EP1473371A2 - 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
EP1473371A2
EP1473371A2 EP04014453A EP04014453A EP1473371A2 EP 1473371 A2 EP1473371 A2 EP 1473371A2 EP 04014453 A EP04014453 A EP 04014453A EP 04014453 A EP04014453 A EP 04014453A EP 1473371 A2 EP1473371 A2 EP 1473371A2
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EP
European Patent Office
Prior art keywords
strip
annealing
temperature
sheet
steel
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Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP04014453A
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English (en)
French (fr)
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EP1473371B1 (de
EP1473371A3 (de
Inventor
Philippe Poiret
André Bertoni
Jean-Claude Bavay
Jaques Hernandez
Jean Verdun
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
ArcelorMittal France SA
Original Assignee
USINOR SA
Arcelor France SA
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Publication date
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Publication of EP1473371A2 publication Critical patent/EP1473371A2/de
Publication of EP1473371A3 publication Critical patent/EP1473371A3/de
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Publication of EP1473371B1 publication Critical patent/EP1473371B1/de
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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 sheet metal manufacturing process of non-oriented grain magnetic steel.
  • Magnetic sheets called non-oriented grain, that is to say having isotropic magnetic properties are particularly intended for the construction of electromagnetic devices in which the magnetic flux generated by the electrical windings is not not constant, as for example in rotating machines. Certain transformers used in the household appliance sector use this type of sheet for economic reasons.
  • These electromagnetic devices are made of sheets cut and assembled.
  • the sheets have an efficiency that is evaluated in function of 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 leads to an increase in electrical resistivity, which has the function of reducing losses by eddy currents.
  • the vacuum production of steel improves on the one hand, the cleanliness and purity of said steel and secondly to reduce losses by hysteresis.
  • EP 0 469 980 discloses a process used in the field of manufacture of non-oriented grain magnetic sheets, the process comprising successively, after preparation under vacuum of a steel, hot rolling operation followed by coiling, annealing fast said to the parade of hot rolled sheet, an optional operation shot blasting, pickling operation, rolling operation cold in one or more stages followed by annealing, the final annealing being performed in a controlled atmosphere, decarburizing if necessary.
  • the sheets obtained by this process for a final thickness of 0.50 mm approximately, have specific losses less than 6.5 W / Kg under an induction of 1.5 Tesla and a frequency of 50 Hertz as well as a magnetization greater than 1.74 Tesla under a field 5000 A / m electric.
  • the losses total mass is 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 invention aims to improve the characteristics magnetic of non-oriented grain sheets made with steel containing very little silicon, i.e. reducing losses magnetic and increase the magnetization under an electric field determined.
  • the single figure shows a magnetization curve as a function cold rolling rates, cold rolling being performed in one single operation.
  • the process for manufacturing a steel from a magnetic sheet with non-oriented grains comprises the production under vacuum of a steel of the following composition: carbon ⁇ 0.01% silicon ⁇ 0.5%, manganese, 0.05 to 0.5% aluminum ⁇ 0.03%, phosphorus ⁇ 0.20%, sulfur ⁇ 0.015%; nitrogen ⁇ 0.01%, oxygen ⁇ 0.01%, the rest being iron and unavoidable impurities.
  • the steel according the invention has a mass content of silicon 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 energy losses by Joule effect in the materials are evacuated outside by through the magnetic circuit made up of cut sheets stacked. The addition of silicon, manganese and aluminum in the iron results in a decrease in thermal conductivity.
