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
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
• • 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
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
  • C21D8/0284—Application of a separating or insulating coating
• • H—ELECTRICITY
  • H01—ELECTRIC ELEMENTS
  • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
  • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
  • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
  • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
  • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
  • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
  • H01F1/147—Alloys characterised by their composition
  • H01F1/14766—Fe-Si based alloys
  • H01F1/14775—Fe-Si based alloys in the form of sheets
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
  • C21D8/0226—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
  • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat 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
• • 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
  • C21D8/1277—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
  • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
  • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
  • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper

Definitions

• the invention relates to a method for producing a grain-oriented, intended for electrical applications electrical tape or sheet.
• Such electrical tapes or sheets are characterized by a particularly sharp ⁇ 110 ⁇ ⁇ 001> texture, which has a slight magnetization direction parallel to the rolling direction.
• Such a texture is called after their discoverer also "Goss texture”.
• Goss texture occurs via a selective anomalous grain growth, which is also called secondary recrystallization.
• secondary recrystallization the natural tendency of a metallic matrix to increase grain size is suppressed by the presence of grain growth inhibitors, which in technical language are also called “inhibitors” or “inhibitor phase” for short.
• the inhibitor phase consists of very fine and homogeneously distributed particles of one or more foreign phases.
• the particles in question already have a natural one at their interface with the matrix Interfacial energy. This obstructs a grain boundary moving across it, because the further savings in interfacial energy in the overall system are greatly reduced.
• the inhibitor phase therefore has a central importance for the formation of the Goss texture and, consequently, for the magnetic properties of the respective material. Of importance here is the homogeneous distribution of very many very small particles. Because the number of excreted particles is not revealed experimentally, their size gives information about their effect. Thus, it is believed that the particles of the inhibitor phase should not be significantly larger than 100 nm on average.
• the grain growth inhibitory effect of the MnS phase is so limited that, starting from the usual Hot strip thicknesses of z. B. 2.30 mm at least two-stage cold rolling to the thickness of the tape is necessary and between the individual cold rolling a recrystallizing intermediate annealing must be carried out to obtain the desired properties.
• the material inhibited by MnS in the course of this treatment only reaches a limited texture sharpness, in which the Goss layer scatters on average by 7 ° around the ideal position. This texture sharpness is reflected in a comparably low magnetic polarization J 800 at a field strength of 800 A / m, which is rarely able to exceed values above 1.87 T.
• the commercial name for such procured material is "Conventional Grain Oriented", in short "CGO".
• a nitriding treatment, as required in the methods of an acquired inhibition method is, if it is carried out in a completed annealing annealing furnace, technically complex, costly and often very difficult to control because of the very precise surface reactions to be controlled.
• Other nitration treatments using nitrogen-donating adhesive additives have only limited effectiveness.
• the hot-rolled strip thickness is preferably selected so that the subsequent cold-rolling process only has to be carried out in one stage in order to achieve the required final thickness of the cold-rolled strip material obtained.
• degree of deformation of this cold rolling depends on the respective adjustable in various ways inhibitor effect.
• the object of the invention was to provide a method which allows using the GWA process cost-effective and with reduced operating costs grain-oriented electrical tapes or to produce sheets whose magnetic properties at least correspond to the properties of CGO material.
• the invention proposes a method whose operations are carried out in accordance with claim 1.
• the invention is based on a grain-oriented electrical steel strip or sheet known per se base alloy system, in addition to iron and unavoidable impurities an Si content of 2 - 6.5 Wt .-%, typically by 3.2 wt .-%, and had to adjust the special features of According to the invention produced electrical tape or sheet contained further alloying elements.
• alloying elements were carbon, sulfur, nitrogen, copper, manganese, aluminum and chromium.
• Thermodynamic model calculations were performed on this multi-component alloy system.
• Silicon in electrical tapes or sheets causes an increase in the specific resistance and thus a reduction in the re-magnetization loss.
• levels below 2% by weight the properties required for use as a grain oriented electrical steel are no longer achieved.
• Optimal processing properties result when the Si contents are in the range of 2.5-4 wt.%.
• Si contents of more than 4% by weight some brittleness of the steel strip occurs, but at Si contents of up to 6.5% by weight, the noise-causing magnetostriction is minimized. Even higher Si contents appear to be too strong However, lowering the saturation polarization does not make sense.
• a particularly important component of the process according to the invention is that it uses sulfides which are eliminated during hot working as inhibitors. Only by the nucleation sites existing there during the transformation can a uniform finely dispersed inhibitor particle distribution be set, as is necessary for effective grain growth inhibition, ie the formation of irregularly sized grains, and thus good magnetic properties.
