JPH09268322A - Production of grain oriented silicon steel sheet with ultralow iron loss - Google Patents
Production of grain oriented silicon steel sheet with ultralow iron lossInfo
- Publication number
- JPH09268322A JPH09268322A JP8340045A JP34004596A JPH09268322A JP H09268322 A JPH09268322 A JP H09268322A JP 8340045 A JP8340045 A JP 8340045A JP 34004596 A JP34004596 A JP 34004596A JP H09268322 A JPH09268322 A JP H09268322A
- Authority
- JP
- Japan
- Prior art keywords
- steel sheet
- annealing
- iron loss
- rolling
- sheet
- Prior art date
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Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/147—Alloys characterised by their composition
- H01F1/14766—Fe-Si based alloys
- H01F1/14775—Fe-Si based alloys in the form of sheets
- H01F1/14783—Fe-Si based alloys in the form of sheets with insulating coating
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- Physics & Mathematics (AREA)
- Electromagnetism (AREA)
- Chemical & Material Sciences (AREA)
- Dispersion Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Power Engineering (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
- Soft Magnetic Materials (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、磁区制御を施した
方向性電磁鋼板に関するもので、特に歪み取り焼鈍を行
っても磁気特性の劣化しない、超低鉄損一方向性電磁鋼
板の製造方法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a grain-oriented electrical steel sheet subjected to magnetic domain control, and particularly to a method for producing an ultra-low iron loss grain-oriented electrical steel sheet in which magnetic properties do not deteriorate even when strain relief annealing is performed. It is about.
【０００２】[0002]
【従来の技術】一方向性電磁鋼板において、近年エネル
ギー節約の観点から鉄損を低減することが強く要望され
ている。鉄損を低減する方法としては高磁束密度化、二
次再結晶粒の小粒化等の冶金的方法の他に、物理的方法
としてレーザー照射やプラズマ照射等による磁区制御技
術が提案されている。（特開昭５７−２２５２号公報、
特開昭５９−２５９２８号公報）しかし、この方法では
歪取り焼鈍を必要とする巻き鉄心トランス用としては使
用できないため、積み、巻き両トランスに使用できる磁
区制御法として、製品の表面に歯型ロールで溝を形成す
る例えば特開昭６１−１１７２１８号公報、最終冷延板
にエッチングにより溝を形成する例えば特公平３−６９
９６８号公報或いは冷延板にレーザーにより溝を形成す
る例えば特開昭６１−７５５０６号公報等に開示された
技術がある。2. Description of the Related Art Recently, it has been strongly desired to reduce iron loss in a grain-oriented electrical steel sheet from the viewpoint of energy saving. As a method for reducing iron loss, a magnetic domain control technique by laser irradiation, plasma irradiation, or the like has been proposed as a physical method, in addition to a metallurgical method such as increasing the magnetic flux density and reducing secondary recrystallized grains. (JP-A-57-2252,
However, since this method cannot be used for a wound iron core transformer that requires strain relief annealing, it is a magnetic domain control method that can be used for both stacking and winding transformers, and therefore a tooth mold on the surface of a product is used. A groove is formed by a roll, for example, JP-A-61-117218, and a groove is formed in a final cold-rolled sheet by etching.
There is a technique disclosed in Japanese Patent No. 968 or in Japanese Patent Laid-Open No. 61-75506, for example, in which grooves are formed on a cold-rolled sheet by laser.
【０００３】この他の鉄損低減方法として、鋼板の表面
を電解研磨又は化学研磨により平滑（鏡面）にする方法
がある（特公昭５２−２４４９９号公報、特公昭５６−
４１５０号公報）。最近では、この鏡面を得る方法とし
て焼鈍分離剤にＡｌ2 Ｏ3 等を用いる方法或いはＭｇＯ
中に塩素化合物等の添加物を添加する方法等が提案され
ている。As another iron loss reduction method, there is a method of making the surface of a steel sheet smooth (mirror surface) by electrolytic polishing or chemical polishing (Japanese Patent Publication No. 52-24499 and Japanese Patent Publication No. 56-56).
No. 4150). Recently, as a method for obtaining this mirror surface, a method using Al 2 O 3 or the like as an annealing separator or MgO is used.
There has been proposed a method of adding an additive such as a chlorine compound therein.
【０００４】特願平４−２１４５１号公報および特開平
４−２１４５２号公報には、この鏡面を有した鋼板に歪
取り焼鈍に耐える磁区制御をし、かつ張力コーティング
を施すことによって超低鉄損材を得る方法を提案してい
る。しかし、これまでに提案されている歪取り焼鈍に耐
える磁区制御法は、鋼板の形状不良や穿孔部のバリの生
成或いはコストの上昇等の問題を抱えており今後の改善
が待たれる。本出願人は、先に特願平０７−２０２３５
１号にて、この改善策の一つとして冷延の途中板厚段階
で溝を形成してから製品板厚に仕上げる一連の工程での
中で磁区制御処理を行う方法を提案した。In Japanese Patent Application No. 4-214551 and Japanese Patent Application Laid-Open No. 4-215252, ultra-low iron loss is achieved by controlling the magnetic domain of a steel plate having this mirror surface to withstand strain relief annealing and applying a tension coating. We are proposing a method of obtaining lumber. However, the magnetic domain control methods that have been proposed so far to withstand the strain relief annealing have problems such as a defective shape of the steel sheet, the formation of burrs in the perforated portion, and an increase in cost, and therefore further improvement is awaited. The present applicant has previously filed Japanese Patent Application No. 07-20235.
In No. 1, as one of the improvement measures, a method of performing magnetic domain control treatment in a series of steps of forming grooves in the plate thickness stage during cold rolling and then finishing the product plate thickness was proposed.
【０００５】[0005]
【発明が解決しようとする課題】本発明は、鋼板形状の
優れた歪み取り焼鈍をしても磁区細分化効果を消失しな
い超低鉄損一方向性電磁鋼板の製造方法を提案するもの
である。DISCLOSURE OF THE INVENTION The present invention proposes a method for producing an ultra-low iron loss unidirectional electrical steel sheet which does not lose the magnetic domain refining effect even if the steel sheet shape is subjected to strain relief annealing. .
