EP1192287B1 - Procede de production de tole electrique a grains non orientes - Google Patents

Procede de production de tole electrique a grains non orientes Download PDF

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Publication number
EP1192287B1
EP1192287B1 EP00918861A EP00918861A EP1192287B1 EP 1192287 B1 EP1192287 B1 EP 1192287B1 EP 00918861 A EP00918861 A EP 00918861A EP 00918861 A EP00918861 A EP 00918861A EP 1192287 B1 EP1192287 B1 EP 1192287B1
Authority
EP
European Patent Office
Prior art keywords
strip
rolling
hot
annealing
ferrite
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
Application number
EP00918861A
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German (de)
English (en)
Other versions
EP1192287A1 (fr
Inventor
Rudolf Kawalla
Hans Pircher
Karl Ernst Friedrich
Brigitte Hammer
Jürgen Schneider
Olaf Fischer
Carl-Dieter Wuppermann
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ThyssenKrupp Steel Europe AG
Original Assignee
ThyssenKrupp Stahl AG
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Publication date
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Priority to SI200030038T priority Critical patent/SI1192287T1/xx
Publication of EP1192287A1 publication Critical patent/EP1192287A1/fr
Application granted granted Critical
Publication of EP1192287B1 publication Critical patent/EP1192287B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—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
    • C21D8/1261—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 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
    • 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
    • C21D8/1266—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
    • 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
    • C21D8/1244—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

