EP0619376A1 - Procédé pour la fabrication de tôles électriques à grains orientés et à perte dans le fer améliorée - Google Patents

Procédé pour la fabrication de tôles électriques à grains orientés et à perte dans le fer améliorée Download PDF

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Publication number
EP0619376A1
EP0619376A1 EP94103908A EP94103908A EP0619376A1 EP 0619376 A1 EP0619376 A1 EP 0619376A1 EP 94103908 A EP94103908 A EP 94103908A EP 94103908 A EP94103908 A EP 94103908A EP 0619376 A1 EP0619376 A1 EP 0619376A1
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EP
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Prior art keywords
temperature
slabs
rolled
hot
range
Prior art date
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Granted
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EP94103908A
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German (de)
English (en)
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EP0619376B1 (fr
Inventor
Fritz Dr. Dipl.-Phys. Bölling
Andreas Dr. Dipl.-Phys. Böttcher
Manfred Dr. Dipl.-Ing. Espenhahn
Christof Dipl.-Phys. Holzapfel
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Thyssen Stahl AG
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Thyssen Stahl AG
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1205—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving particular fabrication steps or treatments of ingots or slabs
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the working steps
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment
    • C21D8/1261—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment following 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
    • C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
    • C21D3/02—Extraction of non-metals
    • C21D3/04—Decarburising
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the working steps
    • C21D8/1233—Cold rolling

