JP3277058B2 - Manufacturing method of unidirectional electrical steel sheet - Google Patents
Manufacturing method of unidirectional electrical steel sheetInfo
- Publication number
- JP3277058B2 JP3277058B2 JP33564293A JP33564293A JP3277058B2 JP 3277058 B2 JP3277058 B2 JP 3277058B2 JP 33564293 A JP33564293 A JP 33564293A JP 33564293 A JP33564293 A JP 33564293A JP 3277058 B2 JP3277058 B2 JP 3277058B2
- Authority
- JP
- Japan
- Prior art keywords
- annealing
- steel sheet
- mgo
- electrical steel
- grain
- 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.)
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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)
- Chemical Treatment Of Metals (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
- Soft Magnetic Materials (AREA)
Description
【０００１】[0001]
【産業上の利用分野】この発明は、一方向性電磁鋼板の
製造方法に関し、とくに良好なフォルステライト質絶縁
被膜を形成することによって、被膜特性のみならず磁気
特性の有利な改善を図ろうとするものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for manufacturing a grain-oriented electrical steel sheet, and more particularly to forming a favorable forsterite-based insulating film to improve not only the film properties but also the magnetic properties. Things.
【０００２】[0002]
【従来の技術】一方向性電磁鋼板において、表面に形成
される絶縁被膜は、単に電気絶縁性の面からだけでな
く、磁気特性及び外観上極めて重要な意味を持つ。かか
る絶縁被膜の形成に当たっては、所望の最終板厚に冷間
圧延した冷延板を、湿水素中にて 700〜900 ℃の温度範
囲で脱炭焼鈍し、その鋼板表面にSiO2を含む内部酸化層
を生成させたのち、マグネシウム（MgＯ）を主成分とす
る焼鈍分離剤を塗布しコイル状に巻き取ってから、高温
仕上げ焼鈍を施すことにより、MgＯ−SiO2系フォルステ
ライト質絶縁被膜を被成する方法が一般に行われてい
る。2. Description of the Related Art In a grain-oriented electrical steel sheet, an insulating film formed on the surface is extremely important not only in terms of electric insulation but also in terms of magnetic properties and appearance. In forming such an insulating film, a cold rolled sheet cold-rolled to a desired final sheet thickness is decarburized and annealed in a wet hydrogen atmosphere at a temperature range of 700 to 900 ° C., and the steel sheet surface contains SiO 2. mixture was allowed to form an oxidation layer, from winding the annealing separator composed mainly of magnesium (MgO) in coated form coils, by performing the high-temperature finish annealing, the MgO-SiO 2 based forsterite insulating coating The method of forming is generally performed.
【０００３】このフォルステライト質絶縁被膜は、焼鈍
分離剤中のMgＯが高温仕上げ焼鈍中に鋼板表面に存在す
るSiO2と固相反応を起こすことによって生成し、鋼板に
対して熱応力に起因する引張応力を付与することによっ
て、渦電流損を低下させる役割を担うだけでなく、製品
外観の良否を決定づけるものでもある。[0003] This forsterite insulating coating is formed by MgO in the annealing separator causing a solid-phase reaction with SiO 2 present on the steel sheet surface during high-temperature finish annealing, and is caused by thermal stress on the steel sheet. By applying a tensile stress, it not only plays a role of reducing eddy current loss, but also determines the quality of the product appearance.
【０００４】従って、一方向性電磁鋼板の表面に優れた
被膜特性を有するフォルステライト質絶縁被膜を形成さ
せることは極めて重要であり、これまでにも数多くの研
究がなされてきた。たとえば、MgＯの活性度や粒度分布
及び粒子形態の適正条件などについては、特開昭55-583
31号、特開昭50-11912号および特開昭58−193373号各公
報等において種々の提案がなされている。Therefore, it is extremely important to form a forsterite insulating coating having excellent coating properties on the surface of a grain-oriented electrical steel sheet, and many studies have been made so far. For example, regarding the activity of MgO, the particle size distribution, and the appropriate conditions for the particle morphology, see JP-A-55-583.
Various proposals have been made in JP-A-31-11, JP-A-50-11912 and JP-A-58-193373.
