EP0732413B1 - Procédé de fabrication d'une tôle d'acier électrique à grains orientés notamment pour transformateurs - Google Patents

Procédé de fabrication d'une tôle d'acier électrique à grains orientés notamment pour transformateurs Download PDF

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Publication number
EP0732413B1
EP0732413B1 EP96400486A EP96400486A EP0732413B1 EP 0732413 B1 EP0732413 B1 EP 0732413B1 EP 96400486 A EP96400486 A EP 96400486A EP 96400486 A EP96400486 A EP 96400486A EP 0732413 B1 EP0732413 B1 EP 0732413B1
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Prior art keywords
nitrogen
less
steel
sheet
process according
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German (de)
English (en)
French (fr)
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EP0732413A1 (fr
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Jean-Claude Bavay
Luc Poissonnet
Jacques Castel
Freddy Messeant
Nadine Blanchot
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UGO
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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
    • C21D8/1205—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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/1216—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
    • C21D8/1233—Cold 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
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1255—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest with diffusion of elements, e.g. decarburising, nitriding
    • 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
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1272—Final recrystallisation annealing
    • 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 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
    • C21D8/1227—Warm 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
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1266—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest between cold rolling steps
    • 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
    • C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
    • C21D8/1283—Application of a separating or insulating coating

Definitions

  • the texture of a grain oriented electrical steel sheet is a so-called Goss texture symbolized by MILLER indices, ⁇ 110 ⁇ ⁇ 001>, that the axis ⁇ 001>, which is an axis of easy magnetization, is substantially parallel to the rolling direction and the plane ⁇ 110 ⁇ is a plane substantially parallel to the surface of the sheet.
  • This texture gives grain oriented electrical steel sheet with good properties magnetic in the rolling direction which is substantially the direction of easy magnetization.
  • B800 induction measurements acquired under a magnetic field of 800 A / m and energy losses W (1.7 / 50) of the sheet steel for a working induction of 1.7 Tesla (T) at a frequency of 50 Hertz are used in practice to assess the magnetic quality samples taken parallel to the direction of rolling of the sheet.
  • the steel of conventional sheets contains, before hot rolling, manganese, sulfur and copper.
  • High permeability sheet steel contains, before hot rolling, aluminum, manganese, copper, sulfur and nitrogen.
  • a method of producing a sheet of grain steel is known. oriented, having substantially the texture ⁇ 110 ⁇ ⁇ 001>, with high permeability in which the steel contains aluminum, manganese, copper, sulfur and nitrogen.
  • Aluminum combines with nitrogen to form aluminum nitride AIN, and manganese and copper combine with the sulfur to form manganese sulfide MnS and copper sulfide CuS.
  • the precipitates of aluminum nitride, manganese sulfide and copper sulfide inhibit normal growth of primary grains during static texturing annealing while allowing development of secondary recrystallization grains having the texture of Goss desired.
  • the heating of the steel slab before hot rolling is operated at a temperature above 1300 ° C, around 1350 to 1400 ° C to completely re-dissolve the AIN, MnS and CuS precipitates alone or in combination.
  • Their size in the state rough casting generally greater than 1 micrometer, is too coarse to allow the development of secondary recrystallization.
  • the compounds AIN, MnS and CuS reprecipitate alone or in combination in the state fine particles, with an average size of less than 150 nanometers (nm) at hot rolling and annealing before cold rolling one operation.
  • nitriding is used which has as its object the formation of fine precipitates of silicon nitride and aluminum (Si, Al) N before the start of secondary recrystallization.
  • Nitriding is carried out either by an additional heat treatment in a gaseous atmosphere containing ammonia NH 3 , or by addition of a compound containing nitrogen, such as manganese nitrides MnN, ferro-manganese FeMnN, chromium CrN, with an annealing separator mainly consisting of MgO magnesia.
  • the slabs generally contain aluminum, and optionally titanium Ti, chromium Cr, boron B, elements known for their ability to form nitrides TiN, CrN, BN. Since this process aims at precipitating fine particles (Si, Al) N at the stage of secondary recrystallization annealing, the previous presence of fine precipitates MnS and AIN is not necessary. Consequently, the re-solution of the coarse particles MnS and AIN is incomplete during the reheating of the slabs, preceding the hot rolling. In addition, an incomplete re-solution of the aluminum is essential for the precipitation of the silicon nitride.
  • Figure 1 is a curve showing the loss of mass as a function the slab reheating temperature and illustrating the formation of fusible oxides above 1300 ° C.
  • Figure 2 shows, after hot rolling, the existing relationship between the average diameter of the precipitates and the sulfur percentage of steel.
  • Figure 3 presents after decarburization, the precipitate densities depending on the stop temperature of the recrystallization annealing secondary.
  • the present invention relates to the use of a steel of composition following determined weight: carbon of between 0.02 and 0.09%, silicon between 2.5 and 4%, copper between 0.06 and 0.50% and a selection, manganese between 0.027 and 0.17%, sulfur between 0.007 and 0.020%, aluminum between 0.010 and 0.030%, nitrogen between 0.004 and 0.012%, the rest being iron and impurities, composition submitted, after preparation by casting continues from the slab or strip to a full reheating to a temperature equal to or less than 1300 ° C.