Definitions

  • the invention relates to a method for producing not grain-oriented electrical sheet, in which from a made of a steel material, such as cast Slabs, bands, curtains or thin slabs, a Hot strip is made, the electric sheet a low turnover loss and a high turnover Polarization and good mechanical properties has.
  • a steel material such as cast Slabs, bands, curtains or thin slabs
  • a Hot strip is made, the electric sheet a low turnover loss and a high turnover Polarization and good mechanical properties has.
  • Such non-grain oriented electrical sheets are mainly used as nuclear material in electrical Machines, such as motors and generators, with rotating magnetic flux direction used.
  • non-grain oriented electrical sheet are here under the DIN EN 10106 ("final annealed Electrical sheet ”) and DIN EN 10165 (" not final annealed Electrical sheet ”) falling electric sheets understood. In addition, also become more anisotropic varieties as long as they are not grain-oriented Electric sheets apply.
  • Non-grain oriented Electrical sheet metal not only affects Non-grain oriented electrical sheets with high losses (P1.5 ⁇ 5 - 6 W / kg), but also sheets with medium (3.5 W / kg ⁇ P1.5 ⁇ 5.5 W / kg) and low losses (P1.5 ⁇ 3.5). Therefore one strives, the entire spectrum the weak, medium and highly silicated Electrotechnical steels in terms of its to improve magnetic polarization values.
  • the object of the invention is a inexpensive way to produce electrical sheets indicate with improved properties.
  • a method for producing non-grain oriented electrical steel in which from a starting material, such as cast slabs, strips or thin slabs, made of a steel with (in wt .-%) 0.001 - 0.05% C, ⁇ 1 , 5% Si, ⁇ 0.4% Al, with Si + 2 Al ⁇ 1.7%, 0.1-1.2% Mn, optionally up to a total of 1.5% of alloying additives, such as P, Sn, Sb, Zr, V, Ti, N, Ni, Co, Nb and / or B, and the remainder being iron and conventional accompanying elements, a hot strip is produced by directing the starting material directly from the casting heat or after a previous reheating to at least 1000 ° C and at most 1180 ° C reheating temperature hot rolled in several forming passes and then coiled, wherein during the hot rolling at least the first forming pass in Austenit with at least one further forming pass in the two-phase mixing area austenite / ferrite is
  • the magnetic Properties of an electrical sheet by deformation during the individual in the course of hot rolling continuous forming passes depending on respective structural state influenced.
  • Crucial part has thereby the rolling in Two-phase mixed area, whereas the proportion of deformation should be as low as possible in the ferrite region.
  • the inventive method is therefore particularly for the processing of such Fe-Si alloys suitable, which is a pronounced two-phase mixed region between have the austenite and the ferrite region.
  • the hot rolling according to the invention is usually in one formed of several rolling stands Finishing roll completed.
  • those traversed in the austenitic area serve Umformstiche to, the thickness of the hot strip before the Start of rolling in the two-phase mixed area so to adjust that during the im Two-phase mixing zone rolling ("Mixing rollers") desired overall shape change safely is reached.
  • the mixing rolls also include at least one forming pass. However, preferably several forming passes in the mixed area austenite / ferrite go through to those required in this mixing rollers Overall shape change of at least 35% sure to reach and so the desired attitude of the To obtain hot strip microstructure.
  • total change in shape ⁇ h is understood here to mean the ratio of the decrease in thickness during rolling in the respective phase region to the thickness of the strip when entering the relevant phase region.
  • a hot strip produced according to the invention has, for example, a thickness h 0 after rolling in the austenite region. In the course of the subsequent rolling in the two-phase mixing zone, the thickness of the hot strip is reduced to h 1 .
  • the total deformation ⁇ h during rolling in the two-phase mixed area austenite / ferrite should reach at least 35% in order to set the desired magnetic and technological properties favorable state of the hot-rolled strip in terms of grain size, texture and precipitates or prepare for subsequent processing steps.
  • Optimal processing results can be achieved if the total deformation in the biphasic mixed area austenite / ferrite is limited to a maximum of 60%.
  • the inventive method allows by a both in terms of temperature control as also with regard to the staggering of the transformations optimized rolling strategy in combination with a suitably selected reel temperature the most cost-effective Production of a high-quality electrical steel material.
  • An advantageous embodiment of the invention is characterized in that the hot strip is finished rolled after forming in the austenite exclusively in the two-phase mixed area austenite / ferrite.
  • the total change in shape ⁇ h achieved during rolling in the two-phase mixed region austenite / ferrite should amount to at least 50%.
  • rolling in the ferrite state of the hot strip is completely avoided.
  • tapes made from Fe-Si steels which have a pronounced two-phase mixed region of austenite / ferrite in the transition from austenite to ferrite. This can be avoided by a suitable choice of the ratio of deformation and forming rate, ie utilization of the heat generated during the forming, an optimal temperature control in terms of avoiding cooling of the rolling stock and thus a complete conversion into ferrite.
  • At least one forming pass in the ferrite region is carried out following the rolling in the two-phase mixed region austenite / ferrite.
  • the total deformation ⁇ h achieved during rolling in the ferrite region should be at least 10% and at most 33%.
  • the rolling in the ferrite is limited to a minimum, so that the center of gravity of the deformation is unchanged in the mixed area austenite / ferrite despite the final rolling in the ferrite.
  • the Hot strip is already softened in the coil, with his Characteristics determining characteristics, such as grain size, Texture and excretions are positively affected.
  • Such an "in-line" running Annealing of the coiled at high temperature, in the coil not substantially cooled hot strip can a otherwise necessary Completely replace hot band bake annealing. Let it be Annealed hot strips with particularly good magnetic and technological properties produce. The required time and Energy expenditure is considerably lower than with the conventionally for improving the properties hot strip annealing performed by electrical steel.
  • the hot strip after rolling in the finishing scale at a reel temperature of less than 600 ° C, in particular less than 550 ° C, reeled.
  • the reeling at these temperatures results in the concerned Alloys to a solidified hot strip state.
