JPH05285592A - Production of unidirectionally grain oriented electrical steel sheet - Google Patents
Production of unidirectionally grain oriented electrical steel sheetInfo
- Publication number
- JPH05285592A JPH05285592A JP4085392A JP8539292A JPH05285592A JP H05285592 A JPH05285592 A JP H05285592A JP 4085392 A JP4085392 A JP 4085392A JP 8539292 A JP8539292 A JP 8539292A JP H05285592 A JPH05285592 A JP H05285592A
- Authority
- JP
- Japan
- Prior art keywords
- steel sheet
- electrical steel
- slab
- atmosphere
- oriented electrical
- 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.)
- Withdrawn
Links
Classifications
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Landscapes
- Manufacturing Of Steel Electrode Plates (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、電気機器の鉄心材料と
して用いられる軟磁性材料である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 method for manufacturing a unidirectional electrical steel sheet which is a soft magnetic material used as an iron core material for electric equipment.
【０００２】[0002]
【従来の技術】一方向性電磁鋼板は、鋼板面が｛１１
０｝面で圧延方向に〈００１〉軸を有するいわゆるゴス
方位（ミラー指数を用い、｛１１０｝〈００１〉と表
す）を持つ結晶粒から構成されており、軟磁性材料とし
て変圧器あるいは発電機用の鉄心に使用される。一方向
性電磁鋼板は、磁気特性として磁化特性と鉄損特性が良
好であることが要求される。2. Description of the Related Art A unidirectional electrical steel sheet has a steel sheet surface of {11
It is composed of crystal grains having a so-called Goss orientation (which uses Miller index and is expressed as {110} <001>) having a <001> axis in the rolling direction on the 0} plane and is used as a soft magnetic material for a transformer or a generator. Used for iron cores. The unidirectional electrical steel sheet is required to have good magnetic characteristics and good iron loss characteristics.
【０００３】磁化特性は、かけられた一定の磁場力の下
で鉄心内に誘起される磁束密度の高低によってその良否
が評価される。高い磁束密度を持つ一方向性電磁鋼板
は、結晶粒の方位を｛１１０｝〈００１〉に高度にそろ
えることによって得られる。The quality of the magnetization characteristic is evaluated by the level of the magnetic flux density induced in the iron core under a constant applied magnetic field force. A grain-oriented electrical steel sheet having a high magnetic flux density can be obtained by highly aligning the crystal grain orientations with {110} <001>.
【０００４】鉄損特性は、鉄心に所定の交流磁場を与え
た場合に、熱エネルギーとして消費される電力損失の多
寡によってその良否が評価される。鉄損特性の良否に
は、磁束密度、板厚、比抵抗、結晶粒径等の因子が影響
する。高い磁束密度を持つ一方向性電磁鋼板は、電気機
器を小型化することを可能ならしめるとともに、鉄損特
性を良好ならしめるので非常に好ましい。The quality of the iron loss characteristic is evaluated based on the amount of power loss consumed as heat energy when a predetermined AC magnetic field is applied to the iron core. Factors such as magnetic flux density, plate thickness, specific resistance, and crystal grain size influence the quality of iron loss characteristics. A grain-oriented electrical steel sheet having a high magnetic flux density is very preferable because it enables downsizing of electric equipment and also improves iron loss characteristics.
【０００５】ところで、一方向性電磁鋼板は、熱間圧
延、冷間圧延および焼鈍の適切な組み合わせによって最
終板厚とした鋼板に、高温の仕上げ焼鈍を施すことによ
って｛１１０｝〈００１〉方位を有する１次再結晶粒が
選択的に成長する、いわゆる２次再結晶によって得られ
る。By the way, the unidirectional electrical steel sheet has a {110} <001> orientation obtained by subjecting a steel sheet having a final thickness by a suitable combination of hot rolling, cold rolling and annealing to high temperature finish annealing. It is obtained by so-called secondary recrystallization in which the primary recrystallized grains that it has grow selectively.
