EP1473371B1 - Verfahren zum Herstellen nicht kornorientierter Elektrobleche und nach diesem Verfahren hergestellte Bleche - Google Patents

Verfahren zum Herstellen nicht kornorientierter Elektrobleche und nach diesem Verfahren hergestellte Bleche Download PDF

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Publication number
EP1473371B1
EP1473371B1 EP04014453A EP04014453A EP1473371B1 EP 1473371 B1 EP1473371 B1 EP 1473371B1 EP 04014453 A EP04014453 A EP 04014453A EP 04014453 A EP04014453 A EP 04014453A EP 1473371 B1 EP1473371 B1 EP 1473371B1
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Prior art keywords
strip
temperature
sheet
annealing
rolled
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Expired - Lifetime
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EP04014453A
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English (en)
French (fr)
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EP1473371A3 (de
EP1473371A2 (de
Inventor
Philippe Poiret
André Bertoni
Jean-Claude Bavay
Jacques Hernandez
Jean Verdun
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ArcelorMittal France SA
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Arcelor France SA
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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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C21D8/1216—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
    • 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
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • H01F1/14775—Fe-Si based alloys in the form of sheets
    • 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
    • C21D8/1266—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 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 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
    • C21D8/1272—Final recrystallisation annealing
    • 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
    • C21D8/1277—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 a particular surface treatment

