EP2729588B1 - Verfahren zum herstellen eines kornorientierten, für elektrotechnische anwendungen bestimmten elektrostahlflachprodukts - Google Patents

Verfahren zum herstellen eines kornorientierten, für elektrotechnische anwendungen bestimmten elektrostahlflachprodukts Download PDF

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EP2729588B1
EP2729588B1 EP20120734890 EP12734890A EP2729588B1 EP 2729588 B1 EP2729588 B1 EP 2729588B1 EP 20120734890 EP20120734890 EP 20120734890 EP 12734890 A EP12734890 A EP 12734890A EP 2729588 B1 EP2729588 B1 EP 2729588B1
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Prior art keywords
annealing
temperature
strip
cold
target
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French (fr)
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EP2729588A1 (de
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Heiner Schrapers
Thorsten KRENKE
Christof Holzapfel
Ludger Lahn
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ThyssenKrupp Electrical Steel GmbH
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ThyssenKrupp Electrical Steel GmbH
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular fabrication or treatment of ingot or slab
    • 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
    • C21D8/1205—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
    • C21D8/1216—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. Electrical steel flat products of this type are also referred to in practice as grain-oriented “electrical sheets” or grain-oriented “electrical tapes”.
  • 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 degree of deformation of the rolling processes and the parameters of the heat treatment steps are coordinated so that targeted recrystallization processes proceed. These recrystallization processes lead to a typical for the material "Goss texture" in which the direction of the easiest magnetization in the rolling direction of the finished strips.
  • Grain-oriented electrical steel or sheet of the type in question has a strongly anisotropic magnetic behavior. This is due to a uniform orientation of the grains (crystallites) of the structure. This crystallographic texture is achieved by effective grain growth selection by taking appropriate measures in the manufacturing process. The aim is to obtain, after a final annealing at the end of the production process, an electrical steel flat product in which the grains have a slight misorientation and, consequently, an almost ideal texture.
  • 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.
  • a continuous decarburization annealing takes place for a total time of between 50 and 350 seconds, at a temperature between 800 and 950 ° C.
  • so-called "low-heating process” can produce highly permeable, grain-oriented electrical sheets with an optimized distribution of properties. Characteristic of this method is a Slab heating temperature below 1250 ° C. As a result of this comparatively low temperature, aluminum nitrides, which are completely dissolved in the high-temperature annealing step at the end of the production process, are only partially dissolved and removed again. As a result, electrical steel produced by the low-heating process has weaker inherent inhibition than material produced by the high temperature slab heating conventional process path.
  • the purpose of the particle inhibition is to suppress the grain growth in the primary structure of the cold strip after and during the decarburization annealing. Only during the final annealing, in which the cold strips are annealed at temperatures of up to 1200 ° C, a controlled abnormal grain growth in the temperature range of 950 - 1100 ° C made in order to enable a high textured sharpness with Gossorienttechnik [001] (110) ,
  • the driving force for grain growth during annealing is the grain boundary energy stored in the microstructure. This is essentially determined by the particle size after the primary recrystallization.
  • the driving force for abnormal grain growth is thus generally lower.
  • a repulsive force opposing the abnormal grain growth is determined by the non-magnetic precipitates (inhibitors) precipitated in the cold strip. Therefore, it is important to have many finely divided particles.
  • the relevant particles are not produced in the hot strip but before, after or during the decarburization annealing or during the heating phase of the final annealing in the course of various nitriding processes.
  • an inhibiting strength Iz by nitrides and sulfides so that the primary grain growth is inhibited in the cold process, even at higher temperatures.
  • the slabs are heated to temperatures of 1100 ° C to 1320 ° C before hot rolling.
  • a nitriding treatment carried out simultaneously with the decarburization annealing at temperatures between 850 and 1050 ° C. in an ammonia-containing atmosphere enables the direct formation of aluminum nitrides.
  • the subsequent high-temperature annealing need not be modified compared to the conventional production method of grain-oriented electrical steel production.
  • the opposite is in the in the EP 0 219 611 B1 Nitriding after the Primary recrystallization, but performed before onset of abnormal grain growth.