Definitions

  • the invention relates to a process for the production of grain-oriented electrical sheets with a finished strip thickness in the range from 0.1 to 0.5 mm, in which produced by a continuous casting or strip casting, more than 0.005%, preferably 0.02 to 0.10% C. , 2.5 to 6.5% Si and 0.03 to 0.15% Mn containing slabs are first heated through at a reduced temperature in one or two steps and then pre-rolled and finish-rolled to the final hot strip thickness, after which the strips that have been hot-rolled to their final thickness are annealed and accelerated, cooled and cold-rolled to the finished strip thickness in a cold rolling stage or in several cold-rolling stages, and the cold-rolled strips are then subjected to recrystallizing annealing in a humid atmosphere containing H2 and N2 with simultaneous decarburization, the application of one releasing agent essentially containing MgO on both sides of the cold strip surface, a high-temperature annealing and finally a final annealing with an insulation coating.
  • slabs preferably continuous cast slabs, with a thickness in the range from approx. 150 to 250 mm, which are usually 0.025 to 0.085% C and 2.0 to 4.0% Si as well as manganese, sulfur, if necessary Contain aluminum and nitrogen, before hot rolling in one or two stages to a temperature in the order of 1350 ° C to max.
  • This measure serves the purpose of the particles known as grain growth inhibitors and acting as a control phase in high-temperature annealing (secondary recrystallization), e.g. Bring sulfides (MnS) and nitrides (AlN) completely into solution.
  • the second heating stage up to a temperature of max. 1450 ° C and a heating of the slabs at this temperature, in order then to reduce the thickness of the slabs to hot strip with a final thickness in the range from 1.5 to about 5 mm, max. up to 7 mm warm and ready to roll.
  • the hot rolling involves at least one recrystallization rolling during finish rolling with at least one pass reduction of more than 30% in a temperature range from 960 ° C. to 1190 ° C contains, namely expressis verbis with the proviso that the inhibitors do not fail during hot rolling. Elimination of the inhibitors and, in particular, coarsening of the particles which may nevertheless be excreted are preferably avoided by this known method if the recrystallization rolling of the slabs previously heated at a temperature of at least 1350 ° C. is carried out in the temperature range from 1050 ° C. to 1150 ° C. becomes.
  • the slabs are proposed before hot rolling, ie before roughing and finishing, to a temperature of in any case greater than 1000 ° C up to max. To heat 1270 ° C and to heat at this temperature.
  • the slabs contain 1.5 to 4.5% Si and, according to the exemplary embodiments, the usual contents of carbon, manganese, aluminum and nitrogen, but preferably only a sulfur content of less than 0.007%.
  • the slabs are hot-rolled in the usual way, the hot-rolled strip is heat-treated or annealed and then also cold-rolled in a known manner in one or two stages to the final sheet thickness.
  • the cold-rolled strip is then annealed for decarburization, then a release agent is applied to both sides of the cold strip surface and finally subjected to high-temperature annealing for secondary recrystallization.
  • the lowering of the temperature required for the heating or solution annealing of the slabs and to be set in the corresponding furnaces primarily means that the formation of liquid slag in these furnaces is advantageously avoided.
  • such a reduction in the heating temperature means significant energy savings, significantly longer furnace service lives and, in particular, an improved and more cost-effective output of the heated slabs.
  • EP-A1 0 321 695, EP-A1 0 339 474, EP-A1 0 390 142, EP-A1 0 400 549) also propose methods for producing grain-oriented electrical sheets with one for warming up the temperature of the slabs is less than approx. 1200 ° C.
  • the slabs preferably contain 0.010 to 0.060% Al, but less than about 0.010% S
  • aluminum nitrides can only be incompletely dissolved in the solution annealing of the slabs.
  • the required inhibitors are therefore produced after decarburization annealing - as in the method known from EP-B1 0 219 611 - by nitriding or nitriding the strip.
  • EP-B1 0 098 324 and EP-A2 0 392 535 Processes are known from EP-B1 0 098 324 and EP-A2 0 392 535 in which the heating temperature is below 1280 ° C. and an additional process step, such as nitriding, is not absolutely necessary.
  • the secondary recrystallization is stabilized in accordance with EP-A2 0 392 535 by setting the hot rolling parameters, such as the final hot rolling temperature, the degree of deformation (based on the last three hot rolling passes) or the reel temperature.
  • This stabilization is achieved by coordinating the annealing conditions, the hot rolling and cold rolling parameters.
  • the object of the invention is to improve the method of the type mentioned at the outset with the advantageously reduced temperature for the solution annealing of the slabs in such a way that for the magnetic properties of the electrical sheets, in particular for the magnetic reversal losses P 1.7 / 50 , more favorable values can be achieved without using further process steps.
  • the slabs contain, in addition to the usual nitrogen content in the range from 0.0045 to 0.0120%, additionally 0.020 to 0.300% Cu and more than 0.010% S, but less than 0.035% Al.
  • process steps (2) and (3) according to the invention have the effect that manganese sulfides are practically not brought into solution and are therefore predominantly excreted as coarse particles after hot rolling.
  • the heating of the slabs according to (2) according to the invention has the effect that only a small proportion of aluminum nitrides are brought into solution and therefore, after hot rolling has been carried out according to (3), are also predominantly precipitated as coarse particles. This portion can also no longer act as an inhibitor in the subsequent process steps.
  • the decisive grain growth inhibitor is very finely divided copper-sulfide particles are with an average diameter of less than approx. 100 nm, preferably less than 50 nm, which in the subsequent stages or process steps represent the actual, essential and effective control phase. Only a very small proportion of aluminum nitrides which have likewise been eliminated and finely divided are effective as inhibitors after process step (4) according to the invention.
  • the slabs contain approx. 0.010 to 0.065% Al
  • the slabs also before the hot rolling at a temperature of the order of magnitude of about 1400 ° C are heated, by hot rolling and by the subsequent hot strip annealing essential inhibitor are finely divided AlN particles and such electrical sheets preferably have a magnetic induction B8 greater than 1.88 T.
  • grain-oriented electrical sheets can now be produced by the method according to the invention with the same magnetic induction B T in Tesla (T) as that of RGO and HGO electrical sheets, but with improved values for the magnetic reversal loss P 1.7 / 50 in watts per kg (W / kg).
  • slabs with an initial thickness in the range from 150 to 300 mm, preferably in the range from 200 to 250 mm are first produced using the known continuous casting method.
  • the slabs can also be so-called thin slabs with an initial thickness in the range from approximately 30 to 70 mm. In these cases, it is advantageously possible to dispense with pre-rolling to an intermediate thickness during the production of the hot strip after process step (3).
