EP0411356B1 - Procédé de production d'une tôle en acier électromagnétique à grain orienté à partir d'une brame coulée en continue par laminage à chaud - Google Patents

Procédé de production d'une tôle en acier électromagnétique à grain orienté à partir d'une brame coulée en continue par laminage à chaud Download PDF

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Publication number
EP0411356B1
EP0411356B1 EP90113249A EP90113249A EP0411356B1 EP 0411356 B1 EP0411356 B1 EP 0411356B1 EP 90113249 A EP90113249 A EP 90113249A EP 90113249 A EP90113249 A EP 90113249A EP 0411356 B1 EP0411356 B1 EP 0411356B1
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Prior art keywords
grain
oriented electrical
electrical steel
rolling
slab
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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.)
Expired - Lifetime
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EP90113249A
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German (de)
English (en)
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EP0411356A3 (en
EP0411356A2 (fr
Inventor
Kishio C/O Nippon Steel Corporation Mochinaga
Kiyokazu C/O Nippon Steel Corporation Ichimura
Shinji C/O Nippon Steel Corporation Shibao
Syuji C/O Nippon Steel Corporation Kitahara
Shiro C/O Nippon Steel Corporation Ichikawa
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Nippon Steel Corp
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Nippon Steel Corp
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Priority claimed from JP15102690A external-priority patent/JPH0713268B2/ja
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Publication of EP0411356A3 publication Critical patent/EP0411356A3/en
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1222—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular fabrication or treatment of ingot or slab