【０００６】[0006]
【課題を解決するための手段】本発明の要旨は以下のと
おりである。 （１）重量比で、Ｓｉ：２．５〜４．５％、Ｃ：０．０
８５％以下、Ｍｎ：０．０５０〜０．４５％、Ｓ≦０．
０１５％、酸可溶性Ａｌ：０．０１０〜０．０４０％、
Ｎ：≦０．０１０％、Ｓｎ：０．０２〜０．１５％、残
部Ｆｅ及び不可避的不純物からなる電磁鋼スラブを１２
８０℃以下の温度で加熱した後、熱延し、熱延板焼鈍を
し、一回または中間焼鈍を介挿する二回以上の圧延でそ
の最終圧延率を８０％以上とし、次いで脱炭焼鈍、窒化
処理、焼鈍分離剤を塗布し、仕上げ焼鈍をする一方向性
電磁鋼板の製造において、その最終冷延の途中板厚段階
で鋼板表面に圧延方向に対して、９０°〜４５°の範囲
で幅が１０〜５００μｍ、深さが板厚ｔ×１／８〜ｔ×
１／３０、間隔が圧延方向に１〜２０mmの溝を点状ある
いは線状に形成した後、最終板厚まで圧延することを特
徴とし、焼鈍分離剤としてＡｌ2 Ｏ3 を塗布し、仕上げ
焼鈍後、張力コーティングを施すフォルステライト皮膜
を有しない超低鉄損方向性電磁鋼板の製造方法。 （２）レーザー光により、鋼板表面に圧延方向にたいし
て９０°から４５°の範囲で幅が１０から５００μｍ、
深さが板厚ｔ×１／８〜ｔ×１／３０、間隔が圧延方向
に１〜２０mmの溝を点状或いは線状に形成し、次いで溝
形成後に生じた溶融付着物を機械的方法で除去した後、
最終板厚まで圧延する（１）記載のフォルステライト皮
膜を有しない超低鉄損方向性電磁鋼板の製造方法。 （３）最終板厚の冷延板を脱炭焼鈍前に軽酸洗を施す
（１）または（２）記載のフォルステライト皮膜を有し
ない超低鉄損方向性電磁鋼板の製造方法。 （４）焼鈍分離剤としてＭｇＯ：１００重量部に対し、
Ｃａ，Ｍｇ，Ｂｉの塩化物から選ばれる１種又は２種以
上を合計で２〜３０重量部添加した焼鈍分離剤を塗布す
る（１），（２）または（３）記載のフォルステライト
被膜を有しない超低鉄損方向性電磁鋼板の製造方法。The gist of the present invention is as follows. (1) In weight ratio, Si: 2.5-4.5%, C: 0.0
85% or less, Mn: 0.050 to 0.45%, S ≦ 0.
015%, acid-soluble Al: 0.010 to 0.040%,
N: ≦ 0.010%, Sn: 0.02 to 0.15%, 12 magnetic steel slabs consisting of balance Fe and unavoidable impurities
After heating at a temperature of 80 ° C or lower, hot rolling, hot-rolled sheet annealing, and final rolling rate of 80% or more are performed once or twice or more with intermediate annealing interposed, and then decarburization annealing. , Nitriding treatment, applying an annealing separator, and finishing annealing, in the production of a unidirectional electrical steel sheet, the range of 90 ° to 45 ° with respect to the rolling direction on the steel sheet surface in the final thickness stage of the cold rolling. Width is 10 to 500 μm, depth is plate thickness t × 1/8 to t ×
It is characterized in that after forming grooves in the form of dots or lines with a distance of 1/30 in the rolling direction of 1 to 30 mm, rolling is carried out to the final plate thickness, Al 2 O 3 is applied as an annealing separator, and finish annealing is performed. After that, a method for producing an ultra-low iron loss grain-oriented electrical steel sheet having no forsterite film to be tension-coated. (2) With a laser beam, the width of the steel sheet surface is 10 to 500 μm in the range of 90 ° to 45 ° in the rolling direction,
Grooves having a depth of t x 1/8 to t x 1/30 and an interval of 1 to 20 mm in the rolling direction are formed in a dot shape or a linear shape, and then a molten deposit formed after the groove formation is mechanically processed. After removing with
A method for producing an ultra-low iron loss grain-oriented electrical steel sheet having no forsterite coating according to (1), which is rolled to a final sheet thickness. (3) The method for producing an ultra-low iron loss grain-oriented electrical steel sheet having no forsterite coating according to (1) or (2), wherein the cold-rolled sheet having the final sheet thickness is lightly pickled before decarburization annealing. (4) As an annealing separator, MgO: 100 parts by weight,
The forsterite coating described in (1), (2) or (3) is applied by applying an annealing separator containing a total of 2 to 30 parts by weight of one or more selected from chlorides of Ca, Mg and Bi. A method for manufacturing an ultra-low iron loss grain-oriented electrical steel sheet that does not have.
【０００７】[0007]
【発明の実施の形態】以下、本発明を実験に基づいて説
明する。 （実験１）重量比で、Ｃ：０．０５５％、Ｓｉ：３．５
０％、Ｍｎ：０．１０％、Ｐ：０．０２５％、Ｓ：０．
００７％、酸可溶性Ａｌ：０．０３０％、Ｓｎ：０．０
７％、Ｃｒ：０．１２％、Ｎ：０．００７５％を含む電
磁鋼熱延鋼板を１１２０℃に加熱後、冷却し、次いで９
００℃に短時間保定する焼鈍を施した後急冷し、酸洗し
冷延を行った。この冷延の板厚途中段階においてレーザ
ー光により深さを５段階に変えて穿孔した。DESCRIPTION OF THE PREFERRED EMBODIMENTS The present invention will be described below based on experiments. (Experiment 1) C: 0.055%, Si: 3.5 by weight ratio
0%, Mn: 0.10%, P: 0.025%, S: 0.
007%, acid-soluble Al: 0.030%, Sn: 0.0
A magnetic steel hot-rolled steel sheet containing 7%, Cr: 0.12% and N: 0.0075% is heated to 1120 ° C., then cooled, and then 9
It was annealed by holding it at 00 ° C for a short time, then rapidly cooled, pickled and cold rolled. In the middle of the plate thickness of this cold rolling, the depth was changed to 5 steps by laser light and punching was performed.
【０００８】 ───────────────────────────────── レーザー照射板厚（mm） 穿孔深さ（μｍ） ───────────────────────────────── ０．３０ ７、１０、３０、３７、４３ ───────────────────────────────── 穿孔はほぼ幅１００μｍ、間隔１００μｍの点列とし、
点列の方向は圧延方向に対して７０°とし、点列のピッ
チは４mmとした。───────────────────────────────── Laser irradiation plate thickness (mm) Perforation depth (μm) ─ ──────────────────────────────── 0.30 7, 10, 30, 37, 43 ────── ─────────────────────────── The perforations are approximately 100 μm wide and spaced 100 μm apart.
The direction of the dot array was 70 ° with respect to the rolling direction, and the pitch of the dot array was 4 mm.