【０００６】２次再結晶は、２次再結晶前の鋼板中に微
細な析出物、例えばＭｎＳ，ＡｌＮ，ＭｎＳｅ等が存在
すること、あるいはＳｎ，Ｓｂ，Ｐ等の粒界偏析型の元
素が存在することによって達成される。これら鋼板中の
微細な析出物あるいは粒界偏析型の元素は、仕上げ焼鈍
中の｛１１０｝〈００１〉方位以外の１次再結晶粒の成
長を抑え、｛１１０｝〈００１〉方位粒を選択的に成長
させる機能を持つ。このような粒成長の抑制作用を、一
般に、インヒビター効果と呼んでいる。In the secondary recrystallization, fine precipitates such as MnS, AlN, MnSe and the like exist in the steel sheet before the secondary recrystallization, or grain boundary segregation type elements such as Sn, Sb and P are present. Achieved by being present. Fine precipitates or grain boundary segregation type elements in these steel sheets suppress the growth of primary recrystallized grains other than the {110} <001> orientation during finish annealing and select the {110} <001> oriented grains. Have the ability to grow physically. Such an effect of suppressing grain growth is generally called an inhibitor effect.
【０００７】従って、当該技術分野における研究開発の
重点課題は、いかなる種類の析出物あるいは粒界偏析型
の元素を用いて２次再結晶を安定させるか、そして正確
な｛１１０｝〈００１〉方位粒の存在割合を高めるため
に、それらの適切な存在状態をいかにして達成するかに
ある。[0007] Therefore, what is important in the research and development in this technical field is what kind of precipitate or grain boundary segregation type element is used to stabilize the secondary recrystallization, and the exact {110} <001> orientation. How to achieve their proper state of presence in order to increase the abundance of grains.
【０００８】しかるに、従来の薄鋳片鋳造技術において
は、母材溶解時の溶湯表面からの成分拡散および鋳造後
の高温の鋳片表面からの成分拡散により、鋳片中の成分
的中が困難であり、ひいては２次再結晶に重要な役割を
果たすインヒビター形成が不安定であり、薄鋳片を出発
材とする一方向性電磁鋼板のコスト上昇の原因となって
いた。However, in the conventional thin slab casting technique, it is difficult to achieve the composition in the slab due to the component diffusion from the surface of the molten metal when the base material is melted and the component diffusion from the surface of the hot slab after casting. In addition, the formation of an inhibitor, which plays an important role in secondary recrystallization, is unstable, which causes a cost increase of the grain-oriented electrical steel sheet starting from a thin cast piece.
【０００９】[0009]
【発明が解決しようとする課題】本発明は、薄鋳片を素
材とする一方向電磁鋼板製造法において、薄鋳片鋳造時
の雰囲気を特定の成分に保つことにより、２次再結晶の
発現に重要な役割を果たす成分を安定にコントロール
し、極めて安定した２次再結晶を実現させ、高磁束密度
を有する製品を得ることを達成しかつ、薄鋳片を素材と
した、より低コストのプロセスを実現することを課題と
するもので、就中良好な磁気特性を有する製品を低コス
トで製造しうる一方向性電磁鋼板製造方法を提供するこ
とを目的とするものである。DISCLOSURE OF THE INVENTION The present invention, in a unidirectional electrical steel sheet manufacturing method using a thin slab as a raw material, keeps an atmosphere during casting of the thin slab with a specific component to cause secondary recrystallization. Stable control of the components that play an important role in achieving stable secondary recrystallization, achieving a product with a high magnetic flux density, and using a thin slab as a raw material It is an object of the present invention to realize a process, and it is an object of the present invention to provide a unidirectional electrical steel sheet manufacturing method capable of manufacturing a product having excellent magnetic properties at low cost.