Definitions

  • This invention relates to a method used in the process of producing grain-oriented electrical steel sheet, particularly to a method for hot rolling a grain-oriented electrical steel slab produced by continuous casting, and still more particularly to a method of hot rolling a grain-oriented electrical steel slab which improves the productivity of grain-oriented electrical steel sheet by enabling maximization of the width of a continuously cast slab of grain-oriented electrical steel.
  • Grain-oriented electrical steel sheet has superior magnetic properties, specifically high flux density and low core loss, and is therefore widely used as a core material for transformers and the like.
  • Heavy-reduction hot edge rolling of continuously cast slab is highly effective for increasing the productivity in terms of amount of production per unit time (ton/hr) in the continuous casting process.
  • the inventors therefore conducted a study on the production conditions in the continuous casting process for manufacturing a grain-oriented electrical steel slab containing Si (e.g. at 2.5 - 4.0%) to which the aforesaid heavy-reduction hot edge rolling is applied.
  • grain-oriented electrical steel sheet One characteristic of the production of grain-oriented electrical steel sheet is that the slab is maintained at a high temperature (e.g. 1300 °C) for a prolonged period prior to hot rolling.
  • a high temperature e.g. 1300 °C
  • flaws known as edge cracks are apt to occur in the hot rolled sheet obtained by this hot rolling and these tend to reduce product yield and lower operating efficiency during pickling and cold rolling.
  • Another object of this invention is to provide a method of hot rolling continuously cast grain-oriented electrical steel slab which enables the grain-oriented electrical steel slab to be stably and efficiently heated in an electric heating furnace after it has been subjected to heavy-reduction edge rolling.
  • Another object of this invention is to provide a method of hot rolling continuously cast grain-oriented electrical steel slab which particularly prevents the occurrence of edge cracks at the tip portion of the hot rolled sheet and enables production of grain-oriented electrical steel sheet with only an extremely small number of edge cracks throughout its entire length.
  • the present invention provides a method of hot rolling a continuously cast grain-oriented electrical steel slab that enables improvement of productivity in the continuous casting process wherein a grain-oriented electrical steel slab produced by continuous casting is heated, the heated slab is subjected to heavy-reduction edge rolling matched to the required width of a hot-rolled coil following hot rolling and the edge rolled slab is then hot rolled, the hot rolling process including the following steps:
  • the hot rolled sheet obtained in this manner is further processed into the final product by conventionally employed methods including, but not limited to, various types of annealing and cold rolling.
  • the present invention further provides a method of hot rolling a continuously cast grain-oriented electrical steel slab which further includes in the hot rolling process the following steps following the aforesaid step (4):
  • edge cracking of the tip of the hot rolled sheet can be almost totally prevented.
  • Fig. 1 is a graph showing the relationship between the furnace discharge temperature of the slab and the worst edge crack depth.
  • Fig. 2 is an explanatory view showing the formation of a dogbones by edge rolling.
  • Fig. 3 is graph showing the relationship between induced heating temperature and a MnS ( ⁇ , ⁇ phase) solid solution curve.
  • Fig. 4 is a graph showing the relationship between the temperature of the finished front surface edges in the widthwise direction of the slab and the worst edge crack depth.
  • Fig. 5 is a graph showing the relationship between temperature and thermal conductivity in materials of differing composition.
  • the inventors conducted various studies regarding the relationship between the heating temperature, heavy-reduction edge rolling, rough rolling and finish rolling of a continuously cast grain-oriented electrical steel slab and edge cracking of the resulting hot rolled sheet. The results of these studies are shown in Fig. 1.
  • the slab heating temperature the temperature of the slab upon its discharge from the heating furnace
  • the depth of the edge cracks in the hot rolled sheet become deep. This is because the grain growth is large at high heating temperature, making it easy for cracking to occur at the grain boundaries.
  • the heating temperature of the slab is less than 900 °C, the rolling resistance increases to make it difficult to carry out heavy-reduction edge rolling.
  • the present invention limits the heating temperature of the continuously cast grain-oriented electrical steel slab prior to heavy-reduction edge rolling to 900 - 1250 °C.
  • Fig. 1 The results shown in Fig. 1 were obtained by tests wherein a slab comprised of 0.07% C, 3.25% Si, 0.07% Mn, 0.01% P, 0.024% S, 0.024% Al, 0.0090% N, 0.05% Cu, 0.10% Sn and the balance substantially of Fe was initially formed to a width of 1200 mm and a thickness of 250 mm, subjected to heavy-reduction edge rolling of 100 mm, and hot rolled to obtain a hot-rolled coil of 2.5 mm thickness.
  • the heating of the continuously cast grain-oriented electrical steel slab prior to heavy-reduction edge rolling is carried out in a gas-fired heating furnace.
  • a gas-fired heating furnace is already widely used at existing facilities for the heating of continuously cast grain-oriented electrical steel slab and (c) heating by a gas-fired heating furnace is more economical than other heating methods.
  • the continuously cast grain-oriented electrical steel slab raised to a temperature of 900 - 1250 °C by the primary heating is immediately conveyed to the rolling line where it is subjected to heavy-reduction edge rolling (in one or more passes).
  • the main object of this invention is to improve the productivity in the continuous casting process.