  • grain-oriented electrical sheets can also be produced from slabs or strips with an even smaller initial thickness by the method according to the invention if these slabs or strips were previously produced with the aid of strip casting.
  • slabs, thin slabs or strips contain the content of carbon, silicon, manganese, nitrogen and copper and in the preamble and in the characterizing part of patent claim 1 in comparison to the prior art (according to EP-B1 0 219 611) the sulfur content according to the invention raised in the range of more than 0.010, preferably greater than 0.015%, up to 0.050% and the aluminum content in the range which has been deliberately lowered to the lower known range from 0.010 to 0.030%, max. up to 0.035%, balance Fe including impurities.
  • the contents of aluminum and sulfur specified in claim 2 are preferably set.
  • the content of the other alloy components is preferably within the ranges specified in claim 2 for each alloy element individually or in combination.
  • tin can be added to the composition up to 0.15%, but preferably only 0.02-0.06%. This does not further improve the magnetic properties.
  • Figures 1, 2 and 3 illustrate the solution behavior for grain-oriented electrical sheets with usual Si contents. The contents taken into account correspond to the exemplary embodiments shown in Tables 1, 2 and 3.
  • Carrying out process step (2) has the effect that when the slabs are heated through before hot rolling, manganese sulfides are practically not brought into solution. Since the corresponding solubility curves for aluminum nitrides are similar or comparable to the solubility curves for manganese sulfides, the predominant proportion of aluminum nitrides is already excreted when the slabs are heated according to the invention. After completion of this process step, practically only copper sulfides are almost completely in solution.
  • process step (3) After the solution annealing of the slabs has been carried out, in process step (3) according to the invention, they are initially rough-rolled in 3 to 7 passes depending on the starting thickness of the slabs and then in 5 to 9 passes to the final hot strip thickness in the range from 1.5 to 5 mm, max. Rolled up to 7 mm.
  • the pre-rolling of slabs takes place with an initial thickness in the range from 150 to 300 mm, preferably in the range from 200 to 250 mm, except for a pre-strip thickness in the range from approx. 30 to 60 mm.
  • the number of stitches is determined during roughing and finish rolling according to the starting thickness of the slabs and according to the desired hot strip end thickness.
  • process step (3) An essential feature of process step (3), however, is that the strips are finish-rolled with the lowest possible final rolling temperature in the range from 880 ° C to 1000 ° C, preferably in the range from 900 ° C to 980 ° C.
  • the lower limit is determined by the fact that problem-free deformation or rolling of the strips without any difficulties, such as e.g. Belt unevenness and belt profile deviations must be possible.
  • process step (3) it is found after the completion of process step (3) that coarse MnS particles and a large number of coarse AlN particles with an average diameter of more than 100 nm are present in the hot strip. After the hot rolling according to the invention has ended, more than 60% of the total nitrogen content is bound to aluminum in the form of AlN.
  • N-Beeghley value A measure of the amount of nitrogen bound to aluminum is the N-Beeghley value. It is determined by a chemical method, which is described in "Analytical Chemistry, Volume 21, No. 12, December 1949". In contrast, in the processes for the production of HGO electrical sheets after solution annealing of the slabs and after hot rolling has ended, there are very few MnS particles and practically no AlN particles with this particle size (i.e. less than 100 nm).
  • Table 4 illustrates how the type and size of the excretions, and thus their effectiveness as an inhibitor, are influenced by the process according to the invention. It also shows the differences from the existing excretions, which are achieved by methods according to the state of the art (HGO, RGO).
  • the slabs must necessarily contain a sulfur content greater than 0.010%, preferably greater than 0.015%, and in any case for the precipitation of the fine copper sulfide particles hot strip annealing is to be carried out according to process step (4). If hot strip annealing (4) is omitted, there are no sufficiently large numbers of particles smaller than 100 nm, preferably smaller than 50 nm, which act as inhibitors in the subsequent process steps, because of the premature separation of coarse MnS and AlN particles due to the process steps (2) and (3).
  • the strip is cold rolled, preferably in one step, down to the finished strip thickness in the range from 0.1 to 0.5 mm.
  • the cold rolling according to claim 6 can also be carried out in two stages, wherein according to claim 7, a preheating is preferably carried out before the first cold rolling stage. This advantageously contributes to the stabilization of the secondary recrystallization in the subsequent high-temperature annealing.
  • the recrystallizing and decarburizing annealing of the strips is carried out at a temperature in the range from 750 ° C. to 900 ° C., preferably at a temperature in the range from 820 ° C to 880 ° C, in a humid atmosphere containing H2 and N2.
  • a glow separator containing primarily MgO is then applied.
  • the strips are then known in a long-term hood annealing with a slow heating of 10 to 100 K / h, preferably 15 to 25 K / h, to at least 1150 ° C at this temperature in an atmosphere consisting of H2 and N2 and slowly cooled again after holding for 0.5 to 30 h.
  • the insulation coating which is also known, is carried out with the associated final annealing.
  • Table 1 shows the results when using the method according to the invention as claimed in claim 1 on slabs with an initial thickness of 215 mm.
  • Table 2 shows further results which are achieved by the method according to the invention in accordance with claim 1 in combination with the method steps in subclaims 6 and 7. In these cases, the cold rolling took place in two stages without and also with the preheating before the first cold rolling stage.
  • grain-oriented electrical sheets can be produced which have a magnetic induction B8, as they also have grain-oriented electrical sheets of both the quality RGO and the quality HGO.
  • these grades are now only achieved by using a single method with the method steps specified in claim 1.
  • values which are substantially more favorable for the associated magnetic reversal losses are advantageously achieved. This is illustrated in FIG.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Mechanical Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Materials Engineering (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Electromagnetism (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
  • Soft Magnetic Materials (AREA)
  • Insulating Of Coils (AREA)
  • Manufacturing Of Magnetic Record Carriers (AREA)
  • Compositions Of Oxide Ceramics (AREA)
  • Processing And Handling Of Plastics And Other Materials For Molding In General (AREA)
  • Manufacture Of Macromolecular Shaped Articles (AREA)
EP94103908A 1993-04-05 1994-03-14 Procédé pour la fabrication de tÔles électriques à grains orientés et à perte dans le fer améliorée Expired - Lifetime EP0619376B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE4311151 1993-04-05
DE4311151A DE4311151C1 (de) 1993-04-05 1993-04-05 Verfahren zur Herstellung von kornorientierten Elektroblechen mit verbesserten Ummagnetisierungsverlusten