  • the steel must be non or very little alloyed, the weak silicon, manganese and aluminum content of steel according to the invention makes it possible to limit the overheating of the motors which is detrimental to the good performance of the insulators coating the conductors.
  • the better removal of calories can also allow an increase mass power, via increased induction levels, without temperature increase.
  • composition of the invention by the thermal conductivity that it gives to steel, ensures thermal conduction cooling of electrical devices.
  • the steel is poured in the form of a slab, then the slab is hot rolled with reheating temperature below 1300 ° C, and an end temperature of hot rolling below 950 ° C.
  • Hot rolled sheet is coiled at a higher temperature at 550 ° C, then is subjected to static annealing at a temperature between 700 and 1050 ° C for a time greater than 1 hour.
  • the strip After the static annealing step, the strip can undergo an operation optional shot peening, before being subjected to an operation of stripping.
  • the pickled strip is cold rolled, with a rate of reduction between 25 and 90%, in a single rolling operation cold to a thickness less than or equal to 1.5 mm, then it undergoes a final annealing performed at the parade.
  • the final annealing at the parade is carried out from preferably at a temperature between 700 and 1050 ° C, for less than 10 minutes.
  • magnetic losses can be reduced mass below 4.5 W / Kg for a sheet 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, in below 12.5 W / Kg for a sheet thickness of 1 mm and obtain a magnetization equal to or greater than 1.77 Tesla by annealing static hot-rolled sheet strip, combined with rolling cold in a single operation followed by continuous annealing on parade.
  • a steel slab N ° 4 whose chemical composition by weight is given in table 1 is reheated to 1173 ° C then undergoes a first hot rolling with a reduction rate of 86% and a second hot rolling with a rate of 93% reduction.
  • the end of hot rolling temperature is 843 ° C
  • the hot rolled sheet strip is wound at the temperature of 738 ° C.
  • the sheet in the form of a coil is subjected to static annealing at the temperature of 800 ° C. for 10 hours under an atmosphere of hydrogen or of hydrogen and nitrogen.
  • the sheet is then cold rolled with a reduction rate of 80% to obtain a sheet thickness of 0.50 mm.
  • the final annealing is carried out at a temperature of 880 ° C. for 2 minutes under an atmosphere of nitrogen and hydrogen.
  • a steel slab n ° 4 whose weight composition is given in table 1 is treated in the same way as steel Example 1, that is to say with the same hot reduction rates and at cold.
  • the heating temperature of the slab is 1185 ° C
  • the end of hot rolling temperature is 857 ° C.
  • the sheet metal strip hot rolled is wound at a temperature of 636 ° C.
  • a stretch of the coil is subjected to static annealing at a temperature of 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.
  • Final annealing is carried out at the temperature of 880 ° C for 2 minutes under a nitrogen and hydrogen atmosphere.
  • a steel slab n ° 4 whose weight composition is given in table 1 is treated in the same way as steel Example 1, that is to say with the same hot reduction rates and at cold.
  • the heating temperature of the slab is 1221 ° C
  • the end of hot rolling temperature is 910 ° C.
  • the sheet metal strip hot rolled is wound at a temperature of 785 ° C.
  • the sheet metal under coil form is subjected to static annealing at the temperature of 800 ° C for 10 hours under a hydrogen atmosphere or hydrogen and nitrogen.
  • the sheet is then cold rolled to reach to a sheet of 0.50 mm thick.
  • Final annealing is carried out at the temperature of 880 ° C for 2 minutes under a nitrogen atmosphere and hydrogen.
  • steel No. 2 the composition is given in table 5, which includes in its composition a manganese content of 0.87% leads to magnetic properties identical to those in Table 4.
  • the content of manganese should however be limited to less than 0.5% to improve thermal conductivity.
  • Step # 2 VS mn Yes S al P 0.003% 0.870% 0.342% 0.008% 0.001% 0.188%
  • a section of the hot-rolled sheet coil obtained in the conditions described in Example 2 is subjected to static annealing at a temperature of 710 ° C for 40 hours under an atmosphere hydrogen or nitrogen and hydrogen.