【０００９】この後最終板厚０．２３mmまで冷延して仕
上げた。この後油洗し脱炭焼鈍を８３０℃×３０秒、Ｈ
2 ：７５％＋Ｎ2 ：２５％、露点４０℃の雰囲気中で行
った。次いで窒化処理を７５０℃×３０秒、Ｈ2 ，Ｎ
2 ，アンモニアの混合ガス中で行い、鋼板の窒素量を２
００ppm に調整し、焼鈍分離剤にＡｌ2 Ｏ3 を使用し、
仕上げ焼鈍昇温過程の雰囲気ガスをＮ2 ：９０％＋Ｈ
2 ：１０％の混合ガスで行ない、１２００℃×２０時間
の純化焼鈍をＨ2 雰囲気ガス中で行なった。この後水洗
し、無水クロム酸、燐酸アルミニュウムを主成分とする
張力焼鈍を施した。この実験で得られた製品の磁気特性
を図１に示す。After that, the product was finished by cold rolling to a final plate thickness of 0.23 mm. This is followed by an oil wash and decarburization annealing at 830 ° C for 30 seconds, H
It was carried out in an atmosphere of 2 : 75% + N 2 : 25% and a dew point of 40 ° C. Next, nitriding treatment is performed at 750 ° C. for 30 seconds, H 2 , N
2. Conducted in a mixed gas of ammonia and set the nitrogen content of the steel plate to 2
Adjusted to 00ppm, using Al 2 O 3 as an annealing separator,
Atmosphere gas of finish annealing temperature rising process is N 2 : 90% + H
2 : 10% mixed gas was used, and purification annealing was performed at 1200 ° C. for 20 hours in a H 2 atmosphere gas. After that, it was washed with water and subjected to tension annealing mainly containing chromic anhydride and aluminum phosphate. The magnetic properties of the product obtained in this experiment are shown in FIG.
【００１０】この図１から、穿孔深さ１０〜３７μｍの
範囲で０．７５Ｗ／kg（Ｗ17/50 ）を下廻る超低鉄損が
得られた。これはレーザー照射時の板厚の１／３０〜１
／８である。 （実験２）実験１で使用した途中板厚段階の穿孔深さ２
０μｍの冷延板を０．２３mmに冷延し脱炭焼鈍板を行っ
た。この材料を用いて以下の３種類の焼鈍分離剤を用い
て磁気特性と板表面状態の検討を行った。From FIG. 1, an ultra-low iron loss of less than 0.75 W / kg (W 17/50 ) was obtained in the range of the depth of drilling from 10 to 37 μm. This is 1/30 to 1 of the plate thickness during laser irradiation
/ 8. (Experiment 2) Perforation depth 2 in the mid-thickness stage used in Experiment 1
A 0 μm cold-rolled sheet was cold-rolled to 0.23 mm and a decarburized annealed sheet was performed. Using this material, the following three types of annealing separators were used to study the magnetic properties and plate surface state.
【００１１】 ＭｇＯ：１００部＋ＴｉＯ2 ：５部＋
Ｎａ2 Ｂ4 Ｏ7 ：０．３部 ＭｇＯ：１００部＋ＣａＣｌ2 ：７部 ＭｇＯ：１００部＋ＢｉＣｌ：２部 上記焼鈍分離剤を塗布した後、Ｎ2 ：５０％＋Ｈ2 ：５
０％の雰囲気中で１２００℃×２０時間の仕上げ焼鈍を
行った。この後、無水クロム酸と燐酸アルミニウムを主
成分とするコーティング液を塗布して、８５０℃×２分
間の焼き付け焼鈍を行った。この結果を次に示す。MgO: 100 parts + TiO 2 : 5 parts +
Na 2 B 4 O 7 : 0.3 parts MgO: 100 parts + CaCl 2 : 7 parts MgO: 100 parts + BiCl: 2 parts After applying the above annealing separator, N 2 : 50% + H 2 : 5
Finish annealing was performed at 1200 ° C. for 20 hours in a 0% atmosphere. After that, a coating liquid containing chromic anhydride and aluminum phosphate as main components was applied, and baking and annealing was performed at 850 ° C. for 2 minutes. The results are shown below.
【００１２】 ────────────────────────────────── 焼鈍分離剤 磁 気 特 性 板表面状態 Ｂ８（Ｔ） Ｗ17/50 （Ｗ／kg） ────────────────────────────────── １．９２ ０．７５ フォルステライト形成 １．９４ ０．７１ フォルステライト無し １．９４ ０．７０ フォルステライト無し ────────────────────────────────── 上記結果から分るように、焼鈍分離剤に塩素化合物を添
加した材料で鉄損の非常に低い超低鉄損材が得られた。────────────────────────────────── Annealing agent Magnetic property Plate surface state B8 (T ) W 17/50 (W / kg) ────────────────────────────────── 1.92 0.75 Forsterite formation 1.94 0.71 Without forsterite 1.94 0.70 Without forsterite ────────────────────────────── ───── As can be seen from the above results, an ultra-low iron loss material with a very low iron loss was obtained from a material in which a chlorine compound was added to the annealing separator.
【００１３】本発明において、出発材料の成分組成の限
定理由は以下の通りである。Ｓｉは、低鉄損を得る上で
多い方が好ましいが、Ｓｉの含有量が４．５％を超える
と材料の冷間圧延時に、割れ、破断が多発し、安定した
冷延作業を不可能にする。Ｃは、０．０８５％を超える
と、脱炭焼鈍時間が長大なものとなり、生産性を損な
う。Ｍｎは、その含有量が少なすぎると二次再結晶が不
安定となり、一方、多すぎると高い磁束密度をもつ製品
を得難くなる。適正な含有量は、０．０５０〜０．４５
％である。Ｓは、周知の如くＭｎＳを形成し、一次再結
晶粒の成長を抑制する。本発明においては二次再結晶粒
を発現させるに必要なインヒビターは脱炭焼鈍以降で造
り込むことを特徴としており、冷延以前で微細な析出物
が分散することは一次再結晶粒径を調整して高磁束密度
鋼板を得る本発明においては好ましくない。従って、Ｓ
は０．０１５％以下としている。好ましくは０．０１０
％以下が良い。In the present invention, the reasons for limiting the component composition of the starting material are as follows. Si is preferably large in order to obtain low iron loss, but if the Si content exceeds 4.5%, cracks and fractures frequently occur during cold rolling of the material, making stable cold rolling work impossible. To If C exceeds 0.085%, the decarburization annealing time becomes long and the productivity is impaired. If the content of Mn is too small, secondary recrystallization becomes unstable, while if it is too large, it becomes difficult to obtain a product having a high magnetic flux density. The appropriate content is 0.050 to 0.45
%. S forms MnS as is well known, and suppresses the growth of primary recrystallized grains. In the present invention, the inhibitor required to develop secondary recrystallized grains is characterized in that it is built after decarburization annealing, and that fine precipitates are dispersed before cold rolling adjusts the primary recrystallized grain size. It is not preferable in the present invention to obtain a high magnetic flux density steel sheet. Therefore, S
Is set to 0.015% or less. Preferably 0.010
% Or less is good.