  • the casting size of the grain-oriented electrical steel slab produced in the continuous casting process is fixed at the largest width (large thickness also of course being preferable) allowable within the restrictions dictated by the need to maintain stable casting performance, and the resulting slab is edged by the aforesaid heavy-reduction edge rolling to obtain the required hot-rolled coil width after hot rolling.
  • the grain-oriented electrical steel slab is edge rolled after being heated to 1300 °C or higher
  • the relationship between the amount of edging and the depth of the edge cracks in the hot rolled sheet is such that the depth of the edge cracks is not so large at an edge rolling reduction of not more than 60 mm.
  • the present invention pertains to edging amounts of 60 mm or greater, namely to edging amounts which at the conventionally used heating temperatures result in deep edge cracking of the hot rolled sheet. The invention thus makes it possible to conduct heavy edging, thereby enabling hot rolled sheets of desired widths to be obtained from continuously cast grain-oriented electrical steel slab of a fixed width.
  • so-called "dogbones” are formed at the upper and lower surfaces of the grain-oriented electrical steel slab which has been subjected to heavy-reduction edge rolling for obtaining a slab width appropriate for obtaining a hot rolled sheet of the desired width.
  • the grain-oriented electrical steel slab having these dogbones causes a major problem in the secondary heating.
  • the present invention uses an induction heating furnace or other type electric furnace for the secondary heating.
  • the presence of the dogbones in the grain-oriented electrical steel slab at the time it is charged into the electric heating furnace for heating would make it difficult to charge the slab into the furnace and also make it difficult to maintain it in a stable vertical posture.
  • there would be such problems as a high risk of damaging the furnace wall, non-uniform heating of the slab, and the like.
  • the present invention calls for the dogbones at the upper and lower surfaces of the grain-oriented electrical steel slab to be eliminated by rolling with horizontal rolls prior to secondary heating.
  • the secondary heating is required for causing the MnS, AlN etc. contained by the slab to enter solid solution and thus ensure that the final product will have excellent magnetic properties.
  • the temperature of this heating is limited to the range of 1300 - 1450 °C.
  • Fig. 3 shows the solid solution curve of the MnS ⁇ , ⁇ phase vs heating temperature for a material containing 0.05% Mn and 0.02% S. As can be seen from this graph, heating to a temperature of 1300 °C or higher is required for entry of an adequate amount of MnS into solid solution.
  • the temperature is lower than 1300 °C, the amount of MnS entering solid solution is insufficient, making it impossible to obtain excellent magnetic properties.
  • the heating is conducted to a temperature higher than 1450 °C, the risk of autogenous cutting arises since the temperature is near the melting temperature of the slab.
  • Japanese Published Unexamined Patent Application No. 62(1987)-130217 discloses a method wherein a slab is heated in a combustion type heating furnace to a center temperature of 900 - 1250 °C, imparted with 10 - 50% hot deformation by rough rolling, and then heated to 1350 - 1420 °C in an induction heating furnace.
  • one of the basic features of the present invention is that, with the aim of improving the productivity of a grain-oriented electrical steel slab in the continuously cast production process, the grain-oriented electrical steel slab is heated to a low temperature in a primary heating step, subjected to heavy-reduction edge rolling, rolled with horizontal rolls for eliminating the dogbones that are unavoidably produced in the heavy-reduction edge rolling step, and then heated to a high temperature in a secondary heating step. Since the aforesaid Published Unexamined Patent Application does not touch at all on this feature, the present invention and this prior art technology are unrelated.
  • the thin slab measuring not more than 100 mm in thickness, particularly the tip in the lengthwise direction thereof, is excessively cooled in the finish rolling step by heat removal through contact with the rolls or through cooling by the roll cooling water, and, as shown in Fig. 4, when the temperature at the opposite edge portions of the thin slab falls to 900 °C or lower, the edge cracks of the hot rolled thin sheet become large.
  • Fig. 4 when the temperature at the opposite edge portions of the thin slab falls to 900 °C or lower, the edge cracks of the hot rolled thin sheet become large.
  • a high Si-content steel such as the grain-oriented electrical steel with which the present invention is concerned has lower thermal conductivity than pure iron, and it is thought that when the thin slab of grain-oriented electrical steel is gripped by the rolls in finish rolling after completion of rough rolling and the temperature of the tip thereof is excessively cooled to 900 °C or below, its hot rolling deformation resistance increases sharply, giving rise to edge cracking during the ensuing finish rolling.
  • both widthwise edges at least at the tip of the thin slab (thickness ⁇ 100 mm) in the lengthwise direction are heated in an electric heating furnace to a temperature of not less than 900 °C and not more than the temperature at the center of the slab.
  • the reason for specifying the heating temperature of the widthwise edges of the thin slab to be not higher than the temperature at the center of the slab is that degradation of the magnetic properties due to insufficient precipitation of MnS would occur should the temperature of the widthwise edges of the thin slab become higher than that at the center in the widthwise direction thereof.
  • the "tip of the slab in the lengthwise direction” typically refers to the portion extending back to about 10 meters (about 1/5 of the total slab length) from the leading end of the slab, although this is not intended to be a rigid definition.
  • the heating of the opposite widthwise edge portions need only be carried out with respect to that part of these portions whose temperature has fallen to 900 °C or less, namely with respect to these portions at the tip of the slab in the lengthwise direction, it can optionally be carried out, without adverse effect, with respect to the widthwise edge portions over the entire slab length.
