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WO2013004747A1 - Procédé de fabrication d'un produit plat en acier électrique à grains orientés destiné à des applications électrotechniques - Google Patents

Procédé de fabrication d'un produit plat en acier électrique à grains orientés destiné à des applications électrotechniques Download PDF

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Publication number
WO2013004747A1
WO2013004747A1 PCT/EP2012/063039 EP2012063039W WO2013004747A1 WO 2013004747 A1 WO2013004747 A1 WO 2013004747A1 EP 2012063039 W EP2012063039 W EP 2012063039W WO 2013004747 A1 WO2013004747 A1 WO 2013004747A1
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WO
WIPO (PCT)
Prior art keywords
annealing
cold
strip
temperature
stage
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.)
Ceased
Application number
PCT/EP2012/063039
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German (de)
English (en)
Inventor
Heiner Schrapers
Thorsten KRENKE
Christof Holzapfel
Ludger Lahn
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.)
ThyssenKrupp Electrical Steel GmbH
Original Assignee
ThyssenKrupp Electrical Steel GmbH
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by ThyssenKrupp Electrical Steel GmbH filed Critical ThyssenKrupp Electrical Steel GmbH
Priority to KR1020147002935A priority Critical patent/KR20140044892A/ko
Priority to CN201280033436.XA priority patent/CN103748240A/zh
Priority to JP2014517790A priority patent/JP2014524978A/ja
Priority to BR112014000185A priority patent/BR112014000185A2/pt
Priority to US14/130,806 priority patent/US20140261895A1/en
Priority to RU2014104074/02A priority patent/RU2014104074A/ru
Priority to EP20120734890 priority patent/EP2729588B1/fr
Publication of WO2013004747A1 publication Critical patent/WO2013004747A1/fr
Anticipated expiration legal-status Critical
Ceased 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
    • C21D8/1205—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
    • 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
    • C21D8/1211—Rapid solidification; Thin strip casting
    • 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
    • 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
    • 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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese

Definitions

  • the invention relates to a method for producing grain-oriented electrical steel flat products intended for electrotechnical applications.
  • Grain-oriented electrical steel flat products have special magnetic properties and are produced by a complex manufacturing process.
  • Base material for electrical steel flat products is a silicon steel sheet. The metallurgical properties of the material, the
  • Electric steel flat products in which the grains do not have pronounced orientation.
  • the magnetic flux is not fixed to any particular direction so that the same magnetic flux in all directions
  • Grain-oriented electrical steel or sheet of the type in question here has a strong anisotropic
  • Grain-oriented electrical steel is particularly suitable for applications in which particularly high demands are placed on the magnetic properties, as is the case, for example, in the construction of transformers.
  • grain-oriented electrical steel are known in greater numbers.
  • Characteristic of this method is a Slab heating temperature below 1250 ° C. Due to this comparably low temperature
  • the purpose of the particle inhibition is to control the grain growth in the primary structure of the cold strip after and during the
  • the driving force for grain growth during annealing is the grain boundary energy stored in the microstructure. This is essentially due to the grain size after the
  • Excretions inhibitors determined. Therefore, it is important to have many finely divided particles. In the low-heating process, however, the relevant particles are not in the hot strip but before, after or during the decarburization annealing or during the
  • an inhibition strength Iz is adjusted by nitrides and sulfides via the hot rolling process in such a way that the primary grain growth during the
  • Nitriding treatment at temperatures between 850 and 1050 ° C in an ammonia-containing atmosphere allows the direct formation of aluminum nitrides.
  • grain-oriented electrical steel can not be modified.
  • the nitration can be carried out here by an atmosphere with nitriding capability or by a nitrogen-donating adhesive protection additive.
  • the nitration is close to
  • EP 1 752 549 A1 discloses a process for the production of high-quality grain-oriented electrical steel based on thin-slab continuous casting, in which the
  • the aim is to avoid the formation of nitridic precipitates before hot rolling and during hot rolling as possible to the possibility of a controlled generation of such
  • unavoidable impurities Si: 2.5-4.0%, C: 0.02-0.10%, Al: 0.01-0.065% N: 0.003-0.015% optionally up to 0.30 % Mn, up to 0.05% Ti, up to 0.3% P, one or more elements from the group S, Se in contents whose sum is at most 0.04%, one or more elements from the group As, Sn, Sb, Te, Bi with contents of up to 0.2% each, one or more elements from the group consisting of Cu, Ni, Cr, Co, Mo with contents of in each case up to 0, 5% and one or more elements of Group B, V, Nb at levels of up to 0.012% each.
  • the composite Melt then becomes secondary metallurgical in one
  • Thin slabs are hot rolled into a hot strip 0.5 to 4.0 mm thick in a multi-stand hot rolling mill in line. During hot rolling, the first forming pass will be at a
  • Temperature of 900 - 1200 ° C performed with a degree of deformation of more than 40%. Furthermore, during hot rolling, at least the two forming passes subsequent to rolling at 900 - 1200 ° C in the
  • the hot strip thus obtained is cooled and coiled into a coil.
  • Cold rolling can be performed. Subsequently, the hot strip is cold rolled to a cold strip having a final thickness of 0.15 mm to 0.50 mm. The resulting cold strip is then annealed recrystallizing and decarburizing. In addition to the decarburization annealing, nitriding of the strip in a NH 3 -containing atmosphere can also be carried out at temperatures above 850 ° C. After this
  • an annealing separator has been applied to the surface of the annealed cold strip, the thus coated cold-rolled strip to the expression of Gosstextur recrystallizing final annealed.
  • the finally annealed cold strip can then be provided with an electrical insulation and
  • EP 0 392 534 B1 describes in detail the atmospheres of decarburization annealing which may be considered. In this context will be on it
  • Nitrierglühung the partial pressure p H 2o P H 2 must be lowered to adjust a suitable oxide layer. The result of this process is a satisfactory formation of the glass film during the annealing.
  • the object of the invention was to provide a method with which it is possible to carry out grain-oriented electrical steel flat products in a simple manner to produce an optimally uniform distribution of the grain size.
  • a method according to the invention for producing a grain-oriented electrical steel flat product intended for electrotechnical applications comprises the following steps: a) producing a molten steel next to iron and
  • unavoidable impurities (in% by weight) Si: 2.5-4.0%, C: 0.02-0.1%, Al: 0.01-0.065%, N: 0.003-0.015%, and optionally up to to 0.30% Mn, up to 0.05% Ti, up to 0.3% P, one or more
  • Continuous casting machine c) separating at least one thin slab from the cast strand, d) heating the thin slab to a temperature between 1050 ° C and 1300 ° C, e) hot rolling the thin slab in a hot rolling mill to a hot strip having a thickness of 0.5-4.0 (f) cooling the hot strip, (g) coiling the hot strip into a coil, (h) cold rolling the hot strip to a cold strip having a final thickness of 0,15 to 0,50 mm, (i) decarburizing and nitriding annealing the cold strip obtained, (j) Applying an annealing separator to the surface of the annealed cold-rolled strip, and k) final annealing the annealing separator
  • Preparation of grain-oriented electrical tapes or sheets are usually required. These include, for example, between steps g) and h) one - or multi - stage hot strip annealing, thermal straightening of the cold - rolled strip and application of an insulating layer carried out as part of the
  • Essential for the invention is that the cold strip in the course of the process step i) "decarburizing and nitriding annealing of the obtained cold strip" in at least two stages decarburizing and nitriding annealed.
  • the first stage of this annealing extends according to the invention over a first time interval, which is a heating of the cold strip, starting from a
  • Start temperature to a first target annealing temperature and then holding at this target annealing temperature includes.
  • the second stage of annealing extends into
  • the first target annealing temperature is lower by 10 to 50 ° C. than the second target annealing temperature.
  • the duration of the first time interval is 30-70% of the total duration of the annealing treatment comprising the first time interval and the second time interval.
  • the invention is based on the recognition that can be produced by an at least two-stage "step annealing" during the step i) a cold strip in which on the one hand the grains have an optimal mean grain size and on the other hand, the deviation of the grain size of the individual grains of the average grain size is low.
  • this can be achieved by subjecting the cold strip for decarburizing and nitriding annealing, obtained after cold rolling, to a continuous flow through at least two zones