  • the nitration can be carried out here by an atmosphere with nitriding ability or by a nitrogen-donating adhesive protection additive.
  • silicon-manganese nitrides are present ( Materials Science Forum 204-206 (1996), 143-154 ). Due to their lower thermodynamic stability they dissolve during the heating of the annealing. The nitrogen then diffuses into the steel matrix and recombines with the free aluminum present there to aluminum nitride ( Materials Science Forum 204-206 (1996), 593-598 ). The resulting aluminum nitrides are then the inhibitors effective for secondary grain growth. Although the inhibition is weaker compared to the conventional process used for the production of grain-oriented electrical steel sheet, but allows a complete secondary recrystallization at higher temperatures with a larger secondary grain size in the finished strip ( TMS Proceedings 3 (2008), 49-54 ).
  • a disadvantage of this approach is that a modified time-temperature cycle of the annealing is required.
  • To make this crucial process step completely possible, is in the implementation of the The method described above requires an isothermal holding step of at least four hours during the heating phase of the high-temperature annealing. This not only requires a significant extension of the entire process duration, but also leads to increased costs in the production.
  • a steel is melted, which besides iron and unavoidable impurities (in mass%) 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%, one or more elements from the group Cu, Ni, Cr, Co, Mo with contents of in each case up to 0, 5% and one or more elements from the group B, V, Nb at levels of up to 0.012%.
  • the composite Melt is then treated secondary metallurgically in a vacuum plant or a ladle furnace and then cast continuously into a strand. From the strand thus obtained thin slabs are divided, which are subsequently heated in a standing oven to a temperature between 1050 ° C and 1300 ° C. The residence time in the oven is at most 60 min. Following the heating of the thin slabs, the thin slabs are hot rolled into a hot strip of thickness 0.5-4.0 mm in a multi-stand hot mill line in line. During hot rolling, the first forming pass is carried out at a temperature of 900 - 1200 ° C with a degree of deformation of more than 40%.
  • the two forming passes subsequent to rolling at 900 to 1200 ° C. are rolled in the two-phase mixing zone ( ⁇ - ⁇ ).
  • the reduction is not more than 30%.
  • the resulting hot strip is cooled and coiled into a coil.
  • annealing of the hot strip after reeling or before cold rolling can be performed.
  • 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.
  • nitriding of the strip in a NH 3 -containing atmosphere can also be carried out at temperatures above 850 ° C.
  • 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 finally annealed stress-free.
  • 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.
  • steps g) and h) carried out single- or multi-stage hot strip annealing, a thermal straightening of the cold strip and the application of an insulating layer, which can be carried out in the context of the inventive method using and taking into account the known from the prior art parameters.
  • 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 over a first time interval, which comprises heating the cold strip starting from a starting temperature to a first desired annealing temperature and then holding it at this desired annealing temperature.
  • the second stage of the annealing extends in a corresponding manner according to the invention over a second time interval, within which the cold strip is first heated to a second target annealing temperature and then maintained at this target annealing temperature.
  • 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 passing the cold strip for decarburizing and nitriding annealing obtained after cold rolling through a continuous annealing furnace divided into at least two zones, setting a target annealing temperature in its first zone passed through first in accordance with the invention is, which is 10 to 50 ° C lower than the target annealing temperature in the subsequently passed by the cold strip second zone of the furnace, the duration of the time interval within which the first stage of the annealing runs, 30-70% of the total duration of the decarburizing and nitriding annealing is.
  • the cold band structure obtained after annealing thus has a significantly smaller variance with the same average grain size set by the higher annealing temperature annealing in the rear furnace zone, thus allowing for a high temperature during the final annealing final annealing achieved a homogeneous secondary grain growth.
  • An electric flat steel product produced according to the invention thus has a crystallographic texture after the annealing treatment carried out after at least two stages following the cold rolling, which optimally ensures homogeneous secondary grain growth during the final high-temperature annealing.