【００１０】[0010]
【課題を解決するための手段】本発明の要旨とするとこ
ろは以下の通りである。 （１）鋼中に２．３〜４．３％、Ｃ：０．０３〜０．１
０％、ｓｏｌＡｌ：０．０１０〜０．０６５％、Ｎ：
０．００１０〜０．０１５０％、Ｍｎ：０．０２〜０．
３０％、Ｓ：０．００５〜０．０４０％および残部が実
質的にＦｅからなる鋼板であり、鋳片の凝固速度が８．
５℃／sec 以上であって、得られた鋳片を出発材とし
て、これに、一回あるいは中間焼鈍を含む二回以上の冷
間圧延を施して最終板厚とし、次いで脱炭焼鈍、焼鈍分
離材塗布を施した後、二次再結晶を目的とする仕上げ焼
鈍を施す一方向性電磁鋼板の製造方法にあって、溶湯の
凝固時に、溶湯周辺の雰囲気を、Ｎ2 ：１〜１００Tor
r、残りはＨｅ，Ｎｅ，Ａｒ等の不活性ガスからなる所
定の雰囲気に保つことを特徴とする一方向性電磁鋼板の
製造方法。The main points of the present invention are as follows. (1) 2.3 to 4.3% in steel, C: 0.03 to 0.1
0%, solAl: 0.010 to 0.065%, N:
0.0010 to 0.0150%, Mn: 0.02 to 0.
30%, S: 0.005 to 0.040% and the balance substantially Fe, and the solidification rate of the slab is 8.
At 5 ° C./sec or more, the obtained slab is used as a starting material, and cold rolling is performed once or twice or more including intermediate annealing to obtain a final plate thickness, and then decarburization annealing and annealing. A method for producing a unidirectional electrical steel sheet, comprising applying a separating material and then performing a final annealing for the purpose of secondary recrystallization, wherein the atmosphere around the molten metal is N 2 : 1 to 100 Tor during solidification of the molten metal.
A method for producing a grain-oriented electrical steel sheet, characterized in that r and the rest are maintained in a predetermined atmosphere of an inert gas such as He, Ne, Ar.
【００１１】（２）前項１の製造方法にあって、凝固直
後の鋳片周辺の雰囲気をＮ2 ：１〜１００Torr、残りは
Ｈｅ，Ｎｅ，Ａｒ等の不活性ガスからなる所定の雰囲気
に保つこと。(2) In the manufacturing method of the above item 1, the atmosphere around the slab immediately after solidification is kept at a predetermined atmosphere of N 2 : 1 to 100 Torr, and the rest is an inert gas such as He, Ne and Ar. thing.
【００１２】以下に、本発明を詳細に説明する。まず、
成分であるが、Ｃは０．０３％未満になると２次再結晶
が不安定になり、またＣが多くなりすぎると脱炭焼鈍時
間が長くなり経済的でないので０．１０％以下とした。
Ｓｉが２．３％未満では、電気抵抗が低く良好な鉄損特
性が得難いので２．３％以上とする。一方、Ｓｉが４．
３％を超えると、鋼板を冷間圧延するときに割れが大き
くなるので、４．３％以下とする。The present invention will be described in detail below. First,
Although it is a component, if C is less than 0.03%, secondary recrystallization becomes unstable, and if C is too much, decarburization annealing time becomes long and it is not economical, so it was made 0.10% or less.
If Si is less than 2.3%, the electric resistance is low and it is difficult to obtain good iron loss characteristics, so the content is set to 2.3% or more. On the other hand, Si is 4.
If it exceeds 3%, cracks will increase during cold rolling of the steel sheet, so the content is made 4.3% or less.
【００１３】ＡｌおよびＮは２次再結晶の安定化に必要
なＡｌＮを確保するため酸可溶性Ａｌとして０．０１０
％以上、Ｎとして０．００１０％以上が必要である。酸
可溶性Ａｌが０．０６５％を超えると熱延板のＡｌＮが
不適切となり、２次再結晶が不安定になるので０．０４
５％以下とした。Ｎについては０．０１５０％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するので
０．０１５０％以下とした。Al and N are 0.010 as acid-soluble Al in order to secure AlN necessary for stabilizing secondary recrystallization.
% Or more and 0.0010% or more as N is required. If the acid-soluble Al exceeds 0.065%, the AlN of the hot-rolled sheet becomes inappropriate and the secondary recrystallization becomes unstable.