  • a steel slab n ° 4 whose weight composition is given in Table 1 is treated in the same way as in Example 1, that is, with the same hot and cold reduction rates.
  • the steel slab No. 4 is reheated to 1188 ° C, the temperature at the end of hot rolling is 816 ° C.
  • the hot-rolled sheet strip is wound at a temperature of 702 ° C.
  • a section of sheet metal in the form of a coil is subjected to static annealing at a temperature of 1000 ° C. for 10 hours under an atmosphere of hydrogen or hydrogen and nitrogen.
  • the sheet is then cold rolled to obtain a sheet 0.50 mm thick.
  • the final annealing is carried out at a temperature of 880 ° C. for 2 minutes under an atmosphere of nitrogen and hydrogen.
  • the magnetic characteristics obtained are presented in Table 7.
  • a section of the hot-rolled sheet coil obtained in the conditions described in Example 2 is subjected to static annealing at temperature of 740 ° C for 40 hours under a hydrogen atmosphere or hydrogen and nitrogen. After annealing the section is divided into four parts which undergo cold rolling respectively with a rate of reduction of 60%, 74%, 80% and 86% to obtain a sheet of 1 mm 0.65 mm, 0.50 mm, and 0.35 mm thick.
  • 0.5 mm thick sheet and 0.35 mm thick sheet are annealed at a temperature of 880 ° C for 2 min.
  • the 0.65 mm thick sheet is annealed at a temperature of 880 ° C for 2 min 30 s.
  • the 1 mm thick sheet is annealed at a temperature of 880 ° C for 3 min 40 s.
  • the single figure shows that the cold rolling rate should be less than 90% to obtain a magnetization equal to or greater than 1.77 Tesla when static annealing is performed after hot rolling.
  • the invention comprises the following stages: static annealing before cold rolling, cold rolling in a single operation, a final annealing as presented in Examples 1, 2, 3, 4, 5 and 6. After cutting of circuit elements and stacking, it can be performed on said circuits an annealing of elimination of the internal stresses.
  • the annealing of elimination of the internal stresses generated by cutting can significantly reduce losses without no degradation of the magnetization of the sheet according to the invention.
  • the sheet undergoes stress elimination annealing at a temperature above 650 ° C, for a time above 3 min.
  • Epstein specimens having a thickness of 0.35 mm, 0.50 mm, 0.65 mm and 1 mm, used to measure the characteristics magnetic plates presented in Examples 1, 3, 4, and 5, have been subjected to an annealing of 750 ° C for 2 hours under a nitrogen and hydrogen atmosphere.
  • the Epstein test tubes used in Example 6 to measure the magnetic characteristics are annealed at 750 ° C for two hours under an atmosphere of nitrogen and hydrogen.
  • the magnetic characteristics obtained are presented in Table 9.
  • 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 as well as 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 long-term static annealing followed by a single cold rolling, it has a thickness of 0.50 mm and 0.65 mm, a significant reduction in mass losses and improved magnetization ability.
  • the sheet obtained by the process can be subjected, after cutting and assembly of magnetic circuits, annealing elimination of constraints.
  • This annealing eliminates the stresses due to cutting, causes a significant reduction in losses without degradation of magnetizability, with static annealing of the rolled strip at hot 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)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Electromagnetism (AREA)
  • Manufacturing & Machinery (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Dispersion Chemistry (AREA)
  • Power Engineering (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
  • Inorganic Insulating Materials (AREA)
  • Soft Magnetic Materials (AREA)
  • Processing And Handling Of Plastics And Other Materials For Molding In General (AREA)
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
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
FR9600808 1996-01-25
EP97400114A EP0786528B1 (de) 1996-01-25 1997-01-21 Verfahren zum Herstellen nichtkornorientierter Elektrobleche und nach diesem Verfahren hergestellte Bleche