  • the invention combines in this way the known from the low-heating process approach with a modern thin-slab production, which takes place according to the known, characterized by a continuous manufacturing process casting-rolling process.
  • an electrical steel flat product is available in accordance with the method according to the invention which has optimum magnetic properties in relation 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 to carry out a residual decarburization and nitration 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.
  • the inventive annealing stages carried out without decarburization or nitriding and to finish the decarburization and nitriding only in an annealing step following the two stages of the annealing according to the invention.
  • the first and second stages of the annealing can be completed following each other and subsequently a further annealing step can be carried out in which the cold strip is subjected to a decarburizing and nitriding annealing.
  • the first and second stages of the annealing in step i) can be carried out taking into account the parameters provided according to the invention for these annealing stages with regard to the position of the temperature levels and the time portion of the first annealing stage, based on the total time of the annealing stages.
  • a further annealing step takes place in which decarburization and nitriding are carried out in a conventional manner.
  • the duration of the first time interval is limited to 30-60% of the total duration of the annealing treatment.
  • the heating of the cold strip to the desired temperature of the first annealing stage should be as fast as possible.
  • the cold-worked strip first undergoes recovery. Then the primary recrystallization begins. At higher temperatures and longer annealing times, grain growth processes are added. In order to provide as much stored energy as possible for recrystallization, the temperature range of the recovery should be run through quickly.
  • an advantageous embodiment of the invention provides that the heating rate with which the cold strip is heated in the first stage of the annealing from the start temperature to the first target annealing temperature, 25 - 500 ° C / s.
  • the heating rate is typically 30-70 ° C / s.
  • a rapid heating rate can be achieved, in particular in the case of continuous production, in that an inductive rapid heating takes place at the entrance of the respective continuous furnace, in which the cold strip is heated by the action of an electromagnetic field induced in the strip.
  • the hot strips produced in the manner described above have been subjected to a two-stage hot strip 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 single-stage hot strip annealing with a uniform uniform annealing temperature could have been carried out.
  • the annealed hot strip was cold rolled in one stage with a degree of deformation of 87% to a final thickness of 0.285 mm. Sheet samples have been separated from the cold strips thus obtained.
  • a comparison group A of these sheet samples has been annealed in a continuous annealing furnace.
  • a second furnace section passed after the first furnace section a second annealing step lasting 30 seconds was carried out under a humid atmosphere composed of an ammonia / hydrogen / nitrogen mixture to effect residual decarburization and nitriding.
  • the temperature of the annealing was always 910 ° C.
  • step i) of the method according to the invention divided into two annealing steps, of which the first annealing step according to the invention predetermined subdivision has been performed again in two annealing stages on the following has been completed as a second annealing step a conventional decarburizing and nitriding annealing.
  • step i) has thus been completed here in three consecutive parts.
  • a second group B of the sheet metal samples has first been annealed in the course of the first annealing step in two consecutive annealing stages according to the invention and then restet carburized and nitrided in a second annealing step.
  • five variants Ba) - Be) of the two-stage annealing according to the invention have been investigated.
  • the first annealing stage which proceeds over a first duration t 1 , in each case one target annealing temperature T 1 and in the second annealing stage a respective target annealing temperature T 2 have 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 the first annealing section comprised a rapid heating to the respective desired annealing temperature T 1 at a heating rate of 40 ° C./sec.
  • 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).
  • the first two annealing stages of the variant exemplified here of the method according to the invention are mainly used for decarburization and are optimized in this regard with respect to gas composition and temperature.
  • the Entkohlungsglühung takes place in two stages with respect to the temperature control in such a way that in the first passed first section is first gently decarburized to avoid grain enlargements as possible, and in the subsequently passed section at the optimal temperature for the effectiveness of the decarburization decarburization is continued and terminated.
  • the third annealing step of the process according to the invention is optimized with respect to 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 .
  • the first furnace section of the continuous annealing furnace has been divided into two equal-length temperature zones, for their passage each required to be glowing sheet metal samples so each 75 s. Accordingly, in these tests, the duration t 1 of the first annealing stage was 50% of the total duration t 2 of 150 s.