【００１４】Ａｌは窒素と結合してＡｌＮを形成する
が、本発明においては、後工程、即ち一次再結晶完了に
鋼を窒化することにより、（Ａｌ，Ｓｉ）Ｎを形成せし
めることを必須としているから、フリーのＡｌが一定量
以上必要である。そのため、酸可溶性Ａｌとして、０．
０１０〜０．０４０％とする。Ｎは０．０１０％以下に
する必要がある。０．０１０％を超えるとブリスターと
呼ばれる鋼板表面の膨れが発生し、また一次再結晶組織
の調整が困難になる。下限は特に限定しないが０．００
２％程度が良い。Al combines with nitrogen to form AlN. In the present invention, it is essential to form (Al, Si) N by nitriding the steel in the subsequent step, that is, the completion of primary recrystallization. Therefore, a certain amount of free Al is required. Therefore, as acid-soluble Al, 0.1.
010 to 0.040%. N needs to be 0.010% or less. If it exceeds 0.010%, blistering of the steel sheet surface called blister occurs, and it is difficult to adjust the primary recrystallization structure. The lower limit is not particularly limited, but is 0.00
About 2% is good.
【００１５】Ｓｎは脱炭焼鈍後の集合組織を改善し、ひ
いては二次再結晶粒を改善し皮膜の安定化と相俟って鉄
損改善に効果が大きい。Ｓｎの適量は０．０２〜０．１
５％であるが、これより少ないと鉄損改善効果が弱く、
一方、多いと窒化が困難になり二次再結晶粒が発達しに
くくなる。好ましくは０．０３〜０．１０％が良い。な
お、微量のＣｕ，Ｐ，Ｔｉを鋼中に含有せしめること
は、本発明の主旨を損なうものではない。Sn improves the texture after decarburization annealing and, by extension, improves secondary recrystallized grains and, in combination with the stabilization of the coating, has a great effect on improving iron loss. Suitable amount of Sn is 0.02-0.1
It is 5%, but if it is less than this, the iron loss improving effect is weak,
On the other hand, if the amount is large, nitriding becomes difficult and secondary recrystallized grains are hard to develop. Preferably, 0.03 to 0.10% is good. The inclusion of trace amounts of Cu, P, and Ti in steel does not impair the gist of the present invention.
【００１６】次に、本発明の製造プロセスについて説明
する。電磁鋼スラブは、転炉或いは電気炉等の溶解炉で
鋼を溶製し、必要に応じて真空脱ガス処理し、次いで連
続鋳造によって、或いは造塊後分塊圧延することによっ
て得られ、しかる後、熱間圧延に先立つスラブ加熱がな
される。スラブ加熱温度は１２８０℃以下の低い温度で
行うことにより加熱エネルギーの消費量を少なくすると
ともに、鋼中のＡｌＮを完全には固溶させず不完全固溶
状態とする。Next, the manufacturing process of the present invention will be described. Electromagnetic steel slabs are obtained by melting steel in a melting furnace such as a converter or an electric furnace, subjecting it to vacuum degassing treatment if necessary, and then by continuous casting or by slabbing after ingot making. After that, slab heating is performed prior to hot rolling. By performing the slab heating at a low temperature of 1280 ° C. or less, the consumption of the heating energy is reduced, and the AlN in the steel is not completely dissolved to form an incomplete solid solution state.
【００１７】このスラブを熱延して所定の厚みの熱延板
を得、次いで、９００℃〜１１５０℃で短時間の熱延板
焼鈍と、それに引続き冷間を行う。冷間圧延の圧延率
は、高磁束密度鋼板を得る上から８０％以上必要であ
る。次に、本発明においては冷間圧延途中の最終板厚と
なる前段階で、穿孔処理を行う。The slab is hot-rolled to obtain a hot-rolled sheet having a predetermined thickness, and then hot-rolled sheet annealing is performed at 900 ° C to 1150 ° C for a short period of time, followed by cold working. The rolling ratio of cold rolling is required to be 80% or more in order to obtain a high magnetic flux density steel plate. Next, in the present invention, a piercing process is performed before the final plate thickness during cold rolling.
【００１８】以下に、穿孔処理の条件について述べる。
穿孔（溝）の幅は１０〜５００μｍとする。５００μｍ
を超すと磁束密度の劣化が大きくなり、鉄損低減効果が
認められない。一方、１０μｍより狭くすることは非常
に難しい。溝の方向は圧延方向に対して９０°〜４５°
とする。４５°より小さくなると、磁区細分化効果が弱
くなり鉄損低減が小さい。溝の間隔は１〜２０mmとす
る。１mm未満は工業的に難しく、一方、２０mmを超える
と鉄損低減が小さくなる。点状の穿孔の場合、穿孔の間
隔は特に拘らないが、磁区は幅の最も広いもので２mm程
度であることから、これを超すことは好ましくない。溝
深さは溝形成時の板厚の１／３０〜１／８の範囲が良
い。１／３０より浅いと鉄損低減が弱く、１／８より深
いと磁束密度の劣化を招き鉄損特性も悪くなる。The conditions for the punching process will be described below.
The width of the perforations (grooves) is 10 to 500 μm. 500 μm
If it exceeds, the deterioration of the magnetic flux density will increase and the iron loss reduction effect will not be recognized. On the other hand, it is very difficult to make it smaller than 10 μm. The groove direction is 90 ° to 45 ° with respect to the rolling direction
And When the angle is smaller than 45 °, the effect of subdividing the magnetic domain is weakened, and the iron loss reduction is small. The interval between the grooves is 1 to 20 mm. If it is less than 1 mm, it is industrially difficult, while if it exceeds 20 mm, the reduction of iron loss becomes small. In the case of point-like perforations, the interval between the perforations is not particularly limited, but the magnetic domain having the widest width is about 2 mm, so it is not preferable to exceed this. The groove depth is preferably in the range of 1/30 to 1/8 of the plate thickness at the time of forming the groove. If it is shallower than 1/30, the reduction of iron loss is weak, and if it is deeper than 1/8, the magnetic flux density is deteriorated and the iron loss characteristics are also deteriorated.