【０００５】[0005]
【課題を解決するための手段】一方向性電磁鋼板の製造
プロセスにおいて、最終冷間圧延後に脱炭焼鈍を施した
鋼板に対してMgＯを主成分とする焼鈍分離剤スラリーを
塗布・乾燥して、コイル状に巻き取り、コイルを仕上げ
焼鈍する間にフォルステライト質絶縁被膜が形成され
る。ここに、フォルステライト質絶縁被膜を形成形態
は、仕上げ焼鈍中のコイル層間雰囲気に大きく影響さ
れ、またこのコイル層間雰囲気ガスの流通性は、焼鈍分
離剤の粒度や焼鈍分離剤塗布・乾燥後のコイル巻取り張
力などに左右される。さらに焼鈍分離剤中のMgＯ自身
が、仕上げ焼鈍中に自己焼結収縮して、コイル層間雰囲
気ガス流通性を変化させる。Means for Solving the Problems In a manufacturing process of a grain-oriented electrical steel sheet, an annealing separator slurry containing MgO as a main component is applied to a steel sheet which has been subjected to decarburizing annealing after final cold rolling and dried. Then, the forsterite insulating film is formed during coiling and finish annealing of the coil. Here, the formation form of the forsterite insulating film is greatly affected by the atmosphere between the coil layers during the finish annealing, and the flowability of the atmosphere gas between the coil layers depends on the particle size of the annealing separator, and after the application and drying of the annealing separator. Depends on coil winding tension. Further, MgO itself in the annealing separator shrinks by self-sintering during the final annealing, and changes the gas flow between the coil layers.
【０００６】従来は、焼鈍分離剤用のMgＯについて、仕
上げ焼鈍中の特性変化に着目していなかったため、被膜
特性に優れたフォルステライト質絶縁被膜を形成するに
は、必ずしも十分というわけではなかった。この発明
は、上記の問題を有利に解決するもので、焼鈍分離剤の
主成分として用いるMgＯの特性を規制することによっ
て、良好なフォルステライト質被膜を形成し、もって優
れた磁気特性を得ることができる一方向性電磁鋼板の製
造方法を提案することを目的とする。[0006] Conventionally, MgO for an annealing separator has not been focused on property changes during finish annealing, so that it is not always sufficient to form a forsterite-based insulating coating having excellent coating properties. . The present invention advantageously solves the above-mentioned problems, and regulates the characteristics of MgO used as a main component of the annealing separator to form a good forsterite coating and thereby obtain excellent magnetic characteristics. It is an object of the present invention to propose a method for producing a grain-oriented electrical steel sheet that can be used.
【０００７】[0007]
【課題を解決するための手段】さて、発明者らは、仕上
げ焼鈍中におけるフォルステライト形成反応と焼鈍分離
剤の主成分であるMgＯ粒子の焼結による自己収縮変化と
の対応を研究する過程で、フォルステライト被膜形成反
応が進行する温度域におけるMgＯ粒子の自己焼結の程度
がフォルステライト被膜の膜質に影響を及ぼすことを見
出した。そこで、被膜形成及び磁気特性に及ぼすMgＯの
自己焼結による収縮率度とMgＯの平均粒子径との影響に
ついて調査したところ、かかる収縮率度と平均粒子径を
所定の範囲に規制することによって、所期した目的が有
利に達成されることの知見を得た。この発明は、上記の
知見に立脚するものである。Means for Solving the Problems In the course of studying the correspondence between the forsterite formation reaction during finish annealing and the change in auto-shrinkage due to sintering of MgO particles, which are the main component of the annealing separator, the inventors have studied. It has been found that the degree of self-sintering of MgO particles in the temperature range where the forsterite film forming reaction proceeds affects the quality of the forsterite film. Therefore, when investigating the effect of the degree of shrinkage due to the self-sintering of MgO and the average particle diameter of MgO on the film formation and magnetic properties, by regulating the degree of shrinkage and the average particle diameter to a predetermined range, It has been found that the intended purpose is achieved advantageously. The present invention is based on the above findings.