• AlN particles formed during hot working are not suitable as a useful inhibitor in both ferrite and austenite because precipitates would always occur in both the ferrite and austenite prior to the onset of hot working very few and very coarse particles would lead to the unfavorable properties of the resulting electrical tape or sheet would entail.
• the content of acid-soluble Al in the steel processed according to the invention may be up to 0.08% by weight, with acid-soluble Al contents of 0.025-0.040% by weight having been proven in practice.
• the N content should be kept as low as possible and not exceed 30 ppm. Nitrogen binds with Al to AlN. In order for sufficient free Al to remain available for optional nitriding treatment, in the case of the present invention, in the case of the effective presence of Al for the ratio% N /% Al of the N content% N to the Al content% Al:% N /% Al ⁇ 0.25.
• the inventive method is completely unaffected by the presence of aluminum.
• the nitrogen content of the melt analysis is kept low, typically below 30 ppm, pure Al is present in the primary recrystallized and decarburized cold rolled strip to finished strip thickness.
• This cold-rolled strip can then be subjected to a nitriding treatment during the decarburization annealing or thereafter, thereby forming AlN particles in the ribbon which act as an additional inhibiting phase, so that a higher Goss texture sharpness can be formed, which can produce magnetic properties similar to those of conventional HGO material are common.
• MnS is also unsuitable as an inhibitor for the process according to the invention, since the solubility temperature is so high that MnS separates clearly before hot rolling, ie already during reheating of the respectively processed thin slab or on its way to the hot rolling device used for hot rolling , In addition, because of the strong affinity of manganese for sulfur at higher Mn contents, the sulfur content deliberately provided for in the steel would almost completely set. Accordingly, the use of MnS as an inhibitor would hardly provide any free sulfur for the formation of copper sulfides during hot working.
• the Mn content is limited to up to 0.1% by weight and at the same time in the case of the presence of Mn for the ratio% Mn /% S of the Mn content% Mn to S Salary% S given the condition:% Mn /% S ⁇ 2.5.
• the invention uses CuS as an inhibitor.
• copper sulfides in the dynamic case in principle, have such low solubility temperatures that they are present in the chemical compositions customary today only excrete at temperatures at which in the conventional production of grain-oriented electrical steel strip or sheet, the coiling of the hot strip.
• the desired goal of a targeted finely dispersed inhibitor excretion is missed.
• the solubility temperature for copper sulfides has been raised by alloying measures so that their precipitation can take place during hot forming.
• the Mn content is lowered as far as possible.
• the aim is to achieve the range of inefficiency, which is why the Mn range to a maximum of 0.1 wt .-%, in particular max. 0.05 wt .-%, is limited.
• the sulfur content was increased to 0.01 wt .-% and thus so far that the mass ratio% Mn /% S each ⁇ 2.5, in particular ⁇ 2 compared with typical grain-oriented electrical steel. This ensures that sufficient free sulfur is always available for the formation of copper sulphides.
• the solubility and thus also the precipitation temperature could be increased by more than 50 ° C in the steel processed according to the invention. If we are talking about "copper sulfides", then by the way, that means the whole group CuxSy compounds, too if they can have very different proportions.
• a steel processed according to the invention comprises not less than 0.1% by weight of Cu. At the top, the Cu content is limited to 0.5% by weight in order to avoid deterioration of the surface finish of the grain-oriented electrical sheet or strip produced according to the invention.
• the S content of the steel according to the invention is at most 0.100% by weight.
• a slab heating temperature of up to 1200 ° C. and times between casting and solidification, homogenization annealing and hot rolling are required, which are available today Casting machines can be realized.
• the hot rolling pass plan used in the method according to the invention is also adapted such that the temperature of the rolling stock is below the precipitation temperature for copper sulfide over as many hot-forming passes as possible.
• the composite according to the invention in the course of the steel inventive method in a conventional manner to 35 - 100 mm, in particular max. 80 mm thick thin slabs processed. This is usually done by conventional continuous casting.
• the simultaneously low Mn content and the concomitant formation of FeS should be selected when pouring the melt according to the invention to the strand from which then the invention processed thin slabs are divided, the casting speed comparatively low to the Danger of strand breakthroughs to be avoided.
• the casting speed during casting can be limited to a maximum of 4.6 m / min.
• the overheating of the melt in the tundish is preferably 3 to 50 K.
• a sufficient amount of casting powder is melted on the bath level in order to ensure the required amounts of slag for the film formation between the mold and the strand shell.
• pouring can be enabled by using a casting powder that is modified to have an increased reflow rate compared to high superheat casting. This can be achieved by adjusting the amount and type of carbon carriers and increasing the flux content of the casting powder.