  • the manganese, sulfur, aluminum and nitrogen are chosen in very narrow ranges, which allows the almost total solution and sufficient quantity of AIN, MnS and CuS precipitates taken alone or in combination, during reheating of the slabs, before hot rolling, to an equal temperature or lower than 1300 ° C which prevents the surface formation of oxides fuses.
  • the precipitates containing sulfur and or most of the nitrogen is put back into solution when the slabs as a result of the adaptation of the chemical composition to the lower reheating temperature.
  • the main inhibitor is nitride of aluminum which precipitates little during hot rolling and essentially during the annealing of the hot-rolled sheet in the form fine particles with an average diameter of less than 100 nanometers.
  • the manganese sulfide is a complementary inhibitor. Copper has in particular a refining effect of the size of these AIN and MnS precipitates with which it can be associated. CuS precipitates that trap part of the sulfur of the steel at the hot rolling stage contributes to the reduction of the mean diameter of the precipitates as shown in Figure 2.
  • the oriented grain steel according to the invention having undergone the stages of manufacturing described above, contains from 0.02 to 0.09% carbon, 2.5 to 4% silicon, 0.027 to 0.17% manganese, 0.007 to 0.020% sulfur, 0.010 to 0.030% aluminum, 0.004 to 0.012 % nitrogen, 0.06% to 0.50% copper, and optionally up to 0.15% tin, the rest being iron and impurities.
  • the product resulting from the multiplication of the sulfur content by the manganese content is less than or equal to 160.10 -5 : (% S) x (% Mn) ⁇ 160.10 -5
  • the product resulting from the multiplication of the nitrogen content by the aluminum content is less than 240.10 -6 : (% N) x (% Al) ⁇ 240.10 -6
  • the percentage of nitrogen precipitated after hot rolling, in the form of fine particles with an average diameter of less than 100 nanometers, is less than 40%.
  • the percentage of nitrogen precipitated, after hot rolling and annealing, in the form of fine particles with an average diameter of less than 100 nanometers, is greater than 60%.
  • the magnesia used as a separator during the annealing of secondary recrystallization and of purification at high temperature may contain, alone or as a mixture, sulfur or one or more sulfur or nitrogen compounds chosen from magnesium sulfate and / or manganese sulfate and / or sodium thiosulfate, and / or urea, one or more sulfur and nitrogen compounds chosen from, amidosulfuric acid, (sulphamic acid) and / or ammonium sulfate and / or ammonium thiosulfate, antimony chloride, boron or a compound of boron and titanium dioxide.
  • Figure 2 shows, after hot rolling, the relationship between the average diameter of the precipitates and the percentage of sulfur in the steel, in the case of an almost total solution of all the precipitates when reheating the slab.
  • the sulfur content according to the present invention is limited to 0.020%.
  • the fine precipitates MnS playing an active role of secondary inhibitor during secondary recrystallization annealing the sulfur content must be at less than 0.007% to obtain a sufficient amount of these rushed.
  • the manganese content according to the present invention must be higher at 0.027% to obtain precipitation of a sufficient amount of ends MnS precipitates exerting an inhibitory effect and having an availability in free manganese in the case of sulfur supply via the additive channel to the magnesia for strengthening the inhibitory power of MnS precipitates. It is limited to 0.17% to avoid the presence of precipitation coarse MnS in slabs and incomplete solution during reheating between 1200 and 1300 ° C before hot rolling.
  • compliance with the condition [% S] x [% Mn] ⁇ 160.10 -5 promotes the presence of fine MnS precipitates in the slabs and their redissolution between 1200 ° C and 1300 ° C before hot rolling .
  • the nitrogen content must be greater than 0.004% in order to obtain sufficient precipitation of fine precipitates AIN, main inhibitor, during the annealing of the hot-rolled sheet.
  • the nitrogen content is limited to 0.012% to avoid the formation of blistering on the surface of the steel.
  • the condition (% N) x (% Al) ⁇ 240.10 -6 allows almost complete dissolution of the AIN precipitates when reheating the slabs between 1200 ° C and 1300 ° C before hot rolling.
  • the aluminum content must be equal to or greater than 0.010% on the one hand, so that the amount of AIN precipitates formed during the annealing of the hot-rolled sheet is sufficient, AIN being the main inhibitor and on the other hand, to have an availability in free aluminum, in the case of nitrogen supply via the additive channel to the magnesia for strengthening the inhibitory power of AIN precipitates.
  • Aluminum content is less than 0.030% to avoid precipitation coarse AIN particles during the final stage of hot rolling.
  • steel can contain up to 0.15% tin which exerts a beneficial effect on inhibition.
  • the density of inhibitory precipitates containing either sulfur and manganese or nitrogen and aluminum may be insufficient to obtain recrystallization complete secondary and homogeneous magnetic quality.
  • it is, of preferably, added to magnesia one or more compounds containing sulfur and or nitrogen or antimony which allow the formation of a complement of inhibitors, either based on sulfur and manganese, or based nitrogen and aluminum, either antimony-based during the rise temperature preceding the start of secondary recrystallization.
  • the present invention is illustrated from the observations and following examples, table 1 giving the chemical composition of tested steels.
  • Steels 2 to 5 and 7 are steels according to the present invention.
  • Steels 1, 6, 8 and 9 are reference steels.
  • Content phosphorus, residual element, according to the present invention, is less than 0.015%.