It was set to 5% or less. When N exceeds 0.0150%, swelling of the steel sheet surface called a blister occurs, so the content was made 0.0150% or less.
【００１４】またＭｎおよびＳはインヒビターＭｎＳを
形成するのに必要な元素であり、上記範囲を外れると２
次再結晶が不安定となり好ましくないので、Ｍｎは０．
０２〜０．３０％、Ｓは０．００５％〜０．０４０％と
定める。その他インヒビターＭｎＳとして公知であるＳ
ｎ，Ｓｂ，Ｓｅ，Ｔｅ，Ｃｕ，Ｎｂ，Ｃｒ，Ｎｉ，Ｂ，
Ｖ，Ａｓ，Ｂｉ等を必要に応じて含有させても良い。Further, Mn and S are elements necessary for forming the inhibitor MnS.
Since secondary recrystallization becomes unstable, it is not preferable.
02 to 0.30% and S are set to 0.005% to 0.040%. S known as other inhibitor MnS
n, Sb, Se, Te, Cu, Nb, Cr, Ni, B,
V, As, Bi, etc. may be contained if necessary.
【００１５】これらの成分を含有する溶鋼を、Ｎ2 ：１
〜１００Torr、好ましくは、Ｎ2 ：１０〜６０Torr、残
部Ｈｅ，Ａｒ等の一種以上の不活性ガスからなる雰囲気
中にて鋳造を行う。Ｎ2 は１Torr以下であると雰囲気に
Ｎ2 添加することによるスラブの成分的中の安定化効果
が見られず、１００Torr以上では鋳造時に雰囲気から鋳
片への過大なＮ2 拡散により、適切なインヒビター形成
に必要な成分的中がかえって困難になる。ベースガスと
しては、溶湯および高温の鋳片中の成分と反応し、酸化
物、窒化物等を形成するおそれのないＡｒ，Ｈｅ等の不
活性ガスが適当である。Molten steel containing these components was added with N 2 : 1.
～100Torr, preferably, N 2: 10~60Torr, balance He, casting in an atmosphere composed of one or more inert gases such as Ar performed. If N 2 is 1 Torr or less, the stabilizing effect in the composition of the slab by adding N 2 to the atmosphere is not seen, and if it is 100 Torr or more, an excessive N 2 diffusion from the atmosphere to the slab at the time of casting is appropriate. The components necessary for inhibitor formation become rather difficult. As the base gas, an inert gas such as Ar or He, which does not react with the components in the molten metal and the high-temperature slab to form an oxide, a nitride, or the like, is suitable.
【００１６】本発明では、ＡｌＮを主インヒビターとし
ており、ＡｌＮの析出処理を目的として、７０〜１２０
０℃の熱延板焼鈍を必要に応じて行う。この薄帯を冷間
圧延し、最終板厚とする。高い磁束密度を有する製品を
得るためには、８０％以上、望ましくは８８％以上の強
圧下を適用する冷間圧延をすることが適切である。最終
板厚とされた材料は、７００℃〜９００℃の温度で脱炭
焼鈍を行う。その後、この脱炭焼鈍板に焼鈍分離材を塗
布する。次いで、２次再結晶を目的とする仕上焼鈍を行
う。In the present invention, AlN is used as the main inhibitor, and 70 to 120 is used for the purpose of precipitating AlN.
Annealing of a hot-rolled sheet at 0 ° C is performed as necessary. This thin strip is cold-rolled to obtain the final plate thickness. In order to obtain a product having a high magnetic flux density, it is appropriate to carry out cold rolling applying a strong reduction of 80% or more, preferably 88% or more. The material having the final plate thickness is subjected to decarburization annealing at a temperature of 700 ° C to 900 ° C. Then, an annealing separator is applied to this decarburized annealed plate. Then, finish annealing for the purpose of secondary recrystallization is performed.