  • At least one of the last Forming passes in the ferrite area with lubrication hot rolled.
  • hot rolling with lubrication occur on the one hand lower shear deformations, so that the rolled Band in the result a more homogeneous structure over the Cross section receives.
  • the Lubrication reduces the rolling forces, so that over the each rolling pass a higher reduction in thickness possible is. Therefore it can, depending on the desired Characteristics of the electric sheet to be produced, be advantageous if all in the ferrite occurring forming passes with a rolling lubrication be performed.
  • the hot strip after reeling and Cooling additionally at an annealing temperature of annealed at least 740 ° C.
  • This glow can be in the Hood furnace or in a continuous furnace
  • Thin slabs or cast strips when cast as a starting material Thin slabs or cast strips are used, can produce hot strips whose thickness ⁇ 1.5 mm is.
  • the production of high quality Bands can be characterized in this context accomplish that the cast starting material in a Cast rolling mill has been produced and coming from this is passed directly into the rolling mill.
  • Hot rolled strips produced according to the invention have such good properties Characteristics that they are suitable for a variety of Use applications directly as electrical sheets let, without the need for another cold rolling requires one about a smoothing or a passing going out cold deformation is made. Therefore there is a preferred embodiment of the invention in that the hot strip is made up and as Electrical sheet is delivered.
  • Hot strip is processed, especially good magnetic Properties can be achieved when hot rolling in Mixed austenite / ferrite is terminated. It has shown that in particular so under avoidance of the Ferrit capablees hot rolled hot strips suitable are without further deformation in the course of a Cold rolling to be delivered to the end user.
  • the magnetic Characteristics of the according to the invention produced hot-rolled Bandes be improved by the fact that the stained Hot strip at a degree of deformation of more than 3 to no more than 15% temper rolling. This too Reworking does not lead to typical thickness reduction, which would be comparable to the typical cold rolling achieved because of the achieved high degrees of deformation Change in strip thickness. Rather, additional Deformation energy introduced into the band, which a positive influence on the later processability of the Dressing rolled strip has.
  • the invention delivered as a hot strip Electrical sheet can in the usual way before his Assembly and delivery at one Annealing temperature> 740 ° C final annealing. Becomes on the other hand, the final annealing was carried out at the processor, so can a non-annealed electric hot strip for be provided by the hot strip before his Assembly and delivery at annealing temperatures > 650 ° C recrystallizing to a non-annealed electrical steel is annealed.
  • the hot strip produced in accordance with the invention is but also because of its mechanical properties particularly suitable, in a conventional manner einoder to be cold-rolled in several stages to a final thickness. If the cold rolling is carried out in several stages, should follow at least one of the cold rolling stages an intermediate annealing done to the good mechanical Maintain properties of the band.
  • a "fully-finished" -Ebandroband produced be then joins the cold rolling Final annealing at an annealing temperature, which preferably> 740 ° C.
  • Cold-rolled electrical steel produced according to the invention is excellent cutting and punching and is suitable as such, especially to components such as Slats or blanks to be processed.
  • components such as Slats or blanks to be processed.
  • the final annealing of the cold-rolled electric sheet preferably in one decarburizing atmosphere.
  • the invention is based on Embodiments explained in more detail.
  • J2500 refers to the following the magnetic polarization at magnetic Field strengths of 2500 A / m, 5000 A / m or 10000 A / m.
  • P 1.0 or P 1.5 is the Loss of magnetization at a polarization of 1.0 T or 1.5 T and a frequency of 50 Hz understood.
  • the Finishing roll is at least the first forming pass exclusively in Austenitic area.
  • Table 2 shows the magnetic properties J 2500 , J 5000 , J 10000 , P 1.0 and P 1.5 for two electrical sheets B1, B2 produced from steels A and B, respectively.
  • the respective hot-rolled strips intended for the production of the electrical sheets B1, B2 have been rolled to completion in the austenitic area at a total degree of deformation ⁇ h of 66% in the two-phase mixed area austenite / ferrite.
  • the rolled hot strips were then rewound at a reel temperature of 750 ° C. Immediately thereafter, the coiled hot strips were cooled and fed to further processing.
  • Table 3 shows the magnetic properties J 2500 , J 5000 , J 10000 , P 1.0 and P 1.5 for electrical sheets B3, B4, B5.
  • the sheet B3 has been produced using the steel A, the sheet B4 using the steel B and the sheet B5 using the steel C.
  • the hot strips intended for the production of the electrical steel sheets B3, B4, B5 have also been converted exclusively in the austenite / ferrite two-phase mixed region after the transformation in the austenite region.
  • the total conversion ⁇ h achieved during rolling in the mixing area was 66%. Subsequently, the hot strips were rewound at a temperature of 750 ° C.
  • Table 4 shows the magnetic properties J 2500 , J 5000 , J 10000 , P 1.0 and P 1.5 for electrical sheets B6, B7, B8, which, in the order given, are also based on steels A, B and C have been generated.
  • the hot strips intended for the production of the electric sheets B6, B7, B8 have been formed after the transformation in the austenite area in the two-phase mixed area austenite / ferrite.
  • the total conversion ⁇ h achieved in the two-phase mixed area was 50%.
  • the hot-rolled strip has undergone several forming passes in the ferrite area.
  • the total conversion ⁇ h achieved in the ferrite region was less than 30%.
  • the thus finished rolled hot strip was coiled at a temperature of 750 ° C.
  • Table 5 shows the magnetic properties J 2500 , J 5000 , J 10000 , P 1.0 and P 1.5 for electrical sheets B9, B10, B11.
  • the sheet B9 has been produced using the steel A, the sheet B10 using the steel B and the sheet B11 using the steel C.
  • the hot strips intended for the production of the electrical steel sheets B9, B10, B11 have been subjected to the same transformations in the finishing roll scale as the strips intended for the production of the metal sheets B6, B7, B8.
  • the thus finished rolled hot strip was coiled at a temperature of 750 ° C.
  • Tables 8a-8c show the magnetic properties J 2500 , J 5000 , J 10000 , P 1.0 and P 1.5 for the three electrical sheets C1-C3 and D1-D3, respectively, produced from steels C and D, respectively ,