  • the slab is finish rolled in the conventional manner, and the result is wound into a coil to obtain a hot-rolled coil of grain-oriented electrical steel that has few edge cracks throughout its length and is of high yield.
  • the thickness of the slab prior to finish rolling is specified as being not more than 100 mm for reasons related to the finish rolling capability.
  • the respective components should preferably be within the following ranges.
  • the C content should preferably be within the range of 0.025 - 0.085% because when it is present at less than 0.025% the secondary recrystallization becomes unstable and when it is present in excess of 0.085% the time required for the decarburization annealing becomes so long as to be economically disadvantageous.
  • the Si content should preferably be in the range of 2.5 - 4.5% because when it is present at less than 2.5% it is not possible to obtain a good core loss property and when it is present in excess of 4.5% the cold rollability of the steel deteriorates markedly.
  • Mn, S, Sol.Al, N, Cu and Sn are, as required, added as inhibitor-forming elements and the contents thereof should respectively be 0.01 - 0.10%, 0.01 - 0.04%, 0.0005 - 0.065%, 0.002 - 0.010%, 0.01 -0.50% and 0.05 - 0.50%. Additionally, Sb, Bi, V, Ni, Cr and B are added as required.
  • Slabs consisting of 0.08% C, 3.25% Si, 0.07% Mn, 0.01% P, 0.028% S, 0.027% Al, 0.0090% N, 0.05% Cu, 0.05% Sn and the balance substantially of Fe and measuring 250 mm in thickness and 1200 mm in width were prepared.
  • Each slab was subjected to heating in a gas heating furnace to one of three temperatures, 1000 °C, 1200 °C and 1400 °C, to one of three degrees of edging (edge rolling), 0 mm, 100 mm and 400 mm, was thereafter horizontally rolled (either for flattening by removal of the dogbones or for reduction from a slab thickness of 250 mm to 200 mm), and then charged in an electric furnace and heated to 1400 °C.
  • This grain-oriented electrical steel sheet was then processed into a high flux density grain-oriented electrical sheet in the conventional manner by pickling, preliminary cold rolling, hot rolled sheet annealing, cold rolling to 0.220 mm, decarburization of the resulting cold rolled sheet by a conventional method, application of a freezing inhibitor, final annealing, and application of a tension coating.
  • Example 2 Slabs of the same composition and size as those in Example 1 were prepared. Each slab was subjected to heating in a gas heating furnace to one of two temperatures, 1000 °C and 1200 °C, to 400 mm edging (edge rolling), was thereafter horizontally rolled (either for flattening by removal of the dogbones or for reduction from a slab thickness of 250 mm to 200 mm), was charged in an electric furnace and heated to 1400 °C, was then subjected to about 85% or about 80% horizontal rolling until it reduced to a slab thickness of 40 mm, was charged in an electric tip portion heating furnace to have its tip portion heated to one of two temperatures, 990 °C and 1020 °C, and was rolled to a hot-rolled coil sheet thickness of 2.5 mm. The temperature of the center portion of the slab at this time was 1300 °C.
  • Example 2 The result was thereafter subjected to the same processing as in Example 1 to obtain a high flux density grain-oriented electrical sheet.
  • the worst edge crack depth, product properties and unit power consumption in the electric heating furnace of the hot-rolled coils produced by this process are shown in Table 2.
  • Each slab was subjected at a gas-heated temperature of 1200 °C to edge rolling at one of three degrees of edging, 0 mm, 100 mm and 400 mm, was thereafter horizontally rolled (either for flattening by removal of the dogbones or for reduction from a slab thickness of 250 mm to 200 mm), and then charged in an electric furnace and heated to 1400 °C and the resulting slab (thickness of 250 mm or 200 mm) was hot rolled to hot-rolled coil sheet thickness (2.5 mm).
  • This grain-oriented electrical steel sheet was then processed into a high flux density grain-oriented electrical sheet in the conventional manner by pickling, preliminary cold rolling, intermediate annealing by a conventional method, cold rolling to 0.30 mm, decarburization, application of a freezing inhibitor, final annealing, and application of a tension coating, to thereby obtain a grain-oriented electrical steel sheet.
  • the worst edge crack depth, product properties and unit power consumption in the electric heating furnace of the hot-rolled coils produced by this process are shown in Table 3.
  • Example 3 Slabs of the same composition and size as those in Example 3 were prepared. Each slab was gas heated to 1200 °C, subjected to edge rolling at an edging (rolling) amount of 400 mm, was thereafter horizontally rolled (either for flattening by removal of the dogbones or for reduction from a slab thickness of 250 mm to 200 mm), was charged in an electric furnace and heated to 1400 °C, was then subjected to about 85% or about 80% horizontal rolling, was charged in an electric tip portion heating furnace to have its tip portion heated to 950 °C, and was rolled to a hot-rolled coil sheet thickness of 2.5 mm. The temperature of the center portion of the slab at this time was 1010 °C. The result was thereafter subjected to the same processing as in Example 3 to obtain-a high flux density grain-oriented electrical sheet. The worst edge crack depth, product properties and unit power consumption in the electric heating furnace of the hot-rolled coils produced by this process are shown in Table 4.
  • the present invention enables a marked reduction in the number of edge cracks in grain-oriented electrical steel sheet and also makes it possible to subject a grain-oriented electrical steel slab to heavy-reduction edge rolling, whereby the productivity of grain-oriented electrical steel slab in the continuous casting process can be improved and the heating of the slab in an electric heating furnace following the heavy-reduction edge rolling can be carried out stably and efficiently.
  • the industrial effect of the invention is therefore great.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Electromagnetism (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
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Claims (3)