  • the desired annealing temperature has been changed from variant to variant when carrying out the experiments according to the invention, while in the second temperature zone when carrying out the second annealing stage a constant amount of 860 ° C. is in each case Target annealing temperature has been set.
  • the target annealing temperature in the second annealing step was 910 ° C.
  • the samples were subsequently coated with magnesia and final annealed under an annealing atmosphere consisting of 50% by volume of H2 and 50% by volume of N2.
  • Hot strips produced from the melt 1 as discussed above were subjected to a two-stage hot strip annealing at 1130 ° C / 900 ° C, hot strips of the melt 2 to a one step hot strip annealing at 980 ° C. Subsequently, 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.
  • a second group B of samples was annealed in the same atmosphere according to the invention in two stages in the first process part of the continuous furnace used.
  • 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 J 800 applied over the annealing time t 1 of 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.
  • 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, during the first, until the 70th second (t 1 / t 2 ⁇ 55%) continuous annealing stage of the annealing a target annealing temperature of 850 ° C and then in the second, from the 70th to the 130th second annealing stage a target annealing temperature of 880 ° C was set. Subsequently, as in Example 1, nitriding and residual decarburization were also carried out at 900 ° C. in each case.
  • Hot strips produced from the melt 3 in the manner explained above were subjected to a two-stage Warrnbandglühung at 1070 ° C / 950 ° C and cold rolled in one stage to form a cold strip with a final thickness of 0.215 mm. From the obtained cold tapes sheet samples have been divided.
  • the annealing temperature was set at 850 ° C for the second annealing stage, while the target annealing temperature in the second annealing stage, which lasted from the 70th to the 120th second, was 870 ° C.
  • the sheet samples were nitrided at 910 ° C in a wet ammonia / hydrogen / nitrogen mixture and restetalled.
  • the first annealing stage of the first annealing step involved rapid heating of the sheet samples to the desired annealing temperature of the first annealing stage.
  • the heating rates AHR were varied in four different experimental runs under otherwise unchanged conditions.

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  • Soft Magnetic Materials (AREA)
  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
EP20120734890 2011-07-06 2012-07-04 Verfahren zum herstellen eines kornorientierten, für elektrotechnische anwendungen bestimmten elektrostahlflachprodukts Not-in-force EP2729588B1 (de)

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DE102011107304A DE102011107304A1 (de) 2011-07-06 2011-07-06 Verfahren zum Herstellen eines kornorientierten, für elektrotechnische Anwendungen bestimmten Elektrostahlflachprodukts
PCT/EP2012/063039 WO2013004747A1 (de) 2011-07-06 2012-07-04 Verfahren zum herstellen eines kornorientierten, für elektrotechnische anwendungen bestimmten elektrostahlflachprodukts

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DE (1) DE102011107304A1 (ru)
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MX2015011022A (es) * 2013-02-28 2015-10-22 Jfe Steel Corp Metodo para la produccion de lamina de acero electrico de grano orientado.
DE102014104106A1 (de) * 2014-03-25 2015-10-01 Thyssenkrupp Electrical Steel Gmbh Verfahren zur Herstellung von hochpermeablem kornorientiertem Elektroband
JP6191564B2 (ja) * 2014-09-04 2017-09-06 Ｊｆｅスチール株式会社 方向性電磁鋼板の製造方法および窒化処理設備
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
KR101751526B1 (ko) * 2015-12-21 2017-06-27 주식회사 포스코 방향성 전기강판의 제조방법
KR102012319B1 (ko) 2017-12-26 2019-08-20 주식회사 포스코 방향성 전기강판 및 그 제조방법
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
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RU2014104074A (ru) 2015-08-20
KR20140044892A (ko) 2014-04-15
US20140261895A1 (en) 2014-09-18
CN103748240A (zh) 2014-04-23
EP2729588A1 (de) 2014-05-14
BR112014000185A2 (pt) 2017-02-07
JP2014524978A (ja) 2014-09-25
WO2013004747A1 (de) 2013-01-10
DE102011107304A1 (de) 2013-01-10

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