• the advantage of very low superheat casting is fast Strand growth in the mold and a significant refinement of the solidification structure.
• the parameters of the post-casting heat treatment and the hot rolling of the thin slabs are particularly adjusted to avoid problems that might otherwise be caused by the formation of liquid FeS (iron sulfide).
• liquid FeS iron sulfide
• free sulfur is still available after the saturation of the manganese, which in any case is present only in small amounts
• liquid iron sulphide forms in the otherwise solid solidified matrix of the steel prior to the formation of copper sulphide.
• the liquid FeS causes such heat brittleness that hot rolling would not be possible.
• the inventors have found that from a ratio% Mn /% S ⁇ 2.5 significant proportions of liquid FeS down to temperatures around 1030 ° C are present.
• the thin slabs are thermally homogenized over a period of 10 -120 min in a compensation furnace.
• the tempered in the manner described above thin slabs get into the hot roll each used in the invention and are hot rolled therein to form a hot strip with a thickness of 0.5 - 4.0 mm.
• the hot working degree achieved in the course of the first two rolling passes should be at least 40% each.
• the hot rolling end temperature ie the temperature of the hot strip obtained when leaving the last Hot rolling stand of the hot roll stand used for hot rolling according to the invention is at least 710.
• the temperatures of the rolling stock during the last pass are typically in the range of 800-870
• the hot strip produced in accordance with the invention is suitable for the production of grain-oriented electrical steel strip.
• an annealing of the hot strip before the cold deformation is not absolutely necessary, but can optionally be carried out at temperatures of 950-1150 ° C to increase the near-surface regions of the hot strip, which have an advantageous texture, and thereby the magnetic properties of the finished grain-oriented Electrical strip or sheet to improve further.
• the hot strip is cold rolled in one or more steps to the use thickness of 0.50 - 0.15 mm. In several cold rolling steps, a recrystallizing intermediate annealing is carried out in between.
• a nitriding treatment may take place in which the strip is annealed in an annealing atmosphere containing NH 3 to thereby increase the N content of the strip.
• the cold strip produced in this way is subsequently coated with an annealing separator, which usually comprises MgO, for subsequent high-temperature crown annealing.
• the Glühseparator can contain nitrogen-containing additives that support the nitriding process. Particularly suitable for this purpose are N-containing substances which decompose thermally in the range from 600 to 900.degree.
• the secondary recrystallization high-temperature annealing can be carried out in a conventional manner. According to a practical embodiment, it is carried out as a bell annealing, wherein in the range between 400 - 1100 ° C heating rates of 10 - 50 K / h can be achieved.
• the resulting electrical steel strip can be provided with a surface insulation layer in a continuous strip-passing annealing line and annealed with low stress.
• a domain refinement treatment carried out in a manner known per se can follow.
• a melt containing in addition to iron and unavoidable impurities (in% by weight) 3.05% Si, 0.045% C, 0.052% Mn, 0.010% P, 0.030% S, 0.206% Cu, 0.067% Cr, 0.030% Al, 0.001% Ti, 0.003% N, 0.011% Sn, 0.016% Ni was cast into a strand from which thin slabs having a thickness of 63 mm and a width of 1100 mm were divided. After a free uncontrolled cooling to about 900 ° C was followed by a homogenization annealing, in which the thin slabs were heated to 1050 ° C.
• the thin slabs were hot rolled in a seven successively run through rolling mills comprising hot rolling mill to a hot strip with a hot strip thickness of 2.30 mm.
• the temperature of the rolling stock was in the first pass in the range of 960-980 ° C, while in the second rolling pass 930-950 ° C.
• the hot rolling end temperature was 840 ° C.
• the resulting hot strip was pickled without annealing and cold rolled in a cold rolling step to the finished strip thickness of 0.285 mm. This was followed by a recrystallizing and decarburizing continuous annealing treatment in which the cold strip was annealed for 180 s at 850 ° C. in a humid nitrogen, hydrogen and about 10% NH 3 -containing atmosphere. Subsequently, the cold strip has been surface-coated with MgO as Glühseparator.
• the MgO annealing separator served as adhesive protection for a subsequent high-temperature bell annealing, in which the cold strip was heated under hydrogen at a heating rate of 20 K / h up to a temperature of 1200 ° C where it has been held for over 20 hours.
• the resulting finished strip is finally coated with a phosphating and then stress-free annealed at 880 ° C and then cooled evenly.
• the grain-oriented electrical steel produced in the manner described above showed good magnetic properties, which are in the range of commercially available HGO. Its loss of magnetization at 50 Hz and 1.7 T modulation was 0.980 W / kg at a polarization of 1.93 T under a field strength of 800 A / m.