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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)
  • Electromagnetism (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
  • Soft Magnetic Materials (AREA)
  • Metal Rolling (AREA)
  • Preparation Of Compounds By Using Micro-Organisms (AREA)

Claims (27)

  1. Procédé de fabrication de tôle électrique à grain non orienté, dans lequel, à partir d'un matériau brut, tel que des brames, des bandes, des pré-bandes ou des brames minces coulées, qui est fabriqué d'un acier ayant (en % en poids) les composants suivants :
    C : 0,001 à 0,05%
    Si : ≤ 1,5%
    Al : ≤ 0,4%
       avec Si + 2Al ≤ 1,7%
    Mn:0,1 à 1,2%
       éventuellement jusqu'à, au total, 1,5% en additifs d'alliage, tels que P, Sn, Sb, Zr, V, Ti, N, Ni, Co, Nb et/ou B, et
       comme restant, du fer ainsi que des éléments d'accompagnement usuels,
    on produit une bande chaude en laminant à chaud le matériau brut directement à la chaleur de coulée ou après un réchauffement préalable à une température de réchauffement atteignant au minimum 1000°C et au maximum 1180°C en plusieurs passes de formage et on l'enroule ensuite de sorte que, au cours du laminage à chaud, au moins la première passe de formage soit réalisée dans le domaine austénitique et qu'au moins une autre passe de formage le soit dans le domaine mixte à deux phases austénite/ferrite, et qu'au cours du laminage dans le domaine mixte à deux phases, on atteigne une modification de forme totale εh d'au moins 35%.
  2. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que la modification de forme totale εh atteint au maximum 60%.
  3. Procédé selon la revendication 1 ou 2, caractérisé en ce que la bande chaude, après formage dans le domaine austénitique, est soumise à un laminage final exclusivement dans le domaine mixte à deux phases austénite/ferrite.
  4. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que la modification de forme totale εh atteinte au cours du laminage dans le domaine mixte à deux phases austénite/ferrite atteint au moins 50%.
  5. Procédé selon la revendication 1, caractérisé en ce que, à la suite du laminage dans le domaine mixte à deux phases austénite/ferrite, on réalise au moins une passe de formage dans le domaine ferritique.
  6. Procédé selon la revendication 5, caractérisé en ce que la modification de forme totale εh atteinte au cours du laminage dans le domaine ferritique atteint au minimum 10% et au maximum 33%.
  7. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que la température d'enroulement atteint au moins 700°C.
  8. Procédé selon la revendication 7, caractérisé en ce que la bande chaude enroulée est soumise à un recuit direct à la chaleur des bobines et en ce que le temps de recuit à une température de recuit supérieure à 700°C atteint au moins 15 minutes.
  9. Procédé selon la revendication 6, caractérisé en ce que l'acier présente une teneur en Si d'au moins 0,7% en poids.
  10. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que la température d'enroulement atteint moins de 600°C, en particulier moins de 550°C.
  11. Procédé selon la revendication 9 ou 10, caractérisé en ce que la bande chaude est refroidie de manière accélérée directement après l'enroulement en bobine.
  12. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que, au cours du laminage à chaud dans le domaine ferritique, on effectue au moins une passe de formage avec une lubrification.
  13. Procédé selon la revendication 12, caractérisé en ce que toutes les passes de formage dans le domaine ferritique sont réalisées avec une lubrification des rouleaux.
  14. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que la bande chaude est soumise à un recuit après l'enroulement à une température de recuit d'au moins 740°C.
  15. Procédé selon la revendication 14, caractérisé en ce que le recuit de la bande chaude enroulée en bobine est réalisé dans un four à hotte.
  16. Procédé selon la revendication 14, caractérisé en ce que le recuit est réalisé dans un four à circulation.
  17. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que l'épaisseur de la bande chaude est ≤ 1,5 mm.
  18. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que la bande chaude est confectionnée et livrée sous la forme d'une tôle électrique.
  19. Procédé selon la revendication 18, caractérisé en ce que la bande chaude est polie au laminoir avant son confectionnement et sa livraison avec un degré de formage ≤ 3%.
  20. Procédé selon la revendication 18, caractérisé en ce que la bande chaude est dressée au laminoir avant son confectionnement et sa livraison avec un degré de formage > 3-15%.
  21. Procédé selon l'une quelconque des revendications 18 à 20, caractérisé en ce que la bande chaude est soumise à un recuit final, avant son confectionnement et sa livraison, à une température de recuit > 740°C.
  22. Procédé selon l'une quelconque des revendications 18 à 20, caractérisé en ce que la bande chaude est soumise à un recuit, avant son élaboration et sa livraison, à des températures de recuit > 650°C pour se recristalliser en une bande électrique non soumise à un recuit final.
  23. Procédé selon l'une quelconque des revendications 1 à 16, caractérisé en ce que la bande chaude est laminée à froid en une ou plusieurs étapes jusqu'à une épaisseur finale.
  24. Procédé selon la revendication 23, caractérisé en ce que le laminage à froid est réalisé en plusieurs étapes et en ce qu'on effectue un recuit intermédiaire à la suite d'au moins l'une des étapes de laminage à froid.
  25. Procédé selon l'une quelconque des revendications 23 ou 24, caractérisé en ce que la bande froide est soumise à un recuit final à la suite du laminage à froid à une température de recuit > 740°C.
  26. Procédé selon l'une quelconque des revendications 23 ou 24, caractérisé en ce que la bande froide après laminage à froid est soumise à un recuit dans un four à hotte ou un four à circulation à des températures de recuit supérieures à 650°C pour se recristalliser en une bande électrique non soumise à un recuit final, puis elle est dressée et écrouie.
  27. Procédé selon l'une quelconque des revendications 21, 22, 25 ou 26, caractérisé en ce que le recuit est effectué dans une atmosphère décarburante.
EP00918861A 1999-07-05 2000-04-07 Procede de production de tole electrique a grains non orientes Expired - Lifetime EP1192287B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
SI200030038T SI1192287T1 (en) 1999-07-05 2000-04-07 Method for producing non-grain oriented electric sheet steel