  • Steel No. 1 is a reference steel containing 0.021% sulfur and 0.030% aluminum (Steel No. 1, Table 1), a slab of which has been reheated to 1400 ° C before hot rolling, so as to dissolve the majority of AIN, MnS, CuS precipitates of coarse size.
  • the cold rolling was carried out according to the invention, in a single operation after annealing of the hot rolled sheet at 1120 ° C.
  • the annealing separator consisted of magnesia containing 0.080% boron and 1.2% of the titanium element in the form of titanium dioxide TiO 2 .
  • magnesium sulfate, manganese, sodium thiosulfate helps strengthen inhibition by precipitates containing manganese and sulfur at during secondary recrystallization annealing.
  • magnesia of a nitrogenous compound allows to introduce nitrogen into the steel which reinforces the inhibition by the precipitates containing nitrogen and aluminum.
  • magnesia of a sulfur and nitrogen compound (ammonium thiosulfate, amidosulfuric acid which contains both 33% sulfur and 14% nitrogen) allows sulfur to be introduced into the steel and nitrogen to reinforce the inhibition by the precipitates containing, on the one hand, manganese and sulfur and, on the other hand, nitrogen and aluminum.
  • the beneficial effect of nitrogen associated with sulfur is illustrated by the fact that the percentage of sulfur used in example 5 is lower than that used in example 4.
  • ammonium sulfate to magnesia also allows a simultaneous supply of sulfur and nitrogen.
  • antimony chloride to magnesia allows the introduction into the steel of the antimony element, which by segregating at the grain boundaries, acts as an inhibitor.
  • a water-soluble sulfur compound is preferred to the possible addition of insoluble elemental sulfur since the dispersion in milk of magnesia is more homogeneous.
  • the addition, to magnesia, of compounds containing sulfur, nitrogen and antimony promotes the obtaining of a homogeneous magnetic quality over the length of the strip of coiled sheet.
  • Table 2 shows that according to the invention, the percentage of nitrogen precipitated in the hot rolled sheet is less than 40%.
  • Lowering winding temperature significantly reduces the percentage of precipitated nitrogen, up to less than 5% in the case of steel n ° 3 reheated to 1280 ° C, hot rolled and coiled to 530 ° C. At this winding temperature, the percentage of precipitated nitrogen remains very low when the slab reheating temperature drops from 1280 ° C to 1240 ° C, usual temperature for reheating carbon steels.
  • the amount of nitrogen combined with aluminum was determined from dosing of precipitated aluminum.
  • Table 3 shows that according to the invention, the percentage of nitrogen precipitate is greater than 60% after annealing the hot-rolled sheet to 950 ° C.
  • Table 4 shows that, according to the invention, the average diameter precipitates containing nitrogen and aluminum, obtained by annealing 160 seconds from hot rolled sheet steel n ° 2, wound at 530 ° C, is less than 50 nanometers in a wide temperature range of annealed.
  • Nitrogen and aluminum precipitates can therefore play an active role as an inhibitor.
  • Table 5 gives the average diameter and density of the precipitates after heating the steel slab n ° 2 to 0.15% copper to 1280 ° C, hot rolling 2.3 mm thick and coiling at 640 ° C.
  • Figure 3 shows the evolution of the density of the CuS precipitates and MnCuS after decarburization and during recrystallization annealing secondary of steel n ° 6 which does not contain aluminum, composition chosen to facilitate counting of precipitates by microscopy electronic transmission.
  • This steel whose slabs were reheated to 1400 ° C, underwent two cold rolling operations with intermediate annealing at 950 ° C, the reduction rate of the second rolling at cold being 60%.
  • the fine CuS precipitates dissolve gradually before secondary recrystallization which occurs around 950 ° C, the release of sulfur accompanied by a fine precipitation of MnS particles.
  • the particles identified under the electron microscope are MnCuS because copper precipitates on the MnS particles during cooling. According to this invention, fine CuS particles do not play a decisive inhibitory role for the development of secondary recrystallization.
  • the percentage of CuS precipitates in diameter mean less than 100 nm is less than 3% of the total population, after annealing of hot rolled sheet.
  • MnS precipitates formed after decarburization and before secondary recrystallization which reinforce inhibition by precipitates containing nitrogen and aluminum.
  • the copper content must be greater than 0.06% to obtain fine precipitation at the hot rolled stages and hot rolled and annealed.
  • the increase in the copper content favors refinement of precipitation.
  • the copper content is limited to 0.50% to avoid the problems of pickling the sheet obtained.
  • the level of losses decreases and that the level of B800 increases as a function of the reduction in the mass oxygen content of the surface oxide film formed during the decarburization operation.
  • the lowering of the oxygen content of the surface oxide film mainly consisting of silica and containing less than 20% of iron oxide, below 800.10 -4 % (approximately 1.8 g of oxygen per m 2 ) allows an improvement in magnetic properties, all the more marked as this reduction is high.
  • the method of the present invention described for slabs of continuous casting with thickness between 150 and 300 mm can be applied to thinner slabs, thickness between 15 and 100 mm approx.
  • the method of the present invention can also be applied to thin strips obtained by casting liquid steel between two rollers, thicker than 2 mm, the strips being heated between 1200 ° C and 1300 ° C, before undergoing hot rolling.
  • the number of passes of preliminary hot rolling and finishing hot rolling is a function of the thickness of the product cast in continuous and the thickness referred to in the hot rolled state. If the thickness of the continuously cast product is sufficiently low, hot rolling preliminary can be deleted.
  • the total duration of the heating cycle for the continuously cast product is a function of its thickness. The smaller this thickness, the faster the reheating temperature is reached at heart.