【００１９】この溝形成にはレーザー光或いはプラズマ
炎を用いると効果的であるが、この他高圧水を用いても
良い。この後製品板厚まで圧延する。この圧延は溝形成
時に生じた形成不良やバリを除去すると同時に、熱影響
部の組織を改善し、磁区制御効果に加えてＧｏｓｓ組織
の発達を製品板厚で照射した場合に比較して更に促進す
る効果がある。この理由は定かでないが、熱影響部の組
織に圧延により歪が導入され、その歪量がＧｏｓｓ組織
の発達に適したものとなっていると推定される。溝形成
にレーザー光を用いる場合、溝周辺に鋼の溶融物が付着
するが、追加圧延によってこの大部分は除去されるもの
の、一部は表面の肌荒れ、或いは板厚精度の低下の原因
となり、商品価値に影響を及ぼしてくる。レーザー照射
後にこの溶融物を例えばブラシ、砥石、ワイパー、圧搾
空気、高圧水等、機械的方法で除去すると、上記欠陥が
解消され優れた製品を得ることが出来る。加えて、最終
板厚の冷延板を硝酸、硫酸、塩酸水等で軽酸洗処理を施
すことは溝内の付着物を除去するのに効果がある。It is effective to use laser light or plasma flame for forming the groove, but high pressure water may be used in addition to this. After that, it is rolled to the product thickness. This rolling eliminates formation defects and burrs generated during groove formation, improves the structure of the heat affected zone, and further promotes the development of the Goss structure in addition to the magnetic domain control effect as compared to the case where irradiation is performed at the product thickness. Has the effect of doing Although the reason for this is not clear, it is presumed that strain is introduced into the structure of the heat-affected zone by rolling, and the amount of strain is suitable for the development of the Goss structure. When using a laser beam for groove formation, the melt of steel adheres to the periphery of the groove, but although most of this is removed by additional rolling, part of it causes rough surface or a decrease in plate thickness accuracy, It will affect the product value. When the melt is removed by a mechanical method such as a brush, a grindstone, a wiper, compressed air, or high-pressure water after the laser irradiation, the above defects can be eliminated and an excellent product can be obtained. In addition, light pickling of the cold-rolled plate having the final plate thickness with nitric acid, sulfuric acid, hydrochloric acid water or the like is effective in removing the deposits in the groove.
【００２０】上述の処理に引続き、脱炭焼鈍と窒化処理
を行う。脱炭焼鈍は公知の方法で行うことが可能であ
り、窒化処理は例えば特開平２−７７５２５号公報に示
されるような、水素、窒素、アンモニアの混合ガス中で
ストリップを走行して行う。焼鈍分離剤にはフォルステ
ライト皮膜を形成させないものを使用する必要がある。
このためにＡｌ2 Ｏ3 の使用或いはＭｇＯにＣａ，Ｍ
ｇ，Ｂｉの塩化物から選ばれる１種又は２種以上を合計
で２〜３０重量部添加した焼鈍分離剤を塗布する必要が
ある。Subsequent to the above treatment, decarburization annealing and nitriding treatment are performed. The decarburization annealing can be performed by a known method, and the nitriding treatment is performed by running the strip in a mixed gas of hydrogen, nitrogen and ammonia as shown in JP-A-2-77525. It is necessary to use an annealing separator that does not form a forsterite film.
For this purpose, use of Al 2 O 3 or Ca, M in MgO
It is necessary to apply an annealing separator containing 2 to 30 parts by weight in total of one or more selected from chlorides of g and Bi.
【００２１】この塩化物の添加は２重量部より少ないと
フォルステライト皮膜が形成され、一方、３０重量部を
超えても効果は変わらない。仕上げ焼鈍は公知の方法で
行う。この後、張力皮膜を形成させるが、張力皮膜とし
ては、例えば特開昭４８−３９３３８号公報によるコロ
イド状シリカと燐酸アルミニウムを主体とするコーティ
ング液、特開昭５０−７９４４２号公報によるコロイド
状シリカと燐酸マグネシウムを主体とするコーティング
液、または特願平４−２２２８４９号公報によるアルミ
ナ・ゾルとほう酸を主成分とするコーティング液を焼き
付ける方法等を採用すればよい。If the amount of this chloride added is less than 2 parts by weight, a forsterite film is formed, while if it exceeds 30 parts by weight, the effect remains unchanged. The finish annealing is performed by a known method. After that, a tension film is formed. Examples of the tension film include colloidal silica disclosed in JP-A-48-39338 and a coating liquid mainly containing aluminum phosphate, and colloidal silica disclosed in JP-A-50-79442. And a coating solution containing magnesium phosphate as a main component, or a method of baking a coating liquid containing alumina sol and boric acid as main components according to Japanese Patent Application No. 4-222849 may be employed.
【００２２】[0022]
＜実施例１＞重量比で、Ｃ：０．０５３％、Ｓｉ：３．
２５％、Ｍｎ：０．１０％、Ｐ：０．０２０％、Ｓ：
０．００７％、酸可溶性Ａｌ：０．０２８％、Ｓｎ：
０．０５％、Ｃｒ：０．１２％、Ｎ：０．００７８％を
含む電磁鋼熱延鋼板を１１２０℃に加熱後冷却し、次い
で９００℃に短時間保定する焼鈍を施した後急冷し、酸
洗し冷延を行った。この冷延の板厚途中段階においてレ
ーザー光により４段階に深さを変えて穿孔した。<Example 1> C: 0.053%, Si: 3.
25%, Mn: 0.10%, P: 0.020%, S:
0.007%, acid-soluble Al: 0.028%, Sn:
An electromagnetic steel hot-rolled steel sheet containing 0.05%, Cr: 0.12% and N: 0.0078% was heated to 1120 ° C., then cooled, then annealed at 900 ° C. for a short time, and then rapidly cooled, It was pickled and cold rolled. In the middle of the plate thickness of this cold rolling, the depth was changed in four steps by laser light for perforation.
【００２３】 ──────────────────────────────── レーザー照射板厚（mm） 穿孔深さ（μｍ） ──────────────────────────────── ０．３４ 照射なし、８、３０、４４ ──────────────────────────────── 穿孔（溝）の幅はほぼ７０μｍ、間隔１００μｍの点列
とし、点列の方向は圧延方向に対して７０°とし、点列
のピッチは４mmとした。──────────────────────────────── Laser irradiation plate thickness (mm) Perforation depth (μm) ── ────────────────────────────── 0.34 No irradiation, 8, 30, 44 ────────── ─────────────────────── The width of the perforations (grooves) is approximately 70 μm and the spacing is 100 μm. The pitch was 70 ° and the pitch of the dot train was 4 mm.