  • a target annealing temperature is set to
  • the cold-rolled strip structure obtained after annealing thus has the same mean grain size as that achieved by the higher annealing temperature
  • Glowing in the rear furnace zone is set to a significantly smaller variance, thus enabling during the final, at a high temperature final annealing achieved a homogeneous secondary grain growth.
  • Electric flat steel product having optimum magnetic properties relative to the uses typical of grain-oriented electrical sheets or tapes.
  • a nitriding and decarburizing annealing (working step i) carried out according to the invention in at least two stages does not mean that a combined nitriding and decarburization always necessarily has to take place in both stages of this annealing.
  • the first stage of this annealing carried out according to the invention can also be carried out as a pure heating stage and the decarburization and nitration take place in the second stage. It is also conceivable to carry out a decarburization over the two annealing stages and then in a further annealing step
  • the decarburization and nitriding can take place in succession distributed over the at least two stages of the annealing carried out according to the invention.
  • Annealing is subjected.
  • the first and second stage of the annealing in step i) can under
  • Target annealing temperature of the first stage by 10 - 30 ° C
  • the heating of the cold strip to the desired temperature of the first annealing stage should be as fast as possible.
  • Nitrianssglühung passes through the cold-worked band initially a recovery. Then set the
  • inductive rapid heating takes place, in which the cold strip is heated by the action of an induced electromagnetic field in the band.
  • Diag. 1 is a schematic representation of the
  • annealing according to the invention for the first annealing stage provided time interval ti to the total duration t 2 of the annealing.
  • the annealing temperature in the first stage of the hot strip annealing was 1090 ° C, while the
  • Annealing temperature in the second stage was 850 ° C.
  • a comparison group A of these sheet samples is in
  • the annealing in step i) of the method according to the invention was hereby subdivided into two annealing steps, of which the first annealing step is according to the invention
  • Annealing step a conventional decarburizing
  • a second group B of the sheet samples is in one
  • Annealing stage is in each case a target annealing temperature ⁇ and in the second annealing stage in each case a target annealing temperature T 2 has been set.
  • the total duration t 2 of the two consecutively completed annealing stages was also 150 s in this case.
  • the first stage of the first glow section also included one with a
  • the temperature curve during the annealing in the first annealing step is shown in a dashed line over the annealing time t on the one hand for the group A electrical sheet samples produced for comparison in a solid line and on the other hand for one of the variants B.a) - B.e).
  • inventive method optimized in terms of nitriding. At the same time a residual decarburization occurs here to a small extent.
  • the optimization of the third annealing stage in relation to the nitriding is done essentially by the choice of an optimized gas composition, but may also mean a temperature adjustment. In Diag. 1 is an example carried out accordingly Temperature control to detect a small temperature jump, which occurs after the end of the annealing time t 2 .
  • Furnace section of the continuous annealing furnace has been divided into two equal-length temperature zones, for their passage each of the glowing sheet metal samples so each 75 s
  • the target annealing temperature in the second annealing step was 910 ° C.
  • Table 2 shows for each variant a) - e) the
  • Annealing stage respectively set target annealing temperature Ti, the difference ⁇ between the first target annealing temperature and the target annealing temperature of the second annealing stage and the polarization J 80 o at 800 A / m, indicated in Tesla, and the specified in W / kg Ummagnethnesmann Pi , 7 at a polarization of 1.7 T and a respective frequency of 50 Hz enumerated. It turns out that the
  • Hot strips produced from the melt 1 in the above-described manner were subjected to a two-stage hot strip annealing at 1130 ° C./900 ° C., hot strips of the melt 2
  • the hot-rolled strip was cold rolled with a degree of deformation of 87% in one stage to 0.285 mm thick cold strips. From the obtained cold tapes sheet samples have been divided. In this case as well, for comparison, a group A of electric-wire samples obtained from the cold-rolled tapes is held for a period of 150 seconds at a temperature of 840 ° C in a wet hydrogen / nitrogen mixed atmosphere , 45). This was followed by annealing in a humid ammonia / hydrogen / nitrogen mixture at 860 ° C. for 30 seconds, with residual decarburization and nitriding. Subsequently, as in Example 1, nitrided at 910 ° C and restentarbohlt.
  • a second group B of samples was in the same
  • Atmosphere according to the invention in two stages in the first
  • Example 1 nitriding and residual decarburization were also carried out at 910.degree.
  • the electric sheet samples were then subsequently coated with magnesium oxide and finally annealed under an annealing atmosphere consisting of 50% by volume of H2 and 50% by volume of N2.
  • Diag. 2 is for the samples prepared from the melts 1 and 2 in accordance with the invention Polarization Jsoo applied over the annealing time ti the first stage of the inventive annealing.
  • Hot melts of melts 1 and 2 were subjected to a single-stage hot strip annealing at 950 ° C. This was followed by one-stage cold rolling to cold-rolled strip with a final thickness of 0.165 mm. From the obtained cold tapes sheet samples have been divided.
  • Sample panels were placed in a humidified at a temperature of 880 ° C for a period of 130 seconds
  • a second group B of sheet metal samples was annealed in the same atmosphere in the first part of the process used in the experiments reported here in two stages, wherein during the first, to 70.
  • Cold strip was cold rolled to a final thickness of 0.215 mm. From the obtained cold tapes sheet samples have been divided.
  • a first group A of the sheet samples was heated for 120 seconds at a temperature of 870 ° C in one of a wet hydrogen / nitrogen mixture
  • a second group B of sheet samples is in a wet hydrogen / nitrogen mixture with , 51
  • Furnace section of the continuous annealing furnace used here has been annealed. It is in a first to 65.
  • the annealing temperature has been set to 850 ° C during the second annealing stage, while the target annealing temperature in the second annealing stage, which is from the 70th to the 120th.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Materials Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Manufacturing & Machinery (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Electromagnetism (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
  • Soft Magnetic Materials (AREA)
  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)