  1. Un procédé de laminage à chaud d'une brame d'acier électrique à grains orientés coulée en continu qui permet l'amélioration du rendement dans le procédé de coulée continue dans lequel une brame d'acier électrique à grains orientés produite par coulée continue est chauffée, la brame chauffée est soumise à un roulage de réduction lourde adapté à la largeur demandée d'une bobine de feuillard laminée à chaud suivant le laminage à chaud et la brame roulée est ensuite laminée à chaud, le procédé de laminage à chaud comprenant les étapes suivantes :
    (1) chauffage de la brame d'acier électrique à grains orientés dans un four de chauffage au gaz à une température dans la plage de 900-1250°C,
    (2) soumission de la brame d'acier électrique à grains orientés chauffée à un roulage de réduction lourde de pas moins de 60 mm,
    (3) élimination des épaulements de bord (dogbones) formés dans la brame d'acier électrique à grains orientés par le roulage de réduction lourde par laminage avec des rouleaux horizontaux,
    (4) chauffage de la brame aplatie d'acier électrique à grains orientés dépourvue des épaulements de bord dans un four de chauffage électrique à une température dans la plage de 1300-1450°C, et
    (5) laminage dégrossisseur et laminage de finition de la brame d'acier électrique à grains orientés chauffée électriquement à ladite température élevée.
  2. Un procédé de laminage à chaud d'une brame d'acier électrique à grains orientés coulée en continu qui permet l'amélioration du rendement dans le procédé de coulée continue dans lequel une brame d'acier électrique à grains orientés produite par coulée continue est chauffée, la brame chauffée est soumise à un roulage de réduction lourde adapté à la largeur demandée d'une bobine de feuillard laminée à chaud suivant le laminage à chaud et la brame roulée est ensuite laminée à chaud, le procédé de laminage à chaud comprenant les étapes suivantes :
    (1) chauffage de la brame d'acier électrique à grains orientés dans un four de chauffage au gaz à une température dans la plage de 900-1250°C,
    (2) soumission de la brame d'acier électrique à grains orientés chauffée à un roulage de réduction lourde de pas moins de 60 mm,
    (3) élimination des épaulements de bord (dogbones) formés dans la brame d'acier électrique à grains orientés par le roulage de réduction lourde par laminage avec des rouleaux horizontaux,
    (4) chauffage de la brame aplatie d'acier électrique à grains orientés dépourvue des épaulements de bord dans un four de chauffage électrique à une température dans la plage de 1300-1450°C,
    (5) laminage dégrossisseur de la brame d'acier électrique à grains orientés chauffée électriquement à ladite température élevée jusqu'à une épaisseur de pas plus de 100 mm,
    (6) avant le laminage de finition de la brame d'acier électrique à grains orientés dégrossie au laminoir, chauffage des deux bords dans le sens de la largeur au moins à leur extrémité dans la direction de la longueur dans un four de chauffage électrique à une température de pas moins de 900°C et pas plus de la température au centre de la brame, et
    (7) laminage de finition de la brame d'acier électrique à grains orientés maintenue à pas moins de 900°C au travers de sa largeur.
  3. Un procédé de laminage à chaud d'une brame d'acier électrique à grains orientés coulée en continu selon la revendication 1 ou 2, dans lequel le laminage horizontal est mis en oeuvre pour éliminer les épaulements de bord et pour réduire, en outre, l'épaisseur de la brame.
EP90113249A 1989-07-12 1990-07-11 Procédé de production d'une tôle en acier électromagnétique à grain orienté à partir d'une brame coulée en continue par laminage à chaud Expired - Lifetime EP0411356B1 (fr)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP179659/89 1989-07-12
JP17965989 1989-07-12
JP151026/90 1990-06-08
JP15102690A JPH0713268B2 (ja) 1989-07-12 1990-06-08 連続鋳造一方向性電磁鋼スラブの熱間圧延方法