【００１７】[0017]
実施例１ 重量比で、Ｃ：０．０６５〜０．０７５％、Ｓｉ：３．
２２〜３．２７％、Ｍｎ：０．１１〜０．１３％、Ｓ：
０．０２２〜０．０２４％、ｓｏｌＡｌ：０．０２６５
〜０．０２７５％、Ｔｏｔａｌ Ｎ：０．００８０〜
０．０８４％、残部実質的にＦｅからなる母材をほぼ１
５００℃からほぼ１０００℃までを６００℃／min の速
度で冷却し厚さ約２．０mmに鋳造した。溶解および鋳造
時の雰囲気は、Ｎ2 ：６０Torr、残部Ａｒ雰囲気に保持
し、Ｎ2 ＋Ａｒを一気圧とした。Example 1 By weight ratio, C: 0.065 to 0.075%, Si: 3.
22-3.27%, Mn: 0.11-0.13%, S:
0.022-0.024%, solAl: 0.0265
~ 0.0275%, Total N: 0.0080 ~
0.084%, the base material consisting essentially of Fe is almost 1
From 500 ° C to almost 1000 ° C was cooled at a rate of 600 ° C / min and cast to a thickness of about 2.0 mm. The atmosphere during melting and casting was N 2 : 60 Torr, the balance was maintained in Ar atmosphere, and N 2 + Ar was set to 1 atm.
【００１８】この板を１１００℃、２分間の焼鈍後、
０．２mmに冷間圧延し、８１０℃で脱炭焼鈍し、焼鈍分
離剤としてＭｇＯ中に５％のＴｉＯを添加したものを塗
布し、１２００℃、２０時間の仕上げ焼鈍を行った。ま
た比較例として、同様の成分の素材を用い、母材の溶解
および鋳片鋳造を大気中で行った。After annealing this plate at 1100 ° C. for 2 minutes,
It was cold-rolled to 0.2 mm, decarburized and annealed at 810 ° C., 5% TiO in MgO was added as an annealing separating agent, and finish annealing was performed at 1200 ° C. for 20 hours. In addition, as a comparative example, using a material having the same composition, melting of the base material and casting of the slab were performed in the atmosphere.
【００１９】本発明の雰囲気中でこの母材から繰り返し
行った鋳片鋳造時のＮの成分的中率（本発明範囲のＮ量
に鋳片中のＮが入った割合）を、鋳片の鋳造を大気中で
行った比較例とともに表１に、このときの磁性と２次再
結晶状況を表２に示す。The component content ratio of N (the ratio of N in the slab to the amount of N in the range of the present invention) during casting of the slab repeatedly performed from this base material in the atmosphere of the present invention Table 1 shows the comparative example in which the casting was performed in the atmosphere, and Table 2 shows the magnetism and the secondary recrystallization condition at this time.
【００２０】[0020]
【表１】 [Table 1]
【００２１】[0021]
【表２】 [Table 2]
【００２２】実施例２ 重量比で、Ｃ：０．０６５〜０．０７５％、Ｓｉ：３．
２２〜３．２７％、Ｍｎ：０．１１〜０．１３％、Ｓ：
０．０２２〜０．０２４％、ｓｏｌＡｌ：０．０２６５
〜０．０２７５％、Ｔｏｔａｌ Ｎ：０．００８０〜
０．０８４％、残部実質的にＦｅからなる母材をほぼ１
５００℃からほぼ１０００℃までを６００℃／min の速
度で冷却し厚さ約２．０mmに鋳造した。溶解および鋳造
時および鋳造直後の鋳片周辺の雰囲気は、Ｎ2 ：６０To
rr、残部Ａｒ雰囲気に保持し、Ｎ2＋Ａｒを一気圧とし
た。Example 2 C: 0.065 to 0.075% by weight, Si: 3.
22-3.27%, Mn: 0.11-0.13%, S:
0.022-0.024%, solAl: 0.0265
~ 0.0275%, Total N: 0.0080 ~
0.084%, the base material consisting essentially of Fe is almost 1
From 500 ° C to almost 1000 ° C was cooled at a rate of 600 ° C / min and cast to a thickness of about 2.0 mm. The atmosphere around the slab during melting and casting and immediately after casting is N 2 : 60To
rr, the balance was maintained in an Ar atmosphere, and N 2 + Ar was adjusted to 1 atm.