Definitions

  • the present invention relates to a method of manufacturing non-oriented grain magnetic steel sheet.
  • non-oriented grain magnetic sheets ie having isotropic magnetic properties are particularly intended for the construction of electromagnetic devices in which the magnetic flux generated by the electric windings is not constant, as for example in machines rotating.
  • Some transformers used in the field of household appliances use this type of sheet for economic reasons.
  • These electromagnetic devices consist of cut and assembled sheets.
  • the plates have an efficiency which is evaluated according to two parameters which are the induction, on the one hand, and the specific losses, on the other hand.
  • the induction is limited by the saturation magnetization of the sheets and this magnetization is all the higher as the steel is rich in iron.
  • the addition of alloying elements in the steel results in an increase in the electrical resistivity, the function of which is to reduce the eddy current losses.
  • the evacuation of the steel vacuum improves on the one hand, cleanliness and purity of the steel and on the other hand, to reduce losses by hysteresis.
  • Patent EP 0 469 980 discloses a method used in the field of the manufacture of non-oriented grain magnetic sheets, the process comprising successively, after vacuum forming of a steel, a hot rolling operation followed by a winding, rapid annealing said parade hot-rolled sheet, an optional shot blasting operation, a stripping operation, a cold rolling operation in one or more steps followed by annealing, the final annealing being carried out under an atmosphere controlled, decarburizing if necessary.
  • the sheets obtained by this method for a final thickness of about 0.50 millimeters, have specific losses of less than 6.5 W / Kg under an induction of 1.5 Tesla and a frequency of 50 Hertz as well as a higher magnetization at 1.74 Tesla under an electric field of 5000 A / m.
  • the total mass losses are less than 7.5 W / Kg under an induction of 1.5 Tesla and a frequency of 50 Hertz.
  • the magnetization is greater than 1.75 Tesla under a field of 5000 A / m.
  • the object of the invention is to improve the magnetic characteristics of non-oriented grain sheets made with a steel containing only very little silicon, that is to say to reduce the magnetic losses and to increase the magnetization under a field. electrical determined.
  • the single figure shows a magnetization curve as a function of the cold rolling rates, the cold rolling being carried out in a single operation.
  • the steel according to the invention has a silicon mass content of less than 0.5%, and a manganese content of less than 0.5% to obtain a high permeability.
  • Thermal conductivity is an important parameter in the construction of electrical machines. Indeed, the Joule energy losses in the materials are discharged to the outside via the magnetic circuit consisting of stacked cut sheets. The addition of silicon, manganese and aluminum in the iron results in a decrease in the thermal conductivity.
  • the steel must be unalloyed or very little alloyed, the low silicon, manganese and aluminum content of the steel according to the invention makes it possible to limit the heating of the engines which is detrimental to the good holding insulation insulating conductors.
  • the better evacuation of the calories can also allow an increase of the mass power, by the increase of the levels of induction, without increase of the temperature.
  • composition of the invention by virtue of the thermal conductivity which it confers on the steel, provides cooling by thermal conduction of the electrical devices.
  • the steel is slab-cast, then the slab is hot-rolled with a reheat temperature below 1300 ° C, and a hot-roll end temperature below 950 ° C.
  • the hot-rolled sheet is wound at a temperature greater than 550 ° C., and then subjected to static annealing at a temperature of between 700 and 1050 ° C. for a time greater than 1 hour.
  • the web may undergo an optional shot blasting operation prior to being stripped.
  • the stripped strip is cold-rolled, with a reduction rate of between 25 and 90%, in a single cold rolling operation to a thickness of less than or equal to 1.5 mm, and then it undergoes a final annealing carried out at parade.
  • the final annealing is carried out preferably at a temperature between 700 and 1050 ° C, for a time less than 10 min.
  • mass magnetic losses can be reduced below 4.5 W / Kg for a sheet metal thickness of 0.35 mm, below 5.30 W / Kg for a sheet thickness of 0.50 mm, below 7 W / Kg for a sheet thickness of 0.65 mm, below 12.5 W / Kg for a sheet thickness of 1 mm and to obtain a magnetization equal to or greater than 1.77 Tesla by performing a static annealing of the hot-rolled sheet strip, associated with a cold rolling in a single operation followed by a continuous annealing at the parade.
  • a No. 4 steel slab whose chemical weight composition is given in Table 1 is heated to 1173 ° C. and then subjected to a first hot rolling with a reduction rate of 86% and a second hot rolling with a 93% reduction.
  • the hot rolling end temperature is 843 ° C
  • the hot rolled strip is wound at the temperature of 738 ° C.
  • the coil sheet was subjected to static annealing at 800 ° C for 10 hours under an atmosphere of hydrogen or hydrogen and nitrogen.
  • the sheet is then cold rolled with a reduction rate of 80% to obtain a sheet of thickness of 0.50 mm.
  • the final annealing is carried out at a temperature of 880 ° C. for 2 minutes under a nitrogen and hydrogen atmosphere.
  • a No. 4 steel slab, the weight composition of which is given in Table 1, is treated in the same way as the steel of Example 1, that is to say with the same rates of heat reduction and Cold.
  • the reheating temperature of the slab is 1185 ° C
  • the hot rolling end temperature is 857 ° C.
  • the hot rolled strip is wound at a temperature of 636 ° C.
  • a portion of the coil is subjected to static annealing at 800 ° C for 10 hours under an atmosphere of hydrogen or hydrogen and nitrogen.
  • the sheet is then cold rolled to obtain a sheet of 0.50 mm thick.
  • the final annealing is carried out at a temperature of 880 ° C. for 2 minutes under a nitrogen and hydrogen atmosphere.