Publications (3)

Publication Number Publication Date
EP0411356A2 EP0411356A2 (fr) 1991-02-06
EP0411356A3 EP0411356A3 (en) 1992-09-30
EP0411356B1 true EP0411356B1 (fr) 1995-11-02

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EP90113249A Expired - Lifetime EP0411356B1 (fr) 1989-07-12 1990-07-11 Procédé de production d'une tôle en acier électromagnétique à grain orienté à partir d'une brame coulée en continue par laminage à chaud

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EP (1) EP0411356B1 (fr)
CA (1) CA2020933C (fr)
DE (1) DE69023291T2 (fr)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE4311150C1 (de) * 1993-04-05 1993-12-23 Thyssen Stahl Ag Verfahren zur Herstellung von Warmband für die Erzeugung von kornorientierten Elektroblechen
DE102008029581A1 (de) 2007-07-21 2009-01-22 Sms Demag Ag Verfahren und Vorrichtung zum Herstellen von Bändern aus Silizum-Stahl oder Mehrphasenstahl
AT507475B1 (de) * 2008-10-17 2010-08-15 Siemens Vai Metals Tech Gmbh Verfahren und vorrichtung zur herstellung von warmband-walzgut aus siliziumstahl
ITRM20110528A1 (it) 2011-10-05 2013-04-06 Ct Sviluppo Materiali Spa Procedimento per la produzione di lamierino magnetico a grano orientato con alto grado di riduzione a freddo.

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
BE790798A (fr) * 1971-11-04 1973-02-15 Armco Steel Corp Procédé de fabrication de fer au silicium à orientation cube-sur-arete à partir de brames coulées
US4204891A (en) * 1978-11-27 1980-05-27 Nippon Steel Corporation Method for preventing the edge crack in a grain oriented silicon steel sheet produced from a continuously cast steel slab
JPS5942561B2 (ja) * 1980-02-13 1984-10-16 新日本製鐵株式会社 熱間圧延方法
JPS60145318A (ja) * 1984-01-09 1985-07-31 Kawasaki Steel Corp 方向性けい素鋼スラブの加熱方法
JPH0699751B2 (ja) * 1985-12-03 1994-12-07 川崎製鉄株式会社 電磁特性の良好な方向性けい素鋼板の製造方法

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CA2020933C (fr) 1993-12-21
DE69023291D1 (de) 1995-12-07
EP0411356A3 (en) 1992-09-30
EP0411356A2 (fr) 1991-02-06
CA2020933A1 (fr) 1991-01-13
DE69023291T2 (de) 1996-04-04

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