【００２３】この板を１１００℃、２分間の焼鈍後、
０．２mmに冷間圧延し、８１０℃で脱炭焼鈍し、焼鈍分
離剤としてＭｇＯ中に５％のＴｉＯを添加したものを塗
布し、１２００℃、２０時間の仕上げ焼鈍を行った。ま
た比較例として、同様の成分の素材を用い、母材の溶解
および鋳片鋳造を大気中で行った。After annealing this plate at 1100 ° C. for 2 minutes,
It was cold-rolled to 0.2 mm, decarburized and annealed at 810 ° C., 5% TiO in MgO was added as an annealing separating agent, and finish annealing was performed at 1200 ° C. for 20 hours. In addition, as a comparative example, using a material having the same composition, melting of the base material and casting of the slab were performed in the atmosphere.
【００２４】本発明の雰囲気中でこの母材から繰り返し
鋳造した鋳片のＮの成分的中率（請求範囲のＮ量に鋳片
中のＮが入った割合）を、鋳片の鋳造を大気中で行った
比較例とともに表３に、このときの磁性と２次再結晶状
況を表４に示す。The N content ratio of the slab repeatedly cast from the base material in the atmosphere of the present invention (the ratio of N in the slab to the N content in the claim) is determined by the atmospheric casting of the slab. Table 3 shows the magnetic properties and the secondary recrystallization state at this time together with the comparative example performed in the above.
【００２５】[0025]
【表３】 [Table 3]
【００２６】[0026]
【表４】 [Table 4]
【００２７】[0027]
【発明の効果】本発明によれば、２次再結晶発現に重要
な役割を果たす成分を制御し、高磁束密度の一方向性電
磁鋼板を安定し製造することが可能である。EFFECTS OF THE INVENTION According to the present invention, it is possible to control the components that play an important role in the development of secondary recrystallization and to stably produce a unidirectional electrical steel sheet having a high magnetic flux density.
Claims (2)
度が８．５℃／sec 以上であって、得られた鋳片を出発
材として、これに一回あるいは中間焼鈍を含む二回以上
の冷間圧延を施して最終板厚とし、次いで脱炭焼鈍、焼
鈍分離材塗布を施した後、二次再結晶を目的とする仕上
げ焼鈍を施す一方向性電磁鋼板の製造方法にあって、溶
湯の凝固時に、溶湯周辺の雰囲気を、Ｎ2 ：１〜１００
Torr、残りはＨｅ，Ｎｅ，Ａｒ等の不活性ガスからなる
所定の雰囲気に保つことを特徴とする一方向性電磁鋼板
の製造方法。1. By weight ratio, Si: 2.3 to 4.3%, C: 0.03 to 0.10%, solAl: 0.010 to 0.065%, N: 0.0010 to 0.0150. %, Mn: 0.02 to 0.30%, S: 0.005 to 0.040% A steel sheet having the balance substantially Fe, and the solidification rate of the slab is 8.5 ° C./sec or more. As a starting material, the obtained slab is subjected to cold rolling once or twice or more including intermediate annealing to obtain a final plate thickness, and then decarburization annealing, after applying an annealing separation material, A method for manufacturing a grain-oriented electrical steel sheet subjected to finish annealing for the purpose of secondary recrystallization, wherein the atmosphere around the molten metal is N 2 : 1 to 100 during solidification of the molten metal.
A method for manufacturing a grain-oriented electrical steel sheet, characterized in that a predetermined atmosphere of Torr and the rest of it is an inert gas such as He, Ne, Ar.
〜１００Torr、残りはＨｅ，Ｎｅ，Ａｒ等の不活性ガス
からなる所定の雰囲気に保つことを特徴とする請求項１
記載の一方向性電磁鋼板の製造方法。2. The atmosphere around the slab immediately after solidification is set to N 2 : 1.
2. The method according to claim 1, wherein the predetermined atmosphere is made of an inert gas such as He, Ne, Ar or the like.