【０００８】すなわち、この発明は、含けい素鋼スラブ
を、熱間圧延したのち、１回又は中間焼鈍を含む２回の
冷間圧延を施して最終板厚とし、ついで脱炭焼鈍後、Mg
Ｏを主成分とする焼鈍分離剤を塗布してから、最終仕上
げ焼鈍を施すことによって一方向性電磁鋼板を製造する
に当たり、上記焼鈍分離剤中のMgＯとして、平均粒子径
が 0.3〜2.5 μm でかつ、1100℃における自己焼結によ
る線収縮率が10〜22％であるものを用いることを特徴と
する一方向性電磁鋼板の製造方法である。That is, according to the present invention, the silicon-containing steel slab is hot-rolled, and then cold-rolled once or twice including intermediate annealing to obtain a final sheet thickness.
In producing a grain-oriented electrical steel sheet by applying an annealing separator containing O as a main component and then performing a final finish annealing, the average particle diameter of MgO in the annealing separator is 0.3 to 2.5 μm. In addition, the present invention provides a method for producing a grain-oriented electrical steel sheet, which uses a linear shrinkage rate of 10 to 22% by self-sintering at 1100 ° C.
【０００９】[0009]
【作用】この発明において、MgＯの平均粒子径及び線収
縮率を上記の範囲に限定した理由は次のとおりである。
まず、MgＯ粉体の平均粒子径については、該粒子径が
0.3μm 未満ではコイル層間における雰囲気ガスの流通
性が劣化するため、フォルステライトの生成が遅れて外
観不良を招き易く、一方 2.5μm を超えるとコイル層間
の雰囲気ガスの流通性が高すぎるため、脱炭焼鈍時に形
成される酸化層内のSiO2の鋼板表面への解離浮上が進行
し易くなり、密着性が劣化するので、平均粒子径は 0.3
〜2.5 μmの範囲に限定した。In the present invention, the reason why the average particle diameter and the linear shrinkage of MgO are limited to the above ranges is as follows.
First, regarding the average particle size of the MgO powder,
If the thickness is less than 0.3 μm, the flow of the atmosphere gas between the coil layers deteriorates, so that the formation of forsterite is delayed and the appearance is likely to be deteriorated.If the thickness exceeds 2.5 μm, the flow of the atmosphere gas between the coil layers is too high. Since the dissociation and floating of the SiO 2 in the oxide layer formed during the charcoal annealing on the steel sheet surface is easy to progress and the adhesion is deteriorated, the average particle diameter is 0.3
Limited to the range of 2.52.5 μm.
【００１０】次に、MgＯ粉体の1100℃における線収縮率
が10％に満たないと、コイル層間のガス流通性が十分で
なく、フォルステライト形成反応の進行が遅くなるた
め、鋼板のフォルステライト被膜の密着性が劣化し、一
方22％を超えると、仕上げ焼鈍中に鋼板表面が酸化され
易くなり、インヒビターの分解やフォルステライト被膜
の結晶粒粗大化を招くので、線収縮率は10〜22％の範囲
に限定した。ここに、焼鈍分離剤を塗布・乾燥した鋼板
のコイル巻き取り時における面圧は約100 kg/cm2である
ので、上記の線収縮率の測定に際しては、MgＯの成形圧
力を100 kg/cm2とし、非酸化性ガス中で焼成し、焼成前
後の寸法変化により求めた。このとき、目標温度での保
定処理は行わなかった。なお、1100℃における線収縮率
を10〜22％の範囲に制御するには、MgO 製造工程の Mg
(OH)2焼成条件すなわち焼成温度パターン、焼成炉内水
蒸気圧力、雰囲気およびガス流量等を調整すれば良い。Next, if the linear shrinkage at 1100 ° C. of the MgO powder is less than 10%, the gas flow between the coil layers is not sufficient, and the progress of the forsterite formation reaction is slowed. If the adhesion of the coating is deteriorated, and if it exceeds 22%, the surface of the steel sheet is easily oxidized during the finish annealing, which leads to decomposition of the inhibitor and coarsening of the crystal grains of the forsterite coating. %. Here, since the surface pressure during coil winding of the steel sheet coated and dried with the annealing separator is about 100 kg / cm 2 , when measuring the linear shrinkage, the forming pressure of MgO is set to 100 kg / cm 2. It was set to 2 and fired in a non-oxidizing gas, and determined by the dimensional change before and after firing. At this time, the holding process at the target temperature was not performed. In order to control the linear shrinkage at 1100 ° C. in the range of 10 to 22%, it is necessary to use Mg
(OH) 2 The firing conditions, that is, the firing temperature pattern, the steam pressure in the firing furnace, the atmosphere, the gas flow rate, and the like may be adjusted.