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EP0619376A1 true EP0619376A1 (fr) 1994-10-12
EP0619376B1 EP0619376B1 (fr) 1998-08-05

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EP94103908A Expired - Lifetime EP0619376B1 (fr) 1993-04-05 1994-03-14 Procédé pour la fabrication de tÔles électriques à grains orientés et à perte dans le fer améliorée

Country Status (17)

Country Link
US (2) US5711825A (fr)
EP (1) EP0619376B1 (fr)
JP (1) JP2728112B2 (fr)
KR (1) KR100247598B1 (fr)
CN (1) CN1040998C (fr)
AT (1) ATE169346T1 (fr)
AU (1) AU673720B2 (fr)
BR (1) BR9401398A (fr)
CA (1) CA2120438C (fr)
CZ (1) CZ282649B6 (fr)
DE (2) DE4311151C1 (fr)
ES (1) ES2121590T3 (fr)
HU (1) HU216760B (fr)
PL (1) PL173284B1 (fr)
RO (1) RO114637B1 (fr)
RU (1) RU2126452C1 (fr)
SK (1) SK281614B6 (fr)

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2761081A1 (fr) * 1997-03-21 1998-09-25 Usinor Procede de fabrication d'une tole d'acier electrique a grains orientes pour la fabrication notamment de circuits magnetiques de transformateurs
WO1999019521A1 (fr) * 1997-10-15 1999-04-22 Thyssen Krupp Stahl Ag Procede de production d'une tole electrique a grains orientes avec une faible perte par inversion magnetique et une polarisation elevee
CN102199696A (zh) * 2010-03-25 2011-09-28 宁波宝新不锈钢有限公司 一种特殊合金钢的预热保温生产方法
EP4589026A1 (fr) 2024-01-18 2025-07-23 Thyssenkrupp Electrical Steel Gmbh Tôle d'acier électrique à grains orientés et son procédé de fabrication