  • a No. 4 steel slab, the weight composition of which is given in Table 1, is treated in the same way as the steel of Example 1, that is to say with the same rates of heat reduction and Cold.
  • the reheating temperature of the slab is 1221 ° C
  • the hot rolling end temperature is 910 ° C.
  • the hot-rolled strip is wound at 785 ° C.
  • the coil sheet was subjected to static annealing at 800 ° C for 10 hours under an atmosphere of hydrogen or hydrogen and nitrogen.
  • the sheet is then cold rolled to obtain a sheet of 0.50 mm thick.
  • the final annealing is carried out at a temperature of 880 ° C. for 2 minutes under a nitrogen and hydrogen atmosphere.
  • steel No. 2 whose composition is given in Table 5, which comprises in its composition a manganese content of 0.87% leads to magnetic properties identical to those in Table 4.
  • the manganese content must however be limited to less than 0.5% to improve the thermal conductivity.
  • a section of the hot-rolled sheet metal coil obtained under the conditions described in Example 2 is subjected to static annealing at a temperature of 710 ° C. for 40 hours under an atmosphere of hydrogen or nitrogen and hydrogen. .
  • a No. 4 steel slab whose weight composition is given in Table 1 is treated in the same way as in Example 1, that is to say with the same reduction rates under hot and cold conditions.
  • the No. 4 steel slab is heated to 1188 ° C, the hot rolling end temperature is 816 ° C.
  • the hot-rolled sheet strip is wound at a temperature of 702 ° C.
  • a coil sheet section is subjected to static annealing at 1000 ° C for 10 hours under an atmosphere of hydrogen or hydrogen and nitrogen.
  • the sheet is then cold rolled to obtain a sheet of 0.50 mm thick.
  • the final annealing is carried out at a temperature of 880 ° C. for 2 minutes under a nitrogen and hydrogen atmosphere.
  • the magnetic characteristics obtained are presented in Table 7. ⁇ b> TABLE 7. ⁇ / b> W 1.5 / 50 (W / kg) B5000 ( You're here ) Sheet of 0.50 mm thickness according to the invention 4.59 1.80
  • a section of the hot-rolled sheet metal coil obtained under the conditions described in Example 2 is subjected to static annealing at the temperature of 740 ° C. for 40 hours under an atmosphere of hydrogen or of hydrogen and of nitrogen. After annealing the section is divided into four parts which are respectively cold rolled with a reduction rate of 60%, 74%, 80% and 86% to obtain a sheet of 1 mm 0.65 mm, 0.50 mm, and 0.35 mm thick.
  • the sheet 0.5 mm thick and the sheet 0.35 mm thick are annealed at a temperature of 880 ° C for 2 minutes.
  • the sheet 0.65 mm thick is annealed at a temperature of 880 ° C for 2 minutes 30 seconds.
  • the sheet 1 mm thick is annealed at a temperature of 880 ° C for 3 minutes 40 s.
  • the single figure shows that the cold rolling rate must be less than 90% to obtain a magnetization equal to or greater than 1.77 Tesla when static annealing is performed after hot rolling.
  • annealing carried out on magnetic cores made by cutting and stacking the sheet according to the invention generates a reduction in losses without degradation. magnetization, the annealing being intended to eliminate the internal stresses due to cutting. It is thus possible to produce sheets having a final thickness of 0.35 mm, which after post-cutting annealing have magnetic losses of less than 4.0 W / Kg with a magnetization equal to or greater than 1.77 Tesla. It is thus possible to produce sheets having a final thickness of 0.50 mm, which after post-cutting annealing have mass losses of less than 4.70 W / kg with a magnetization equal to or greater than 1.77 Tesla.
  • the invention comprises the following steps: a static annealing before cold rolling, a cold rolling in a single operation, a final annealing as shown in Examples 1, 2, 3, 4, 5 and 6. After cutting the elements of circuit and stack, an annealing of elimination of internal stresses is performed on said circuits.
  • the sheet undergoes stripping annealing at a temperature above 650 ° C, for a time greater than 3 minutes.
  • Epstein test pieces having a thickness of 0.35 mm, 0.50 mm, 0.65 mm and 1 mm, used to measure the magnetic characteristics of the sheets presented in Examples 1, 3, 4 and 5, were subjected to an annealing of 750 ° C for 2 hours under an atmosphere of nitrogen and hydrogen.
  • the Epstein test pieces used in Example 6 to measure the magnetic characteristics are subjected to annealing at 750 ° C. for two hours under a nitrogen and hydrogen atmosphere.
  • the magnetic characteristics obtained are presented in Table 9. ⁇ b> Table 9. ⁇ / b> W 1.5 / 50 (W / kg) B5000 ( You're here ) Sheet of 0.35 mm thick. 3.37 1.78 Sheet of 0.5 mm thick. 3.94 1.79 Sheet of 0.65 mm thick. 5.36 1.80 Sheet 1 mm thick according to the invention.
  • the sheet according to the invention is produced with static annealing after hot rolling, it is thus possible to obtain sheets having a final thickness of 0.35 mm, 0.50 mm, 0.65 mm and 1 mm and which, after post-cutting annealing respectively have mass losses of less than 4 W / Kg, 4.70 W / kg, 6 W / Kg and 11.5 W / Kg, and a magnetization equal to or greater than 1.77 Tesla.
  • the sheet according to the invention When the sheet according to the invention is hot rolled and subjected to a long-lasting static annealing followed by a single cold rolling, it has a thickness of 0.50 mm and 0.65 mm, a significant reduction in losses. mass and an improvement of the magnetization ability.
  • the sheet obtained by the process can be subjected, after cutting and assembly of the magnetic circuits, to stress-relieving annealing.
  • This annealing of elimination of stresses due to cutting causes a significant reduction in losses without degradation of the magnetization ability, with static annealing of the hot-rolled strip and then cold-rolled in a single operation.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Materials Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Mechanical Engineering (AREA)
  • Electromagnetism (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Dispersion Chemistry (AREA)
  • Power Engineering (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
  • Inorganic Insulating Materials (AREA)
  • Processing And Handling Of Plastics And Other Materials For Molding In General (AREA)
  • Soft Magnetic Materials (AREA)