【００１１】この発明の素材である含けい素鋼の組成は
特に限定されることはなく、従来公知のものいずれもが
適合する。参考のために、好適組成範囲を例示すると次
のとおりである。 Ｃ：0.001 〜0.10％ Ｃは、熱間圧延及び冷間圧延中における組織の均一微細
化だけでなく、ゴス方位の発達に有用な元素であり、少
なくとも 0.001％含有することが好ましい。しかしなが
ら、0.10％を超えて含有した場合には脱炭が困難とな
り、かえってゴス方位に乱れが生じるので、上限は0.10
％とすることが好ましい。The composition of the silicon-containing steel which is the material of the present invention is not particularly limited, and any conventionally known one can be used. For reference, a preferred composition range is as follows. C: 0.001 to 0.10% C is an element useful for not only making the structure uniform and fine during hot rolling and cold rolling, but also for developing the Goss orientation, and is preferably contained at least 0.001%. However, if the content exceeds 0.10%, decarburization becomes difficult, and the Goss orientation is rather disturbed. Therefore, the upper limit is 0.10%.
% Is preferable.
【００１２】Si：2.5 〜4.5 ％ Siは、鋼板の比抵抗を高め鉄損の低減に寄与するが、含
有量が 4.5％を上回ると冷延性が損なわれ、一方 2.5％
に満たないと比抵抗が低下するだけでなく、二次再結晶
及び純化のために行われる最終焼鈍中にα−γ変態によ
って結晶方位のランダム化を生じ、十分な鉄損改善効果
が得られないので、Siは 2.5〜4.5 ％程度とするのが好
ましい。Si: 2.5 to 4.5% Si contributes to increase the specific resistance of the steel sheet and reduce iron loss. However, if the content exceeds 4.5%, the cold rolling property is impaired, while 2.5% to 4.5%.
Not only lowers the specific resistance, but also randomizes the crystal orientation by α-γ transformation during the final annealing performed for secondary recrystallization and purification, and a sufficient iron loss improvement effect is obtained. Therefore, the content of Si is preferably about 2.5 to 4.5%.
【００１３】Mn：0.02〜0.12％ Mnは、熱間脆化を防止するためには少なくとも0.02％程
度を必要とするが、あまり多すぎると磁気特性を劣化さ
せるので、上限は0.12％程度とするのが好ましい。Mn: 0.02 to 0.12% Mn requires at least about 0.02% in order to prevent hot embrittlement, but if it is too much, magnetic properties are degraded, so the upper limit is about 0.12%. Is preferred.
【００１４】インヒビターとしては、いわゆるMnＳ, Mn
Se系とAlＮ系とがある。 MnＳ, MnSe系の場合 Ｓ, Seのうちから選ばれる少なくとも一種：0.005 〜0.
06％ Ｓ, Seはいずれも、方向性けい素鋼板の二次再結晶を制
御するインヒビターとして有力な元素である。抑制力の
観点からは、少なくとも 0.005％程度を必要とするが0.
06％を超えるとその効果が損なわれる。従って、その上
限、下限はそれぞれ 0.005％、0.06％程度とするのが好
ましい。 AlＮ系の場合 Al:0.005〜0.10, Ｎ：0.004 〜0.015 ％ Al及びＮの範囲についても、上述のMnＳ, MnSe系の場合
と同様の理由から上記の範囲に定めた。なお、上述のMn
Ｓ, MnSe系及びAlＮ系はそれぞれ併用が可能である。さ
らに、インヒビター成分としては、上記したＳ, Se, Al
の他、Cu, Sn, Sb,Mo, Te及びBi等も有利に作用するの
でそれぞれ少量併せて含有させることもできる。これら
の成分の好適添加範囲はそれぞれ、Cu, Sn：0.01〜0.15
％、Sb, Mo,Te, Bi：0.005 〜0.1 ％であり、これらの
各インヒビター成分についても、単独使用及び複合使用
のいずれもが可能である。As inhibitors, so-called MnS, Mn
There are Se type and AlN type. MnS, MnSe system At least one selected from S and Se: 0.005 to 0.