【００２４】この後最終板厚０．２７mmまで冷延して仕
上げた。この後油洗し脱炭焼鈍を８３０℃×３０秒、Ｈ
2 ：７５％＋Ｎ2 ：２５％、露点４０℃の雰囲気中で行
った。次いで窒化処理を７５０℃×３０秒、Ｈ2 、Ｎ
2 、アンモニアの混合ガス中で行い、鋼板の窒素量を２
００ppm に調整し、焼鈍分離剤にＡｌ2 Ｏ3 を使用し、
１２００℃×２０時間の仕上げ焼鈍を昇温過程は窒素雰
囲気中で、均熱時は水素雰囲気中で行った。この後水洗
し、無水クロム酸、燐酸アルミニュウムを主成分とする
張力コーテングを施した。得られた磁気特性を次に示
す。After this, the product was finished by cold rolling to a final plate thickness of 0.27 mm. After this, wash with oil and decarburize annealing at 830 ° C for 30 seconds
It was carried out in an atmosphere of 2 : 75% + N 2 : 25% and a dew point of 40 ° C. Next, nitriding treatment is performed at 750 ° C. for 30 seconds, H 2 , N
2. Conducted in a mixed gas of ammonia and set the nitrogen content of the steel plate to 2
Adjusted to 00ppm, using Al 2 O 3 as an annealing separator,
Final annealing at 1200 ° C. for 20 hours was performed in a nitrogen atmosphere during the temperature rising process and in a hydrogen atmosphere during soaking. After that, it was washed with water and subjected to tension coating containing chromic anhydride and aluminum phosphate as main components. The magnetic properties obtained are shown below.
【００２５】 ──────────────────────────────── 試料（溝深さμｍ） Ｂ８（Ｔ） Ｗ17/50 （Ｗ／kg） ──────────────────────────────── 照射なし １．９５ ０．９０ ８ １．９４ ０．８７ ２０ １．９４ ０．７８ ４４ １．９２ ０．８６ ──────────────────────────────── 上記結果から分るように本発明の範囲で低超鉄損が得ら
れた。 ＜実施例２＞重量比で、Ｃ：０．０５６％，Ｓｉ：３．
３％，Ｍｎ：０．１０％，Ｐ：０．０２５％，Ｓ：０．
００７％，酸可溶性Ａｌ：０．０２７％，Ｓｎ：０．０
５％，Ｃｒ：０．０８％，Ｎ：０．００８０％を含む電
磁鋼スラブを熱延し、板厚２．３mmとした。次いでこの
熱延板を１１２０℃で加熱後、冷却し９００℃で短時間
保定する焼鈍を施した後急冷し、酸洗し、冷延をおこな
った。この冷延途中板厚段階の０．３０mmでレーザー光
により溝を圧延方向と９０°方向に形成した。溝の幅は
ほぼ１００μｍ、深さ約１８μｍ、圧延方向の溝のピッ
チは４mmとした。この後、１つはこのままの状態で、他
の１つは溝部の溶融付着物をサンドベルトで除去した後
いずれも０．２３mmまで冷延した。この後油洗し、脱炭
焼鈍を８３０℃で行った後窒化処理を７５０℃ｘ３０
秒、Ｈ2 ，Ｎ2 、アンモニアの混合ガス中で行い、窒素
量をほぼ２００ppm に調整した。この後焼鈍分離剤にＡ
ｌ2 Ｏ3 を塗布し、１２００℃ｘ２０時間の仕上焼鈍を
行った。この焼鈍の昇温過程の雰囲気ガスはＨ2 ：１０
％＋Ｎ2 ：９０％の混合ガスとし、純化はＨ2 ガスとし
た。この後水洗し、無水クロム酸、リン酸アルミニュウ
ムを主成分とする張力コーティングを施した。得られた
特性を表１に示す。──────────────────────────────── Sample (groove depth μm) B8 (T) W 17/50 (W / kg) ──────────────────────────────── No irradiation 1.95 0.90 8 1.940 .87 20 1.94 0.78 44 1.92 0.86 ──────────────────────────────── Above results As can be seen from the above, low super-iron loss was obtained within the range of the present invention. <Example 2> C: 0.056%, Si: 3.
3%, Mn: 0.10%, P: 0.025%, S: 0.
007%, acid-soluble Al: 0.027%, Sn: 0.0
An electromagnetic steel slab containing 5%, Cr: 0.08%, N: 0.0080% was hot-rolled to a plate thickness of 2.3 mm. Next, this hot-rolled sheet was heated at 1120 ° C., cooled, annealed at 900 ° C. for a short time, then rapidly cooled, pickled, and cold-rolled. Grooves were formed in the 90 ° direction with the rolling direction by laser light at a plate thickness of 0.30 mm during the cold rolling. The groove width was about 100 μm, the depth was about 18 μm, and the groove pitch in the rolling direction was 4 mm. After this, one was left as it was, and the other was cold-rolled to 0.23 mm after removing the molten deposits in the grooves with a sand belt. After that, it was washed with oil, decarburized and annealed at 830 ° C., and then nitrided at 750 ° C. × 30.
Second, in a mixed gas of H 2 , N 2 and ammonia, the nitrogen amount was adjusted to about 200 ppm. After this, the annealing separator was
l 2 O 3 was applied and finish annealing was performed at 1200 ° C. for 20 hours. The atmosphere gas in the temperature rising process of this annealing is H 2 : 10.
% + N 2 : A mixed gas of 90% was used, and H 2 gas was used for purification. After that, it was washed with water and subjected to tension coating mainly containing chromic anhydride and aluminum phosphate. The obtained characteristics are shown in Table 1.
【表１】 このように、溝部の研磨を行うと鉄損、板厚精度とも改
善されることが分かる。 ＜実施例３＞重量比で、Ｃ：０．０５２％，Ｓｉ：３．
２５％，Ｍｎ：０．１０％，Ｐ：０．０２５％，Ｓ：
０．００７％，酸可溶性Ａｌ：０．０２６％，Ｓｎ：
０．０７％，Ｃｒ：０．１２％，Ｎ：０．００７８％を
含む電磁鋼スラブを１１５０℃で熱延し、板厚１．８mm
とし、次いで１１２０℃で加熱後、冷却し９００℃で短
時間保定する焼鈍を施した後急冷し、酸洗し、冷延をお
こなった。この冷延の板厚途中段階の０．２５mmでレー
ザー光により溝を圧延方向と７５°方向に形成した。溝
の幅は、ほぼ１００μｍ、深さ約１５μｍ、圧延方向の
溝のピッチは４mmとした。更に、溝部の溶融付着物をサ
ンドベルトで除去した後、０．１７mmまで冷延した。こ
の後、３０％硝酸水で短時間酸洗し、脱炭焼鈍を８３０
℃で行った後、窒化処理を７５０℃ｘ３０秒、Ｈ2 ，Ｎ
2 、アンモニアの混合ガス中で行い、窒素量を２００pp
m に調整した。この後、焼鈍分離剤に次の条件のものを
使用した。 ＭｇＯ＋ＣａＣｌ2 （７％） ＭｇＯ＋ＢｉＣｌ3 （３％） ＭｇＯ＋ＭｇＣｌ2 （７％） ＭｇＯのみ（比較） この後、１２００℃ｘ２０時間の仕上焼鈍を行った。こ
の焼鈍の昇温過程の雰囲気ガスはＨ2 ：２５％＋Ｎ2 ：
７５％の混合ガスとし、純化はＨ2 ガスとした。この後
水洗し、無水クロム酸、リンサンアルミニュウムを主成
分とする張力焼鈍を施した。得られた特性を表２に示
す。[Table 1] As described above, it is understood that the iron loss and the plate thickness accuracy are improved by polishing the groove portion. <Example 3> C: 0.052%, Si: 3.