Claims (3)

  1. Verfahren zum Herstellen nicht kornorientierter Elektrobleche, folgende Schritte umfassend :
    - Herstellen unter Vakuum eines Stahls folgender Zusammensetzung:
    Kohlenstoff < 0,01 %,
    Silicium < 0,5 %,
    Mangan, von 0,05 bis 0,5 %,
    Aluminium < 0,03 %,
    Phosphor < 0,20 %,
    Schwefel < 0,015 %,
    Stickstoff < 0,01 %,
    Sauerstoff < 0,01 %,
    wobei es sich bei dem Rest um Eisen und unvermeidliche Verunreinigungen handelt,
    - Formen des Stahls zu einer Bramme,
    - Warmwalzen der Bramme, wobei die Erhitzungstemperatur niedriger als 1300 °C ist und die Temperatur am Ende des Warmwalzvorgangs niedriger als 950 °C ist,
    - Aufrollen des warmgewalzten Bandes bei einer Temperatur von mehr als 550 °C,
    - Haubenglühen des aufgerollten Bandes bei einer Temperatur zwischen 700 und 1050 °C für mehr als eine Stunde,
    - eventuelles Kugelstrahlen des geglühten Bandes,
    - Beizen des geglühten und eventuell kugelgestrahlten Bandes, und anschließendes
    - Kaltwalzen des gebeizten Bandes in einem einzigen Kaltwalzdurchgang zu einer Dicke von höchstens 1,5 mm, wobei die Abnahme zwischen 25 und 90 % beträgt,
    - Fertigglühen des kaltgewalzten Bandes im Durchlaufverfahren, und anschließendes
    - Schneiden des Bandes zu Blechen und Glühen der Bleche zur Entspannung.
  2. Verfahren nach Anspruch 1, dadurch gekennzeichnet, dass das Fertigglühen im Durchlaufverfahren weniger als 10 Minuten lang bei einer Temperatur zwischen 700 und 1050 °C durchgeführt wird.
  3. Verfahren nach den Ansprüchen 1 oder 2, dadurch gekennzeichnet, dass das Glühen zur Entspannung mehr als 3 Minuten lang bei einer Temperatur von mehr als 650 °C durchgeführt wird.
EP04014453A 1996-01-25 1997-01-21 Verfahren zum Herstellen nicht kornorientierter Elektrobleche und nach diesem Verfahren hergestellte Bleche Expired - Lifetime EP1473371B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
FR9600808 1996-01-25
FR9600808A FR2744135B1 (fr) 1996-01-25 1996-01-25 Procede de fabrication de tole d'acier magnetique a grains non orientes et tole obtenue par le procede
EP97400114A EP0786528B1 (de) 1996-01-25 1997-01-21 Verfahren zum Herstellen nichtkornorientierter Elektrobleche und nach diesem Verfahren hergestellte Bleche

