EP0411356B1 - Verfahren zum Herstellen kornorientierter Elektrobleche aus Stangguss durch Warmwalzen - Google Patents
Verfahren zum Herstellen kornorientierter Elektrobleche aus Stangguss durch Warmwalzen Download PDFInfo
- 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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- EP
- European Patent Office
- Prior art keywords
- grain
- oriented electrical
- electrical steel
- rolling
- slab
- 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.)
- Expired - Lifetime
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- 229910001224 Grain-oriented electrical steel Inorganic materials 0.000 title claims description 79
- 238000000034 method Methods 0.000 title claims description 32
- 238000005098 hot rolling Methods 0.000 title claims description 27
- 238000005096 rolling process Methods 0.000 claims description 73
- 238000010438 heat treatment Methods 0.000 claims description 64
- 238000009749 continuous casting Methods 0.000 claims description 21
- 238000005485 electric heating Methods 0.000 claims description 18
- 238000004519 manufacturing process Methods 0.000 description 11
- 238000005336 cracking Methods 0.000 description 10
- 238000007688 edging Methods 0.000 description 10
- 238000005266 casting Methods 0.000 description 9
- 239000000047 product Substances 0.000 description 8
- 238000000137 annealing Methods 0.000 description 6
- 238000005097 cold rolling Methods 0.000 description 6
- 229910052799 carbon Inorganic materials 0.000 description 5
- 229910052802 copper Inorganic materials 0.000 description 5
- 230000004907 flux Effects 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 5
- 229910052748 manganese Inorganic materials 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- 229910052782 aluminium Inorganic materials 0.000 description 4
- 239000011162 core material Substances 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 229910052757 nitrogen Inorganic materials 0.000 description 4
- 229910052718 tin Inorganic materials 0.000 description 4
- 229910000831 Steel Inorganic materials 0.000 description 3
- 238000005261 decarburization Methods 0.000 description 3
- 239000012467 final product Substances 0.000 description 3
- 229910052698 phosphorus Inorganic materials 0.000 description 3
- 238000005554 pickling Methods 0.000 description 3
- 239000010959 steel Substances 0.000 description 3
- 229910052787 antimony Inorganic materials 0.000 description 2
- 239000011248 coating agent Substances 0.000 description 2
- 238000000576 coating method Methods 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 238000007710 freezing Methods 0.000 description 2
- 230000008014 freezing Effects 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- 239000003112 inhibitor Substances 0.000 description 2
- 241000722948 Apocynum cannabinum Species 0.000 description 1
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000000498 cooling water Substances 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 238000006731 degradation reaction Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 239000002893 slag Substances 0.000 description 1
Images
Classifications
-
- 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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- 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)
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Claims (3)
- Verfahren zum Warmwalzen einer stranggegossenen kornorientierten Elektrostahlbramme, welches eine Verbesserung der Produktivität beim Stranggießen ermöglicht, wobei eine mittels Strangguß erzeugte kornorientierte Elektrostahlbramme aufgeheizt wird, die aufgeheizte Bramme einer stark reduzierenden Kantenwalzung unterzogen wird, die auf die erforderliche Breite eines Warmwalzwickels nach dem Warmwalzen abgestimmt ist, und die kantengewalzte Bramme dann warmgewalzt wird, und das Warmwalzen die folgenden Schritte aufweist:(1) Aufheizen der kornorientierten Elektrostahlbramme in einem gasbefeuerten Heizofen auf eine Temperatur in dem Bereich von 900 bis 1250°C,(2) Unterwerfen der aufgeheizten kornorientierten Elektrostahlbramme einer stark reduzierenden Kantenwalzung von nicht weniger als 60 mm,(3) Beseitigen der in der kornorientierten Elektrostahlbramme durch die stark reduzierende Kantenwalzung erzeugten Hundeknochenform mittels Walzen mit horizontalen Walzen,(4) Aufheizen der flachen, kornorientierten und von den Hundeknochen befreiten Elektrostahlbramme in einem elektrischen Heizofen auf eine Temperatur in dem Bereich von 1300 bis 1450°C, und(5) Vorwalzen und Fertigwalzen der elektrisch auf diese hohe Temperatur aufgeheizten kornorientierten Elektrostahlbramme.