Abstract

L'invention concerne un procédé de fabrication d'un produit plat en acier à grains orientés pour des applications électrotechniques, selon lequel du métal en fusion est coulé pour former une barre, une brame mince est séparée de la barre coulée, la brame mince est chauffée et laminée à chaud pour former un feuillard à chaud, le feuillard à chaud est refroidi, bobiné et laminé à froid pour former un feuillard à froid, le feuillard à froid est soumis à un recuit de décarburation et nitruration, un séparateur de recuit est appliqué sur la surface du feuillard à froid et le feuillard à froid est soumis à un recuit final pour lui conférer une texture de Goss. L'opération de « recuit de décarburation et nitruration » est effectuée en deux étapes, la première étape du recuit s'étendant sur un premier intervalle de temps qui comprend un chauffage du feuillard à froid en partant d'une température de départ et en allant jusqu'à une première température de recuit de consigne et un maintien à cette température de recuit de consigne, et la deuxième étape du recuit s'étendant sur un deuxième intervalle de temps dans lequel le feuillard à froid est chauffé à une deuxième température de recuit de consigne puis est maintenu à cette température de recuit de consigne. La première température de recuit de consigne est inférieure de 10 - 50 °C à la deuxième température de recuit de consigne et la durée du premier intervalle de temps représente 30 - 70 % de la durée totale du traitement de recuit englobant le premier et le deuxième intervalle de temps.
PCT/EP2012/063039 2011-07-06 2012-07-04 Procédé de fabrication d'un produit plat en acier électrique à grains orientés destiné à des applications électrotechniques Ceased WO2013004747A1 (fr)

Priority Applications (7)

Application Number Priority Date Filing Date Title
KR1020147002935A KR20140044892A (ko) 2011-07-06 2012-07-04 전기공학적 용도를 위한 방향성 전기 강 판상 제품을 제조하는 방법
CN201280033436.XA CN103748240A (zh) 2011-07-06 2012-07-04 制造晶粒取向的、针对电工用途的电工扁钢产品的方法
JP2014517790A JP2014524978A (ja) 2011-07-06 2012-07-04 電気工学用途を意図した方向性電気鋼板製品の製造方法
BR112014000185A BR112014000185A2 (pt) 2011-07-06 2012-07-04 método para produzir um produto plano de aço para fins elétricos de grãos orientados destinado a aplicações eletroquímicas
US14/130,806 US20140261895A1 (en) 2011-07-06 2012-07-04 Method for Producing a Grain-Oriented Electrical Steel Flat Product Intended for Electrotechnical Applications
RU2014104074/02A RU2014104074A (ru) 2011-07-06 2012-07-04 Способ производства плоского проката из электростали с ориентированной зернистой структурой для применения в электротехнической промышленности
EP20120734890 EP2729588B1 (fr) 2011-07-06 2012-07-04 Procédé de fabrication d'un produit plat en acier électrique à grains orientés destiné à des applications électrotechniques

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102011107304A DE102011107304A1 (de) 2011-07-06 2011-07-06 Verfahren zum Herstellen eines kornorientierten, für elektrotechnische Anwendungen bestimmten Elektrostahlflachprodukts
DE102011107304.7 2011-07-06

Publications (1)

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BR112015020187B1 (pt) 2013-02-28 2019-11-05 Jfe Steel Corp método de produção de chapas de aço elétrico de grão orientado
DE102014104106A1 (de) * 2014-03-25 2015-10-01 Thyssenkrupp Electrical Steel Gmbh Verfahren zur Herstellung von hochpermeablem kornorientiertem Elektroband
US11239012B2 (en) * 2014-10-15 2022-02-01 Sms Group Gmbh Process for producing grain-oriented electrical steel strip
DE102015114358B4 (de) * 2015-08-28 2017-04-13 Thyssenkrupp Electrical Steel Gmbh Verfahren zum Herstellen eines kornorientierten Elektrobands und kornorientiertes Elektroband
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JP7106910B2 (ja) * 2018-03-20 2022-07-27 日本製鉄株式会社 方向性電磁鋼板の製造方法
JP2025502711A (ja) * 2021-12-22 2025-01-28 ポスコ カンパニー リミテッド 無方向性電気鋼板、その製造方法及びそれを含むモーターコア
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DE102011107304A1 (de) 2013-01-10
CN103748240A (zh) 2014-04-23
BR112014000185A2 (pt) 2017-02-07
RU2014104074A (ru) 2015-08-20
EP2729588B1 (fr) 2015-05-06

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