鋼板と
したところ、この鋼板の磁気特性はＢ１゜値の平均値が
１．８９Ｔで１．９３Ｔを越える製品はほとんど得られ
ず、鉄損ｈ＋ｔ／ｓｏ値は０．９〜１．１Ｗ／ｋｇであ
った。<Ladle slag composition> Cab/Sing: 2.10 AI, 0. : 7.5% TiO□ : 0.60% (MnO+ FeO±Mg0) : 9.6% Next, this continuous cast slab was made into a grain-oriented silicon steel plate in the same manner as in the above example, and the magnetic properties of this steel plate were as follows. The average B1° value was 1.89T, and hardly any products exceeding 1.93T were obtained, and the iron loss h+t/so value was 0.9 to 1.1 W/kg.
ちなみにこの発明に従うＡＩ及びＴｉの混入低減方法は
、高炭素軸受鋼や極細線用鋼等の溶製にも適用できる。Incidentally, the method for reducing contamination of AI and Ti according to the present invention can also be applied to the production of high carbon bearing steel, ultrafine wire steel, and the like.
（発明の効果）
この発明に従う方法によって、けい素鋼素材の（Ｔｉ
＋ Ａ １５ａｔ）混入量を２０ｐｐｍ未満に抑えるこ
とができ、Ｂ１゜値の平均値が１．９１を越えるような
高磁束密度でかつ、鉄損値ｈ＋ｔｚｓ。値も大幅に低減
した方向性けい素鋼板の製造を容易に実現するけい素鋼
素材を工業的に熔製し得る。(Effect of the invention) By the method according to the invention, silicon steel material (Ti
+ A 15at) A high magnetic flux density such that the amount of contamination can be suppressed to less than 20 ppm, the average value of B1° value exceeds 1.91, and iron loss value h + tzs. It is possible to industrially melt a silicon steel material that can easily produce grain-oriented silicon steel sheets with significantly reduced values.
同same
Claims (1)
Ｓｉを含有しかつ、Ｔｉ：０．０２０ｗｔ％以下及びＡ
ｌ：０．０５０ｗｔ％以下に抑制した成分組成のＦｅＳ
ｉ合金を添加し、取鍋内のスラグ成分を Ａｌ＿２Ｏ＿３：８ｗｔ％以下 ＴｉＯ＿２：０．５ｗｔ％以下でかつ ＣａＯ／ＳｉＯ＿２：０．６〜２．０ の範囲に調整することを特徴とするけい素鋼素材の溶製
方法。[Claims] 1. Molten steel for silicon steel contained in a ladle contains 70 to 80% Si, Ti: 0.020 wt% or less, and A
l: FeS with a component composition suppressed to 0.050 wt% or less
i-alloy is added, and the slag component in the ladle is adjusted to Al_2O_3: 8 wt% or less, TiO_2: 0.5 wt% or less, and CaO/SiO_2: 0.6 to 2.0. Method for melting steel materials.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP02222357A JP3105525B2 (en) | 1990-08-27 | 1990-08-27 | Melting method of silicon steel material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP02222357A JP3105525B2 (en) | 1990-08-27 | 1990-08-27 | Melting method of silicon steel material |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH04107239A true JPH04107239A (en) | 1992-04-08 |
| JP3105525B2 JP3105525B2 (en) | 2000-11-06 |
Family
ID=16781075
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP02222357A Expired - Fee Related JP3105525B2 (en) | 1990-08-27 | 1990-08-27 | Melting method of silicon steel material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3105525B2 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008260997A (en) * | 2007-04-11 | 2008-10-30 | Nippon Steel Corp | Desulfurization method of molten steel |
| JP2013527318A (en) * | 2010-06-23 | 2013-06-27 | 宝山鋼鉄股▲分▼有限公司 | Control method for ultra-low carbon, ultra-low Ti aluminum and silicon killed steel |
| CN111471827A (en) * | 2020-04-03 | 2020-07-31 | 湖南华菱涟源钢铁有限公司 | Method for controlling titanium content in smelted silicon steel to be less than or equal to 15ppm |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH08284379A (en) * | 1995-04-17 | 1996-10-29 | Matsukusuton Kk | Waterproofed combustible surface decorated mat |
-
1990
- 1990-08-27 JP JP02222357A patent/JP3105525B2/en not_active Expired - Fee Related
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008260997A (en) * | 2007-04-11 | 2008-10-30 | Nippon Steel Corp | Desulfurization method of molten steel |
| JP2013527318A (en) * | 2010-06-23 | 2013-06-27 | 宝山鋼鉄股▲分▼有限公司 | Control method for ultra-low carbon, ultra-low Ti aluminum and silicon killed steel |
| CN111471827A (en) * | 2020-04-03 | 2020-07-31 | 湖南华菱涟源钢铁有限公司 | Method for controlling titanium content in smelted silicon steel to be less than or equal to 15ppm |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3105525B2 (en) | 2000-11-06 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US7377986B2 (en) | Method for production of non-oriented electrical steel strip | |
| US5779819A (en) | Grain oriented electrical steel having high volume resistivity | |
| KR20120030140A (en) | Method for producing grain-oriented electromagnetic steel plate | |
| JP3550924B2 (en) | Method for manufacturing high carbon steel wire and wire | |
| KR100479992B1 (en) | A non-oriented steel sheet with excellent magnetic property and a method for producing it | |
| JPH04107239A (en) | Method for melting silicon steel stock | |
| JPS633007B2 (en) | ||
| JPH05140649A (en) | Manufacture of now-oriented silicon steel sheet excellent in magnetic property | |
| US3986902A (en) | Silicon steel suitable for production of oriented silicon steel using low slab reheat temperature | |
| JP2003286533A (en) | Processes for producing highly pure ferroboron, mother alloy for iron-based amorphous alloy and iron-based amorphous alloy | |
| JP3179530B2 (en) | Melting method of extremely low Ti steel | |
| JP4593313B2 (en) | Fe-Ni-based magnetic alloy plate excellent in hot workability and manufacturing method thereof | |
| JPH07122090B2 (en) | Method of melting directional silicon steel material | |
| JPS63195217A (en) | Nonoriented electrical steel sheet having small iron loss after magnetic annealing | |
| JP3456295B2 (en) | Melting method of steel for non-oriented electrical steel sheet | |
| JPH0463220A (en) | Method for refining silicon steel stock | |
| JPH0967654A (en) | Nonoriented silicon steel sheet excellent in core loss characteristics | |
| JP4256617B2 (en) | High purity ferroboron, master alloy for iron-based amorphous alloy, and method for producing iron-based amorphous alloy | |
| JP4218136B2 (en) | Non-oriented electrical steel sheet with high magnetic flux density and low iron loss and method for producing the same | |
| JP7413600B1 (en) | Fe-Ni alloy plate and its manufacturing method | |
| JP6989000B2 (en) | Manufacturing method of slab slab, which is a material for non-oriented electrical steel sheets | |
| JP4055252B2 (en) | Method for melting chromium-containing steel | |
| JPH0565524A (en) | Production of slab for grain oriented silicon steel | |
| JPH10212555A (en) | Nonoriented silicon steel sheet excellent in magnetic property and its production | |
| JP2002206144A (en) | Fe-Ni BASED ALLOY HAVING EXCELLENT SURFACE PROPERTY AND PRODUCTION METHOD THEREFOR |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20070901 Year of fee payment: 7 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20080901 Year of fee payment: 8 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20080901 Year of fee payment: 8 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20090901 Year of fee payment: 9 |
|
| LAPS | Cancellation because of no payment of annual fees |