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE19930519A DE19930519C1 (de) 1999-07-05 1999-07-05 Verfahren zum Herstellen von nicht kornorientiertem Elektroblech
DE19930519 1999-07-05
PCT/EP2000/003125 WO2001002610A1 (fr) 1999-07-05 2000-04-07 Procede de production de tole electrique a grains non orientes

Publications (2)

Publication Number Publication Date
EP1192287A1 EP1192287A1 (fr) 2002-04-03
EP1192287B1 true EP1192287B1 (fr) 2003-01-08

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EP00918861A Expired - Lifetime EP1192287B1 (fr) 1999-07-05 2000-04-07 Procede de production de tole electrique a grains non orientes

Country Status (12)

Country Link
US (1) US6773514B1 (fr)
EP (1) EP1192287B1 (fr)
JP (2) JP2003504508A (fr)
KR (1) KR100707503B1 (fr)
AT (1) ATE230803T1 (fr)
AU (1) AU3965500A (fr)
BR (1) BR0012227A (fr)
DE (2) DE19930519C1 (fr)
ES (1) ES2189751T3 (fr)
MX (1) MXPA02000156A (fr)
PL (1) PL194908B1 (fr)
WO (1) WO2001002610A1 (fr)

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JP4303431B2 (ja) * 2000-12-11 2009-07-29 新日本製鐵株式会社 超高磁束密度無方向性電磁鋼板およびその製造方法
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ATE230803T1 (de) 2003-01-15
ES2189751T3 (es) 2003-07-16
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JP5529418B2 (ja) 2014-06-25
PL353181A1 (en) 2003-11-03
KR20020035827A (ko) 2002-05-15
EP1192287A1 (fr) 2002-04-03
BR0012227A (pt) 2002-04-02
JP2009149993A (ja) 2009-07-09
DE19930519C1 (de) 2000-09-14
DE50001064D1 (de) 2003-02-13
PL194908B1 (pl) 2007-07-31
US6773514B1 (en) 2004-08-10
AU3965500A (en) 2001-01-22
MXPA02000156A (es) 2002-07-30
JP2003504508A (ja) 2003-02-04

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