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EP97400114A Division EP0786528B1 (de) 1996-01-25 1997-01-21 Verfahren zum Herstellen nichtkornorientierter Elektrobleche und nach diesem Verfahren hergestellte Bleche
EP97400114.1 Division 1997-01-21

Publications (3)

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EP1473371A2 EP1473371A2 (de) 2004-11-03
EP1473371A3 EP1473371A3 (de) 2005-04-13
EP1473371B1 true EP1473371B1 (de) 2006-10-25

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EP04014453A Expired - Lifetime EP1473371B1 (de) 1996-01-25 1997-01-21 Verfahren zum Herstellen nicht kornorientierter Elektrobleche und nach diesem Verfahren hergestellte Bleche
EP97400114A Expired - Lifetime EP0786528B1 (de) 1996-01-25 1997-01-21 Verfahren zum Herstellen nichtkornorientierter Elektrobleche und nach diesem Verfahren hergestellte Bleche

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EP (2) EP1473371B1 (de)
AT (2) ATE278041T1 (de)
DE (2) DE69730884T2 (de)
ES (2) ES2230591T3 (de)
FR (1) FR2744135B1 (de)

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1415008A1 (de) * 2001-08-11 2004-05-06 ThyssenKrupp Stahl AG Nichtkornorientiertes elektroblech oder -band und verfahren zu seiner herstellung
PL1752549T3 (pl) * 2005-08-03 2017-08-31 Thyssenkrupp Steel Europe Ag Sposób wytwarzania taśmy elektrotechnicznej o zorientowanych ziarnach
PL1752548T3 (pl) * 2005-08-03 2017-08-31 Thyssenkrupp Steel Europe Ag Sposób wytwarzania taśmy elektrotechnicznej o zorientowanych ziarnach
IT1402624B1 (it) 2009-12-23 2013-09-13 Ct Sviluppo Materiali Spa Procedimento per la produzione di lamierini magnetici a grano orientato.
DE102013019787A1 (de) * 2013-11-27 2015-05-28 Valeo Schalter Und Sensoren Gmbh Verfahren zum Herstellen eines ferromagnetischen Bauteils für einen Drehmomentsensor einer Fahrzeuglenkwelle und Drehmomentsensor

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IT1237481B (it) * 1989-12-22 1993-06-07 Sviluppo Materiali Spa Procedimento per la prodizione di lamierino magnetico semifinito a grano non orientato.
FR2665181B1 (fr) * 1990-07-30 1994-05-27 Ugine Aciers Procede de fabrication de tole d'acier magnetique a grains non orientes et tole obtenue par ce procede.
JPH04107216A (ja) * 1990-08-25 1992-04-08 Kobe Steel Ltd 無方向性電磁鋼板の製造方法
TW198734B (de) * 1990-12-10 1993-01-21 Kawasaki Steel Co
JP3348802B2 (ja) * 1993-06-30 2002-11-20 新日本製鐵株式会社 磁束密度が高く、鉄損の低い無方向性電磁鋼板の製造方法
DE69518529T2 (de) * 1994-06-24 2001-04-19 Nippon Steel Corp., Tokio/Tokyo Verfahren zur herstellung von elektrischen nicht orientierten stahlplatten mit hoher magnetischer flussdichte und geringem eisenverlust

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Publication number Publication date
FR2744135A1 (fr) 1997-08-01
EP1473371A3 (de) 2005-04-13
DE69730884T2 (de) 2005-11-17
DE69736868T2 (de) 2007-06-06
ES2230591T3 (es) 2005-05-01
ATE278041T1 (de) 2004-10-15
EP0786528A1 (de) 1997-07-30
FR2744135B1 (fr) 1998-02-27
EP1473371A2 (de) 2004-11-03
ES2276191T3 (es) 2007-06-16
EP0786528B1 (de) 2004-09-29
ATE343651T1 (de) 2006-11-15
DE69730884D1 (de) 2004-11-04
DE69736868D1 (de) 2006-12-07

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