25%, Mn: 0.10%, P: 0.025%, S:
0.007%, acid-soluble Al: 0.026%, Sn:
Electromagnetic steel slab containing 0.07%, Cr: 0.12%, N: 0.0078% is hot-rolled at 1150 ° C to obtain a plate thickness of 1.8 mm.
Then, it was heated at 1120 ° C., cooled and annealed at 900 ° C. for a short time, then rapidly cooled, pickled, and cold rolled. Grooves were formed in a direction of 75 ° with the rolling direction by laser light at 0.25 mm in the middle of the cold rolling. The groove width was about 100 μm, the depth was about 15 μm, and the groove pitch in the rolling direction was 4 mm. Further, the molten deposit in the groove was removed by a sand belt and then cold rolled to 0.17 mm. After this, pickling with a 30% nitric acid solution for a short time and decarburization annealing for 830
After nitriding at 750 ° C for 30 seconds, H 2 , N
2. Performed in a mixed gas of ammonia and nitrogen amount of 200 pp
Adjusted to m. Then, the annealing separator was used under the following conditions. MgO + CaCl 2 (7%) MgO + BiCl 3 (3%) MgO + MgCl 2 (7%) MgO only (comparison) After that, finish annealing was performed at 1200 ° C. for 20 hours. The atmosphere gas in the temperature rising process of this annealing is H 2 : 25% + N 2 :
A 75% mixed gas was used and H 2 gas was used for purification. After that, it was washed with water and subjected to tension annealing mainly containing chromic anhydride and phosphorus phosphorus aluminum. Table 2 shows the obtained characteristics.
【表２】 このように、焼鈍分離剤にＣａＣｌ2，ＢｉＣｌ3，Ｍｇ
Ｃｌ2を添加することにより超低鉄損材が得られた。[Table 2] As described above, the annealing separator is not limited to CaCl 2 , BiCl 3 , Mg.
An ultra low iron loss material was obtained by adding Cl 2 .
【００２６】[0026]
【発明の効果】以上説明したように、本発明は最終冷延
の途中板厚段階で鋼板表面にレーザー光などにより人為
的に圧延方向に対し特定の角度で微小の溝を点状ないし
線状に付与し、最終板まで冷延後、Ａｌ2 Ｏ3 またはＭ
ｇＯにＣａ，Ｍｇ，Ｂｉの塩化物を添加した焼鈍分離剤
を塗布することで０．８０Ｗ／kg（Ｗ17/50 ）以下とい
う超低鉄損を有する方向性電磁鋼板を容易に製造するこ
とができるものである。As described above, according to the present invention, minute grooves are artificially formed on the surface of a steel sheet at a specific angle with respect to the rolling direction at a specific angle with respect to the rolling direction during the final cold rolling in a sheet thickness step. Al 2 O 3 or M after cold rolling to the final plate
To easily manufacture a grain- oriented electrical steel sheet having an ultra-low iron loss of 0.80 W / kg (W 17/50 ) or less by applying an annealing separator containing gO containing chlorides of Ca, Mg and Bi. Is something that can be done.
【図１】穿孔深さと鉄損との関係を示す図。FIG. 1 is a diagram showing the relationship between perforation depth and iron loss.
フロントページの続き (72)発明者 藤井 浩康 福岡県北九州市戸畑区飛幡町１−１ 新日 本製鐵株式会社八幡製鐵所内 (72)発明者 黒木 克郎 福岡県北九州市戸畑区大字中原46番地の59 日鐵プラント設計株式会社内 (72)発明者 田中 収 福岡県北九州市戸畑区大字中原46番地の59 日鐵プラント設計株式会社内 (72)発明者 岩永 功 福岡県北九州市戸畑区飛幡町１−１ 新日 本製鐵株式会社八幡製鐵所内(72) Inventor Hiroyasu Fujii 1-1 Tobata-cho, Tobata-ku, Kitakyushu, Fukuoka Prefecture Inside Nippon Steel Corporation Yawata Works (72) Inventor Katsuro Kuroki 46, Nakahara, Tobata-ku, Kitakyushu, Fukuoka 59 Nittetsu Plant Design Co., Ltd. (72) Inventor Osamu Tanaka At 59 Nittetsu Plant Design Co., Ltd. at 46 Nakahara, Tobata-ku, Kitakyushu, Fukuoka Prefecture (72) Inventor Isao Iwanaga Tobata-cho, Tobata-ku, Kitakyushu, Fukuoka 1-1 Nippon Steel Corporation Yawata Works
Claims (4)
Ｃ：０．０８５％以下、Ｍｎ：０．０５０〜０．４５
％、Ｓ≦０．０１５％、酸可溶性Ａｌ：０．０１０〜
０．０４０％、Ｎ：≦０．０１０％、Ｓｎ：０．０２〜
０．１５％、残部Ｆｅ及び不可避的不純物からなる電磁
鋼スラブを１２８０℃以下の温度で加熱した後、熱延
し、熱延板焼鈍をし、一回または中間焼鈍を介挿する二
回以上の圧延でその最終圧延率を８０％以上とし、次い
で脱炭焼鈍、窒化処理、焼鈍分離剤を塗布し、仕上げ焼
鈍をする一方向性電磁鋼板の製造において、その最終冷
延の途中板厚段階で鋼板表面に圧延方向に対して、９０
°〜４５°の範囲で幅が１０〜５００μｍ、深さが板厚
ｔ×１／８〜ｔ×１／３０、間隔が圧延方向に１〜２０
mmの溝を点状あるいは線状に形成した後、最終板厚まで
圧延後焼鈍分離剤としてＡｌ2 Ｏ3 を塗布し、仕上げ焼
鈍、張力コーティングを施すことを特徴とするフォルス
テライト皮膜を有しない超低鉄損方向性電磁鋼板の製造
方法。Claims: 1. A weight ratio of Si: 2.5 to 4.5%,
C: 0.085% or less, Mn: 0.050 to 0.45
%, S ≦ 0.015%, acid-soluble Al: 0.010
0.040%, N: ≦ 0.010%, Sn: 0.02
An electromagnetic steel slab consisting of 0.15% and the balance Fe and unavoidable impurities is heated at a temperature of 1280 ° C. or lower, and then hot-rolled, hot-rolled sheet annealed once or twice or more with intermediate annealing interposed. In the production of the unidirectional electrical steel sheet in which the final rolling rate is 80% or more by rolling, decarburization annealing, nitriding treatment, and annealing separator are applied, and finish annealing is performed, the final cold rolling intermediate sheet thickness step 90 ° to the steel plate surface in the rolling direction
The width is 10 to 500 μm, the depth is plate thickness t × 1/8 to t × 1/30, and the interval is 1 to 20 in the rolling direction in the range of ° to 45 °.