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EP0709470B1 (fr) * 1993-11-09 2001-10-04 Pohang Iron & Steel Co., Ltd. Procede de production de tole d'acier a champ electromagnetique directionnel avec chauffage de brames a basse temperature
FR2731713B1 (fr) * 1995-03-14 1997-04-11 Ugine Sa Procede de fabrication d'une tole d'acier electrique a grains orientes pour la realisation notamment de circuits magnetiques de transformateurs
DE19628137C1 (de) * 1996-07-12 1997-04-10 Thyssen Stahl Ag Verfahren zur Herstellung von kornorientiertem Elektroblech
DE19628136C1 (de) * 1996-07-12 1997-04-24 Thyssen Stahl Ag Verfahren zur Herstellung von kornorientiertem Elektroblech
IT1284268B1 (it) * 1996-08-30 1998-05-14 Acciai Speciali Terni Spa Procedimento per la produzione di lamierino magnetico a grano orientato, con elevate caratteristiche magnetiche, a partire da
IT1285153B1 (it) * 1996-09-05 1998-06-03 Acciai Speciali Terni Spa Procedimento per la produzione di lamierino magnetico a grano orientato, a partire da bramma sottile.
IT1290173B1 (it) * 1996-12-24 1998-10-19 Acciai Speciali Terni Spa Procedimento per la produzione di lamierino di acciaio al silicio a grano orientato
IT1290171B1 (it) * 1996-12-24 1998-10-19 Acciai Speciali Terni Spa Procedimento per il trattamento di acciaio al silicio, a grano orientato.
IT1290978B1 (it) * 1997-03-14 1998-12-14 Acciai Speciali Terni Spa Procedimento per il controllo dell'inibizione nella produzione di lamierino magnetico a grano orientato
IT1290977B1 (it) * 1997-03-14 1998-12-14 Acciai Speciali Terni Spa Procedimento per il controllo dell'inibizione nella produzione di lamierino magnetico a grano orientato
AU2698897A (en) * 1997-04-16 1998-11-11 Acciai Speciali Terni S.P.A. New process for the production of grain oriented electrical steel from thin slabs
WO1998046801A1 (fr) * 1997-04-16 1998-10-22 Acciai Speciali Terni S.P.A. Nouveau procede pour la production d'acier electrique a grains orientes a faible temperature
WO1998048062A1 (fr) * 1997-04-24 1998-10-29 Acciai Speciali Terni S.P.A. Nouveau procede de production d'acier electrique extremement permeable a partir de plaquettes
DE19735062A1 (de) * 1997-08-13 1999-02-18 Thyssen Stahl Ag Verfahren zur Herstellung von kornorientiertem Elektroblech und Verwendung eines Stahls für Elektroblech
IT1299137B1 (it) * 1998-03-10 2000-02-29 Acciai Speciali Terni Spa Processo per il controllo e la regolazione della ricristallizzazione secondaria nella produzione di lamierini magnetici a grano orientato
EP0947597B2 (fr) * 1998-03-30 2015-06-10 Nippon Steel & Sumitomo Metal Corporation Procédé de fabrication d'une tôle d'acier à grains orientés presentant d'excellentes caracteristiques magnétiques
DE19816158A1 (de) * 1998-04-09 1999-10-14 G K Steel Trading Gmbh Verfahren zur Herstellung von korn-orientierten anisotropen, elektrotechnischen Stahlblechen
RU2180925C2 (ru) * 1999-11-22 2002-03-27 Открытое акционерное общество "Новолипецкий металлургический комбинат" Способ производства холоднокатаной полуобработанной электротехнической стали
RU2178006C1 (ru) * 2000-08-02 2002-01-10 Открытое акционерное общество "Новолипецкий металлургический комбинат" Способ производства холоднокатаной полуобработанной электротехнической стали
KR100482208B1 (ko) * 2000-11-17 2005-04-21 주식회사 포스코 침질처리에 의한 용접구조용 강재의 제조방법
RU2202631C2 (ru) * 2001-03-23 2003-04-20 Липецкий государственный технический университет Способ получения литой стали
RU2181786C1 (ru) * 2001-07-02 2002-04-27 Цырлин Михаил Борисович Анизотропная электротехническая сталь и способ ее получения