Related Parent Applications (2)

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

Publications (3)

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

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

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

Country Status (5)

Country Link
EP (2) EP0786528B1 (de)
AT (2) ATE278041T1 (de)
DE (2) DE69730884T2 (de)
ES (2) ES2230591T3 (de)
FR (1) FR2744135B1 (de)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2007014868A1 (de) * 2005-08-03 2007-02-08 Thyssenkrupp Steel Ag Verfahren zur herstellung von kornorientiertem elektroband
WO2007014867A1 (de) * 2005-08-03 2007-02-08 Thyssenkrupp Steel Ag Verfahren zur herstellung von kornorientiertem elektroband
ITRM20090681A1 (it) * 2009-12-23 2011-06-24 Ct Sviluppo Materiali Spa Procedimento per la produzione di lamierini magnetici a grano orientato.

Families Citing this family (2)

* 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
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
WO1996000306A1 (fr) * 1994-06-24 1996-01-04 Nippon Steel Corporation Procede de fabrication de tole d'acier electromagnetiquement non orientee presentant une densite elevee de flux magnetique pour un niveau faible de perte dans le noyau

Cited By (19)

* Cited by examiner, † Cited by third party
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CN101238226B (zh) * 2005-08-03 2011-07-13 蒂森克虏伯钢铁公司 生产晶粒取向的电工带钢的方法
KR101365652B1 (ko) * 2005-08-03 2014-02-19 티센크루프 스틸 유럽 악티엔게젤샤프트 방향성 전자 강 스트립 제조 방법
EP1752549A1 (de) * 2005-08-03 2007-02-14 ThyssenKrupp Steel AG Verfahren zur Herstellung von kornorietiertem Elektroband
EP1752548A1 (de) * 2005-08-03 2007-02-14 ThyssenKrupp Steel AG Verfahren zur Herstellung von kornorietiertem Elektroband
WO2007014868A1 (de) * 2005-08-03 2007-02-08 Thyssenkrupp Steel Ag Verfahren zur herstellung von kornorientiertem elektroband
KR101365653B1 (ko) * 2005-08-03 2014-02-19 티센크루프 스틸 유럽 악티엔게젤샤프트 방향성 전자 강 스트립 제조 방법
AU2006274900B2 (en) * 2005-08-03 2011-07-28 Thyssenkrupp Steel Ag Method for producing a grain-oriented electrical steel strip
TWI402353B (zh) * 2005-08-03 2013-07-21 Thyssenkrupp Steel Ag 製造晶粒取向性磁鋼帶的方法（二）
WO2007014867A1 (de) * 2005-08-03 2007-02-08 Thyssenkrupp Steel Ag Verfahren zur herstellung von kornorientiertem elektroband
US8038806B2 (en) 2005-08-03 2011-10-18 Thyssenkrupp Steel Ag Method for producing grain oriented magnetic steel strip
CN101238227B (zh) * 2005-08-03 2011-11-16 蒂森克虏伯钢铁公司 生产晶粒取向的电工带钢的方法
US8088229B2 (en) 2005-08-03 2012-01-03 Thyssenkrupp Steel Ag Method for producing grain oriented magnetic steel strip
AU2006274901B2 (en) * 2005-08-03 2011-07-28 Thyssenkrupp Steel Ag Method for producing a grain-oriented electrical steel strip
TWI402352B (zh) * 2005-08-03 2013-07-21 Thyssenkrupp Steel Ag 製造晶粒取向性磁鋼帶的方法（一）
ITRM20090681A1 (it) * 2009-12-23 2011-06-24 Ct Sviluppo Materiali Spa Procedimento per la produzione di lamierini magnetici a grano orientato.
CN102834528A (zh) * 2009-12-23 2012-12-19 材料开发中心股份公司 晶粒取向磁性片材的生产方法
WO2011077470A1 (en) * 2009-12-23 2011-06-30 Centro Sviluppo Materiali S.P.A. Process for the production of grain-oriented magnetic sheets
CN102834528B (zh) * 2009-12-23 2015-05-06 材料开发中心股份公司 晶粒取向磁性片材的生产方法
US9328396B2 (en) 2009-12-23 2016-05-03 Centro Sviluppo Materiali S.P.A. Process for the production of grain-oriented magnetic sheets

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EP0786528B1 (de) 2004-09-29
EP0786528A1 (de) 1997-07-30
ES2230591T3 (es) 2005-05-01
EP1473371B1 (de) 2006-10-25
ES2276191T3 (es) 2007-06-16
DE69736868T2 (de) 2007-06-06
ATE343651T1 (de) 2006-11-15
FR2744135A1 (fr) 1997-08-01
ATE278041T1 (de) 2004-10-15
DE69730884T2 (de) 2005-11-17
DE69736868D1 (de) 2006-12-07
EP1473371A3 (de) 2005-04-13
FR2744135B1 (fr) 1998-02-27
DE69730884D1 (de) 2004-11-04

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