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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)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
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  • Manufacturing Of Steel Electrode Plates (AREA)
  • Soft Magnetic Materials (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
EP96400486A 1995-03-14 1996-03-08 Procédé de fabrication d'une tôle d'acier électrique à grains orientés notamment pour transformateurs Expired - Lifetime EP0732413B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR9502916A FR2731713B1 (fr) 1995-03-14 1995-03-14 Procede de fabrication d'une tole d'acier electrique a grains orientes pour la realisation notamment de circuits magnetiques de transformateurs
FR9502916 1995-03-14

Publications (2)

Publication Number Publication Date
EP0732413A1 EP0732413A1 (fr) 1996-09-18
EP0732413B1 true EP0732413B1 (fr) 2001-09-26

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EP (1) EP0732413B1 (zh)
JP (1) JPH10500454A (zh)
KR (1) KR970702932A (zh)
CN (1) CN1148411A (zh)
AT (1) ATE206171T1 (zh)
BR (1) BR9605937A (zh)
CZ (1) CZ284873B6 (zh)
DE (1) DE69615429T2 (zh)
ES (1) ES2161988T3 (zh)
FR (1) FR2731713B1 (zh)
PL (1) PL317155A1 (zh)
PT (1) PT732413E (zh)
WO (1) WO1996028576A1 (zh)