• the melts were cast in a continuous casting process into thin slabs with a thin slab thickness of 63 mm.
• the overheating temperature of the melt in the tundish was 25-45 K.
• the casting speed in the continuous casting was in the range of 3.5-4.2 m / min.
• the strand cooled to about 900 ° C before entering the roller hearth furnaces.
• the thin slabs separated from the rod are reheated to temperatures between 1030 and 1070 ° C for 20 minutes in an equalizing furnace and then placed in a blender Hot rolling has been supplied.
• the actual set reheating temperatures SRT are given in Table 2 as well as the ratios% Mn /% S and% Cu /% S in the alloys of melts A and B.
• the temperature of the thin slabs dropped to values around 1000 ° C, whereby it was checked that the metallurgical critical limit of 1030 ° C remained reliably undercut.
• the pass schedule of the hot rolling mill used for hot rolling of the thin slabs comprising seven rolling mills, has been designed so that the first and the second forming pass resulted in a reduction of about 55% in the first and about 48% in the second hot forging.
• the temperature of the rolling stock during the first two hot-formed passes was between 950-980 ° C in the first pass and 920-960 ° C in the second pass.
• the hot rolling end temperatures ranged from 800 to 860 hot rolled thicknesses were in the range of 2.0 to 2.8 mm.
• the hot strips thus produced are annealed at 1080 ° C under inert gas and then cooled with water accelerated. This was followed by surface descaling in a pickling bath.
• the further processing included a two-stage cold rolling with recrystallizing intermediate annealing to a finished strip thickness of 0.30 mm, a subsequent recrystallizing and decarburization annealing, an order of an essentially consisting of MgO Glühseparators and a high-temperature bonnet annealing to carry out the secondary recrystallization and an order of an insulator and a relaxing directional annealing at the end, these operations have been carried out in a manner known per se from the prior art.
• the mean values of the magnetic properties are P 1.7 (Loss of magnetization at 50 Hz and 1.7 T modulation), J 800 (Polarization under a field intensity of 800 A / m), and the proportion of magnetic degradation for those from the melts A and B in the manner explained above produced electrical tapes at the finished strip nominal thickness 0.30 mm.
• the further processing was carried out via a one-stage cold rolling to the Fertigbandnendie thickness 0.23 mm and a subsequent recrystallizing and decarburization annealing, which has been simultaneously nitrided during the decarburization by adding 15% NH 3 to the annealing gas.
• a subsequent recrystallizing and decarburization annealing which has been simultaneously nitrided during the decarburization by adding 15% NH 3 to the annealing gas.
• MgO existing Glühseparator applied as an adhesive
• the secondary recrystallization was carried out in a high-temperature bell annealing.
• the insulation coating has been applied and a relaxing directional annealing has been carried out.
• the finished tape has undergone domain refinement by laser treatment.
• the steps of processing the hot strip into a cold rolled HGO steel strip have also been carried out in a manner known per se from the prior art.
• Thin slabs from the melt C are deviating from the specifications according to the invention hot rolled. Specifically, the hot working temperatures were varied in the first two passes. This was possible by initially setting the temperature of the equalization furnace a little higher and by rapid operation starting hot working at higher temperatures. Subsequently, the compensation furnace temperatures are lowered to the usual target value of the given system and the hot working start temperatures have been varied by different time delays.
• Table 7 shows the operating parameters "reheating temperature SRT”, "temperature ⁇ F1 of the rolling stock in the first forming pass", “temperature ⁇ F2 of the rolling stock in the second forming pass” and the percentage of those in the experiments for experiments 1 to 18 produced electrical sheets that fall in the respective range of Ummagnetmaschinesppen P 1.7 .
• the invention thus provides a method for producing a grain-oriented electrical strip or sheet, in which generally the slab temperature of a thin slab made of a steel having (in wt.%) Si: 2-6.5%, C: 0.02 - 0.15%, S: 0.01 - 0.1%, Cu: 0.1 - 0.5%, wherein the Cu to S content ratio is% Cu /% S> 4, Mn: up to 0.1%, wherein the Mn to S content ratio is% Mn /% S ⁇ 2.5, and optional contents of N, Al, Ni, Cr, Mo, Sn, V, Nb is homogenized to 1000 - 1200 ° C, wherein the thin slab to a hot strip with a thickness of 0.5 - 4.0 mm at a hot rolling start temperature ⁇ 1030 ° C and a hot rolling end temperature ⁇ 710 ° C and a reduction in thickness in both the first as well as in the second hot forming pass of ⁇ 40% to a hot strip, the hot strip is cooled and coiled into a coil

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