06% S and Se are both effective elements as inhibitors for controlling secondary recrystallization of grain-oriented silicon steel sheets. From the viewpoint of suppressing power, at least about 0.005% is required,
If it exceeds 06%, the effect will be lost. Therefore, the upper and lower limits are preferably set to about 0.005% and 0.06%, respectively. AlN-based Al: 0.005 to 0.10, N: 0.004 to 0.015% The ranges of Al and N are also set to the above ranges for the same reason as in the case of the above-mentioned MnS and MnSe-based. Note that the above Mn
S, MnSe-based and AlN-based can be used together. Further, as the inhibitor component, S, Se, Al
Besides, Cu, Sn, Sb, Mo, Te, Bi and the like also act advantageously, so that they can be contained together in small amounts. The preferable addition ranges of these components are respectively Cu and Sn: 0.01 to 0.15.
%, Sb, Mo, Te, Bi: 0.005 to 0.1%, and each of these inhibitor components can be used alone or in combination.
【００１５】鋼板の製造方法については、特に限定され
ることはなく、従来公知の製造条件で行えば良い。すな
わち、含けい素鋼スラブを、熱間圧延した後、１回また
は中間焼鈍を含む２回の冷間圧延を施して最終板厚と
し、ついで脱炭焼鈍後、鋼板表面に焼鈍分離剤を塗布し
てから、２次再結晶焼鈍および純化焼鈍を施せば良い。The method for manufacturing the steel sheet is not particularly limited, and may be performed under conventionally known manufacturing conditions. That is, after the silicon-containing slab is hot-rolled, it is cold-rolled once or twice, including intermediate annealing, to a final thickness. Then, after decarburizing annealing, an annealing separator is applied to the steel sheet surface. Then, secondary recrystallization annealing and purification annealing may be performed.
【００１６】[0016]
【実施例】Ｃ：0.07wt％，Si：3.25wt％，Mn：0.07wt
％，Se：0.017 wt％，Al：0.023 wt％及びＮ：0.0085wt
％を含み、残部は実質的にFeの組成になるスラブを、熱
間圧延したのち、中間焼鈍を含む２回の冷間圧延を施し
て最終板厚：0.23mmの冷延板し、ついで脱炭焼鈍後、表
１に示す種々のMgＯを主成分とする焼鈍分離剤をそれぞ
れ塗布してから、仕上げ焼鈍を施した。得られた製品の
被膜特性及び鉄損値について調べた結果を図１に示す。[Example] C: 0.07 wt%, Si: 3.25 wt%, Mn: 0.07 wt%
%, Se: 0.017 wt%, Al: 0.023 wt% and N: 0.0085 wt%
%, And the remainder is substantially rolled to a slab having a composition of Fe, and then cold-rolled twice including intermediate annealing to obtain a cold-rolled sheet having a final thickness of 0.23 mm. After the charcoal annealing, various annealing separators mainly composed of MgO shown in Table 1 were applied, respectively, and then subjected to finish annealing. FIG. 1 shows the results of examining the film properties and iron loss value of the obtained product.
【００１７】[0017]
【表１】 [Table 1]
【００１８】図１から明らかなように、この発明に従い
得られたNo.1〜5 はいずれも、被膜形成が均一であり、
フォルステライト被膜と地鉄との密着性も十分であるた
め、良好な鉄損値が得られている。これに対し、平均粒
子径や線収縮率が適正範囲を逸脱したNo.6〜10の比較例
は、被膜特性が不良であるため、鉄損も劣化している。As is clear from FIG. 1, all of Nos. 1 to 5 obtained according to the present invention have uniform film formation,
Since the adhesion between the forsterite film and the ground iron is also sufficient, a good iron loss value is obtained. On the other hand, in Comparative Examples Nos. 6 to 10 in which the average particle diameter and the linear shrinkage ratio deviated from the appropriate ranges, the core loss was deteriorated because the coating properties were poor.