RU2180356C1 (ru) * 2001-07-06 2002-03-10 Цырлин Михаил Борисович Способ производства холоднокатаной электротехнической анизотропной стали
RU2180357C1 (ru) * 2001-07-06 2002-03-10 Цырлин Михаил Борисович Способ производства холоднокатаной полосы из электротехнической анизотропной стали
RU2180924C1 (ru) * 2001-08-06 2002-03-27 Цырлин Михаил Борисович Способ производства электротехнической текстурованной стали с ограниченной анизотропией, полоса, полученная этим способом, и изделие из нее
RU2199595C1 (ru) * 2002-06-25 2003-02-27 Открытое акционерное общество "Новолипецкий металлургический комбинат" Способ производства холоднокатаной электротехнической анизотропной стали
KR100953755B1 (ko) * 2005-06-10 2010-04-19 신닛뽄세이테쯔 카부시키카이샤 자기 특성이 극히 우수한 방향성 전자강판의 제조 방법
EP1752549B1 (fr) * 2005-08-03 2016-01-20 ThyssenKrupp Steel Europe AG Procédé de fabrication de bande d'acier magnétique à grains orientés
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ITRM20070218A1 (it) * 2007-04-18 2008-10-19 Ct Sviluppo Materiali Spa Procedimento per la produzione di lamierino magnetico a grano orientato
CN101545072B (zh) * 2008-03-25 2012-07-04 宝山钢铁股份有限公司 一种高电磁性能取向硅钢的生产方法
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BRPI0918138B1 (pt) * 2008-09-10 2017-10-31 Nippon Steel & Sumitomo Metal Corporation Method of production of steel sheets for electric use with oriented grain
AT507475B1 (de) * 2008-10-17 2010-08-15 Siemens Vai Metals Tech Gmbh Verfahren und vorrichtung zur herstellung von warmband-walzgut aus siliziumstahl
IT1396714B1 (it) * 2008-11-18 2012-12-14 Ct Sviluppo Materiali Spa Procedimento per la produzione di lamierino magnetico a grano orientato a partire da bramma sottile.
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CA2781916C (fr) * 2009-11-25 2014-01-28 Tata Steel Ijmuiden B.V. Procede pour fabriquer une bande de tole magnetique en acier a grains orientes et tole magnetique en acier a grains orientes produite par celui
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CN102382963B (zh) * 2011-11-08 2013-11-27 北京科技大学 一种提高高硅电工钢室温塑性的热处理方法
WO2014020369A1 (fr) * 2012-07-31 2014-02-06 Arcelormittal Investigación Y Desarrollo Sl Procédé de production d'une tôle d'acier au silicium à grains orientés, tôle d'acier électrique à grains orientés et son utilisation
CN103834856B (zh) 2012-11-26 2016-06-29 宝山钢铁股份有限公司 取向硅钢及其制造方法
WO2014132354A1 (fr) * 2013-02-27 2014-09-04 Ｊｆｅスチール株式会社 Procédé de production de tôles d'acier électrique à grains orientés
CN103484643B (zh) * 2013-08-23 2015-04-15 安阳钢铁股份有限公司 一种防止取向硅钢热轧边裂的方法
JP6828820B2 (ja) * 2017-07-13 2021-02-10 日本製鉄株式会社 方向性電磁鋼板、及び方向性電磁鋼板の製造方法
JP6946848B2 (ja) * 2017-08-17 2021-10-13 日本製鉄株式会社 方向性電磁鋼板の製造方法
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CN114540714B (zh) * 2022-02-28 2022-12-27 西北工业大学 一种改善含铜取向硅钢磁性能的方法

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BR9401398A (pt) 1994-10-18
HU9400843D0 (en) 1994-06-28
CN1040998C (zh) 1998-12-02
AU673720B2 (en) 1996-11-21
RU94009842A (ru) 1996-06-27
PL173284B1 (pl) 1998-02-27
RO114637B1 (ro) 1999-06-30
DE4311151C1 (de) 1994-07-28
RU2126452C1 (ru) 1999-02-20
AU5924394A (en) 1994-10-27
CN1098440A (zh) 1995-02-08
JPH06322443A (ja) 1994-11-22
US5711825A (en) 1998-01-27
HU216760B (hu) 1999-08-30
CA2120438A1 (fr) 1994-10-06
CA2120438C (fr) 2006-06-13
DE59406591D1 (de) 1998-09-10
KR100247598B1 (ko) 2000-04-01
ATE169346T1 (de) 1998-08-15
ES2121590T3 (es) 1998-12-01
CZ67194A3 (en) 1994-12-15
JP2728112B2 (ja) 1998-03-18
HUT70224A (en) 1995-09-28
EP0619376B1 (fr) 1998-08-05
SK281614B6 (sk) 2001-05-10
US5759294A (en) 1998-06-02
SK38894A3 (en) 1994-11-09

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