Families Citing this family (25)

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Publication number Priority date Publication date Assignee Title
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
IT1290171B1 (it) * 1996-12-24 1998-10-19 Acciai Speciali Terni Spa Procedimento per il trattamento di acciaio al silicio, 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
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
FR2761081B1 (fr) * 1997-03-21 1999-04-30 Usinor Procede de fabrication d'une tole d'acier electrique a grains orientes pour la fabrication notamment de circuits magnetiques de transformateurs
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
AU2701197A (en) * 1997-04-24 1998-12-11 Acciai Speciali Terni S.P.A. New process for the production of high-permeability electrical steel fr om thin slabs
DE19816158A1 (de) * 1998-04-09 1999-10-14 G K Steel Trading Gmbh Verfahren zur Herstellung von korn-orientierten anisotropen, elektrotechnischen Stahlblechen
CA2287658C (en) * 1998-10-27 2009-01-13 Kawasaki Steel Corporation Electromagnetic steel sheet and process for producing the same
EP1162280B1 (en) * 2000-06-05 2013-08-07 Nippon Steel & Sumitomo Metal Corporation Method for producing a grain-oriented electrical steel sheet excellent in magnetic properties
IT1316029B1 (it) * 2000-12-18 2003-03-26 Acciai Speciali Terni Spa Processo per la produzione di acciaio magnetico a grano orientato.
CN100389222C (zh) * 2005-12-13 2008-05-21 武汉钢铁(集团)公司 提高含铜取向硅钢电磁性能和底层质量的生产方法
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
CN101643881B (zh) * 2008-08-08 2011-05-11 宝山钢铁股份有限公司 一种含铜取向硅钢的生产方法
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.
JP5353234B2 (ja) * 2008-12-26 2013-11-27 Ｊｆｅスチール株式会社 方向性電磁鋼板の製造方法
JP5434438B2 (ja) * 2009-09-30 2014-03-05 Ｊｆｅスチール株式会社 一方向性電磁鋼板の製造方法
JP6009438B2 (ja) * 2010-06-10 2016-10-19 タタ、スティール、アイモイデン、ベスローテン、フェンノートシャップＴａｔａ Ｓｔｅｅｌ Ｉｊｍｕｉｄｅｎ Ｂｖ オーステナイト鋼の製造方法
CN102071303B (zh) * 2011-01-30 2012-11-21 中冶南方(武汉)威仕工业炉有限公司 带钢在硅钢连续退火干燥炉的穿带方法
CN103667602B (zh) * 2013-11-26 2015-04-08 山西太钢不锈钢股份有限公司 一种晶粒取向电工钢rh精炼钢水增氮方法
CZ2014325A3 (cs) * 2014-05-12 2015-11-11 Arcelormittal Ostrava A.S. Pás z orientované transformátorové oceli a způsob jeho výroby
CN106048411A (zh) * 2016-06-27 2016-10-26 马鞍山钢铁股份有限公司 一种变压器用冷轧取向电工钢及其生产方法
CN111020140A (zh) * 2019-12-17 2020-04-17 无锡晶龙华特电工有限公司 一种磁性优良取向硅钢氧化镁退火隔离剂及其涂覆工艺
CN112522609B (zh) * 2020-11-18 2021-12-14 武汉钢铁有限公司 一种含复合抑制剂的高磁感取向硅钢及生产方法

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FR2731713A1 (fr) 1996-09-20
PT732413E (pt) 2002-03-28
ES2161988T3 (es) 2001-12-16
PL317155A1 (en) 1997-03-17
DE69615429D1 (de) 2001-10-31
EP0732413A1 (fr) 1996-09-18
FR2731713B1 (fr) 1997-04-11
WO1996028576A1 (fr) 1996-09-19
CZ368496A3 (en) 1997-04-16
CZ284873B6 (cs) 1999-03-17
ATE206171T1 (de) 2001-10-15
DE69615429T2 (de) 2002-06-20
KR970702932A (ko) 1997-06-10
BR9605937A (pt) 1997-08-12
CN1148411A (zh) 1997-04-23
JPH10500454A (ja) 1998-01-13

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