- Verfahren zum Warmwalzen einer stranggegossenen kornorientierten Elektrostahlbramme, welches eine Verbesserung der Produktivität beim Stranggießen ermöglicht, wobei eine mittels Strangguß erzeugte kornorientierte Elektrostahlbramme aufgeheizt wird, die aufgeheizte Bramme einer stark reduzierenden Kantenwalzung unterzogen wird, die auf die erforderliche Breite eines Warmwalzwickels nach dem Warmwalzen abgestimmt ist, und die kantengewalzte Bramme dann warmgewalzt wird, und das Warmwalzen die folgenden Schritte aufweist:(1) Aufheizen der kornorientierten Elektrostahlbramme in einem gasbefeuerten Heizofen auf eine Temperatur in dem Bereich von 900 bis 1250°C,(2) Unterwerfen der aufgeheizten kornorientierten Elektrostahlbramme einer stark reduzierenden Kantenwalzung von nicht weniger als 60 mm,(3) Beseitigen der in der kornorientierten Elektrostahlbramme durch die stark reduzierende Kantenwalzung erzeugten Hundeknochenform mittels Walzen mit horizontalen Walzen,(4) Aufheizen der flachen, kornorientierten und von den Hundeknochen befreiten Elektrostahlbramme in einem elektrischen Reizofen auf eine Temperatur in dem Bereich von 1300 bis 1450°C,(5) Vorwalzen der elektrisch auf diese hohe Temperatur aufgeheizten kornorientierten Elektrostahlbramme auf eine Dicke von nicht mehr als 100 mm,(6) vor dem Fertigwalzen der vorgewalzten kornorientierten Elektrostahlbramme, Aufheizen beider breitseitigen Seitenkanten zumindest an deren Anfang in der Längsrichtung in einem elektrischen Heizofen auf eine Temperatur von nicht weniger als 900°C und nicht mehr als die Temperatur im Kern der Bramme, und(7) Fertigwalzen der auf einer Temperatur von nicht weniger als 900°C über die gesamte Breite gehaltenen kornorientierten Elektrostahlbramme.
- Verfahren zum Warmwalzen einer stranggegossenen kornorientierten Elektrostahlbramme nach Anspruch 1 oder 2, wobei das Horizontalwalzen ausgeführt wird, um die Hundeknochenform zu beseitigen und um ferner die Dicke der Bramme zu reduzieren.
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 (de) | 1991-02-06 |
EP0411356A3 EP0411356A3 (en) | 1992-09-30 |
EP0411356B1 true EP0411356B1 (de) | 1995-11-02 |
Family
ID=26480423
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP90113249A Expired - Lifetime EP0411356B1 (de) | 1989-07-12 | 1990-07-11 | Verfahren zum Herstellen kornorientierter Elektrobleche aus Stangguss durch Warmwalzen |
Country Status (3)
Country | Link |
---|---|
EP (1) | EP0411356B1 (de) |
CA (1) | CA2020933C (de) |
DE (1) | DE69023291T2 (de) |
Families Citing this family (4)
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)
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 |
-
1990
- 1990-07-11 DE DE69023291T patent/DE69023291T2/de not_active Expired - Lifetime
- 1990-07-11 CA CA002020933A patent/CA2020933C/en not_active Expired - Lifetime
- 1990-07-11 EP EP90113249A patent/EP0411356B1/de not_active Expired - Lifetime
Also Published As
Publication number | Publication date |
---|---|
DE69023291T2 (de) | 1996-04-04 |
DE69023291D1 (de) | 1995-12-07 |
EP0411356A2 (de) | 1991-02-06 |
EP0411356A3 (en) | 1992-09-30 |
CA2020933A1 (en) | 1991-01-13 |
CA2020933C (en) | 1993-12-21 |
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