After forming a groove of mm in a dot shape or a linear shape, after rolling to the final plate thickness, Al 2 O 3 is applied as an annealing separating agent, and finish annealing and tension coating are applied, which does not have a forsterite film. Ultra low iron loss grain oriented electrical steel sheet manufacturing method.
に対して９０°から４５°の範囲で幅が１０から５００
μｍ、深さが板厚ｔ×１／８〜ｔ×１／３０、間隔が圧
延方向に１〜２０mmの溝を点状或いは線状に形成し、次
いで溝形成後に生じた溶融付着物を機械的方法で除去し
た後、最終板厚まで圧延することを特徴とする請求項１
記載のフォルステライト皮膜を有しない超低鉄損方向性
電磁鋼板の製造方法。2. The width of the steel sheet surface is 10 to 500 in the range of 90 ° to 45 ° with respect to the rolling direction by laser light.
μm, depth t × 1/8 to t × 1/30, and interval of 1 to 20 mm in the rolling direction are formed into dots or lines, and then the molten deposits generated after the grooves are machined. After removing it by a mechanical method, it is rolled to the final plate thickness.
A method for producing an ultra-low iron loss grain-oriented electrical steel sheet having no forsterite coating as described in the above.
を施すことを特徴とする請求項１または２記載のフォル
ステライト皮膜を有しない超低鉄損方向性電磁鋼板の製
造方法。3. The ultra-low iron loss grain-oriented electrical steel sheet having no forsterite coating according to claim 1 or 2, wherein the cold-rolled sheet having the final sheet thickness is lightly pickled before decarburization annealing. Production method.
に対し、Ｃａ，Ｍｇ，Ｂｉの塩化物から選ばれる１種又
は２種以上を合計で２〜３０重量部添加した焼鈍分離剤
を塗布することを特徴とする請求項１，２または３記載
のフォルステライト被膜を有しない超低鉄損方向性電磁
鋼板の製造方法。4. An annealing separator, which is obtained by adding 2 to 30 parts by weight in total of one or two or more kinds selected from chlorides of Ca, Mg, and Bi to 100 parts by weight of MgO as an annealing separator. The method for producing an ultra-low iron loss grain-oriented electrical steel sheet having no forsterite coating according to claim 1, 2 or 3.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP8340045A JPH09268322A (en) | 1996-02-02 | 1996-12-19 | Production of grain oriented silicon steel sheet with ultralow iron loss |
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1737196 | 1996-02-02 | ||
| JP8-17371 | 1996-02-02 | ||
| JP8340045A JPH09268322A (en) | 1996-02-02 | 1996-12-19 | Production of grain oriented silicon steel sheet with ultralow iron loss |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH09268322A true JPH09268322A (en) | 1997-10-14 |
Family
ID=26353881
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP8340045A Withdrawn JPH09268322A (en) | 1996-02-02 | 1996-12-19 | Production of grain oriented silicon steel sheet with ultralow iron loss |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH09268322A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100956533B1 (en) * | 2001-07-24 | 2010-05-07 | 제이에프이 스틸 가부시키가이샤 | A method of manufacturing grain-oriented electrical steel sheets |
| WO2012033197A1 (en) | 2010-09-09 | 2012-03-15 | 新日本製鐵株式会社 | Oriented electromagnetic steel sheet and process for production thereof |
| CN105463172A (en) * | 2015-12-14 | 2016-04-06 | 武汉钢铁(集团)公司 | Method for improving magnetic performance of silicon steel sheet through laser indented oriented silicon steel cold-rolled sheet |
| CN108138291A (en) * | 2015-10-26 | 2018-06-08 | 新日铁住金株式会社 | Grain-oriented magnetic steel sheet and the decarburization steel plate for its manufacture |
| KR20210110864A (en) * | 2019-01-16 | 2021-09-09 | 닛폰세이테츠 가부시키가이샤 | Grain-oriented electrical steel sheet and its manufacturing method |
-
1996
- 1996-12-19 JP JP8340045A patent/JPH09268322A/en not_active Withdrawn
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100956533B1 (en) * | 2001-07-24 | 2010-05-07 | 제이에프이 스틸 가부시키가이샤 | A method of manufacturing grain-oriented electrical steel sheets |
| WO2012033197A1 (en) | 2010-09-09 | 2012-03-15 | 新日本製鐵株式会社 | Oriented electromagnetic steel sheet and process for production thereof |
| US8657968B2 (en) | 2010-09-09 | 2014-02-25 | Nippon Steel & Sumitomo Metal Corporation | Grain-oriented electrical steel sheet and method of manufacturing the same |
| CN108138291A (en) * | 2015-10-26 | 2018-06-08 | 新日铁住金株式会社 | Grain-oriented magnetic steel sheet and the decarburization steel plate for its manufacture |
| EP3369834A4 (en) * | 2015-10-26 | 2019-07-10 | Nippon Steel Corporation | Grain-oriented electromagnetic steel sheet and decarburized steel sheet used for producing same |
| US10907234B2 (en) | 2015-10-26 | 2021-02-02 | Nippon Steel Corporation | Grain-oriented electrical steel sheet and decarburized steel sheet used for manufacturing the same |
| CN105463172A (en) * | 2015-12-14 | 2016-04-06 | 武汉钢铁(集团)公司 | Method for improving magnetic performance of silicon steel sheet through laser indented oriented silicon steel cold-rolled sheet |
| KR20210110864A (en) * | 2019-01-16 | 2021-09-09 | 닛폰세이테츠 가부시키가이샤 | Grain-oriented electrical steel sheet and its manufacturing method |
| EP3913092A4 (en) * | 2019-01-16 | 2022-12-14 | Nippon Steel Corporation | Grain-oriented electrical steel sheet and method for manufacturing same |
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