【００１９】[0019]
【発明の効果】かくしてこの発明に従い、焼鈍分離剤と
して、平均粒子径が 0.3〜2.5 μm でかつ、1100℃にお
ける自己焼結による線収縮率が10〜22％のMgＯを用いる
ことにより、仕上げ焼鈍中のコイル層間のガス流通性や
MgＯの活性度が最適となるので、良好なフォルステライ
ト被膜を形成することができ、被膜特性のみならず磁気
特性も優れた方向性電磁鋼板を得ることができる。According to the present invention, MgO having an average particle diameter of 0.3 to 2.5 μm and a linear shrinkage rate of 10 to 22% by self-sintering at 1100 ° C. is used as an annealing separator according to the present invention. Gas flow between coil layers inside
Since the activity of MgO is optimized, a good forsterite coating can be formed, and a grain-oriented electrical steel sheet having excellent magnetic properties as well as coating properties can be obtained.
【図１】焼鈍分離剤として種々のMgＯを用いた場合にお
ける被膜特性及び鉄損値を示した図である。FIG. 1 is a diagram showing coating properties and iron loss values when various MgOs are used as an annealing separator.
───────────────────────────────────────────────────── フロントページの続き (58)調査した分野(Int.Cl.7，ＤＢ名) C23C 22/00 C21D 9/46 501 H01F 1/16 ──────────────────────────────────────────────────続 き Continued on the front page (58) Field surveyed (Int. Cl. 7 , DB name) C23C 22/00 C21D 9/46 501 H01F 1/16
Claims (1)
ち、１回又は中間焼鈍を含む２回の冷間圧延を施して最
終板厚とし、ついで脱炭焼鈍後、MgＯを主成分とする焼
鈍分離剤を塗布してから、最終仕上げ焼鈍を施すことに
よって一方向性電磁鋼板を製造するに当たり、 上記焼鈍分離剤中のMgＯとして、平均粒子径が 0.3〜2.
5 μm でかつ、1100℃における自己焼結による線収縮率
が10〜22％であるものを用いることを特徴とする一方向
性電磁鋼板の製造方法。1. A silicon steel slab is hot-rolled and then cold-rolled once or twice including intermediate annealing to a final thickness, and after decarburizing annealing, MgO is mainly used. After producing the grain-oriented electrical steel sheet by applying the annealing separator to be subjected to final finish annealing, the average particle diameter of the MgO in the annealing separator is 0.3 to 2.
A method for producing a grain-oriented electrical steel sheet, wherein a sheet having a diameter of 5 μm and a linear shrinkage ratio of 10 to 22% by self-sintering at 1100 ° C. is used.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP33564293A JP3277058B2 (en) | 1993-12-28 | 1993-12-28 | Manufacturing method of unidirectional electrical steel sheet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP33564293A JP3277058B2 (en) | 1993-12-28 | 1993-12-28 | Manufacturing method of unidirectional electrical steel sheet |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH07188937A JPH07188937A (en) | 1995-07-25 |
| JP3277058B2 true JP3277058B2 (en) | 2002-04-22 |
Family
ID=18290887
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP33564293A Expired - Fee Related JP3277058B2 (en) | 1993-12-28 | 1993-12-28 | Manufacturing method of unidirectional electrical steel sheet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3277058B2 (en) |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH1088244A (en) * | 1996-09-12 | 1998-04-07 | Kawasaki Steel Corp | Magnesium oxide for separation agent at annealing used fixed at manufacture of grain oriented silicon steel sheet |
| JP4569070B2 (en) * | 2003-03-13 | 2010-10-27 | Ｊｆｅスチール株式会社 | Finish annealing method for grain-oriented electrical steel sheets |
| JP4632775B2 (en) * | 2004-12-22 | 2011-02-16 | Ｊｆｅスチール株式会社 | Method for producing MgO for annealing separator |
| JP5434560B2 (en) * | 2009-12-17 | 2014-03-05 | Ｊｆｅスチール株式会社 | Finishing annealing method for annealing separator and grain-oriented electrical steel sheet |
| JP5494268B2 (en) * | 2010-06-15 | 2014-05-14 | Ｊｆｅスチール株式会社 | Annealing separator and method for producing grain-oriented electrical steel sheet |
| JP5729009B2 (en) * | 2011-02-25 | 2015-06-03 | Ｊｆｅスチール株式会社 | Annealing separator |
-
1993
- 1993-12-28 JP JP33564293A patent/JP3277058B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH07188937A (en) | 1995-07-25 |
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