A method for producing the described unidirectional electrical steel sheet.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4085392A JPH05285592A (en) | 1992-04-07 | 1992-04-07 | Production of unidirectionally grain oriented electrical steel sheet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4085392A JPH05285592A (en) | 1992-04-07 | 1992-04-07 | Production of unidirectionally grain oriented electrical steel sheet |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH05285592A true JPH05285592A (en) | 1993-11-02 |
Family
ID=13857496
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP4085392A Withdrawn JPH05285592A (en) | 1992-04-07 | 1992-04-07 | Production of unidirectionally grain oriented electrical steel sheet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH05285592A (en) |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS54165221U (en) * | 1978-05-08 | 1979-11-20 | ||
| JPH028739U (en) * | 1988-06-30 | 1990-01-19 | ||
| JPH0231848U (en) * | 1988-08-25 | 1990-02-28 |
-
1992
- 1992-04-07 JP JP4085392A patent/JPH05285592A/en not_active Withdrawn
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS54165221U (en) * | 1978-05-08 | 1979-11-20 | ||
| JPH028739U (en) * | 1988-06-30 | 1990-01-19 | ||
| JPH0231848U (en) * | 1988-08-25 | 1990-02-28 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US3636579A (en) | Process for heat-treating electromagnetic steel sheets having a high magnetic induction | |
| JPH0774388B2 (en) | Method for manufacturing unidirectional silicon steel sheet with high magnetic flux density | |
| EP0947597B1 (en) | Method of producing a grain-oriented electrical steel sheet excellent in magnetic characteristics | |
| JPH0686631B2 (en) | Method for manufacturing unidirectional electrical steel sheet with high magnetic flux density | |
| JPS6250529B2 (en) | ||
| JP3212376B2 (en) | Manufacturing method of ultra high magnetic flux density unidirectional electrical steel sheet | |
| JP3359449B2 (en) | Manufacturing method of ultra high magnetic flux density unidirectional electrical steel sheet | |
| JPH0686630B2 (en) | Method for manufacturing unidirectional silicon steel sheet with high magnetic flux density | |
| JPH0717959B2 (en) | Method for manufacturing unidirectional high magnetic flux density electrical steel sheet | |
| JPS5836048B2 (en) | Manufacturing method of unidirectional electrical steel sheet with excellent iron loss | |
| KR950002895B1 (en) | Ultrahigh-silicon directional electrical steel sheet and production thereof | |
| US5478410A (en) | Process for producing grain-oriented electrical steel sheet having low watt loss | |
| JPH05285592A (en) | Production of unidirectionally grain oriented electrical steel sheet | |
| JPH05295440A (en) | Production of grain-oriented silicon steel sheet using rapidly solidified thin cast slab | |
| JPH06256847A (en) | Manufacture of grain-oriented electrical steel sheet having excellent magnetic characteristic | |
| JPH0686632B2 (en) | Method for manufacturing unidirectional silicon steel sheet with high magnetic flux density | |
| JPH05285593A (en) | Production of unidirectionally grain oriented electrical steel sheet by using rapidly solidified thin slab cast in specific atmosphere | |
| JP3498978B2 (en) | Manufacturing method of grain-oriented electrical steel sheet with extremely low iron loss | |
| JPH0733549B2 (en) | Method for manufacturing bidirectional silicon steel sheet | |
| JP2991613B2 (en) | Method for producing grain-oriented silicon steel sheet with good magnetic properties | |
| JPH04362132A (en) | Production of double oriented silicon steel sheet | |
| JPH07258738A (en) | Production of grain-oriented magnetic steel sheet having high magnetic flux density | |
| JP3479984B2 (en) | Unidirectional silicon steel sheet having stable magnetic properties and method of manufacturing the same | |
| JPH0617512B2 (en) | Method for producing unidirectional electrical steel sheet with extremely high magnetic flux density | |
| JPH0417618A (en) | Production of grain-oriented electrical steel sheet having excellent magnetic characteristic |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A300 | Withdrawal of application because of no request for examination |
Free format text: JAPANESE INTERMEDIATE CODE: A300 Effective date: 19990608 |