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
  • C21D6/00—Heat treatment of ferrous alloys
• • 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
  • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
  • C21D8/1233—Cold rolling
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
  • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
  • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
  • C21D8/1266—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest between cold rolling steps
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
• • 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
  • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
• • 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
  • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
• • 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
• • 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
  • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
• • 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
  • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt

Definitions

• the present invention relates to a non-grain-oriented electrical steel, with a special composition and texture, a process for its production, comprising at least the following process steps (A) providing a hot-rolled, optionally separately annealed, non-grain-oriented electrical steel, preferably both via the conventional production route via Continuous caster as well as thin slab production, in a thickness of 1 to 4 mm, (B) cold rolling the electrical strip from step (A) to a thickness of 0.5 to 0.8 mm to obtain a first cold strip, (C) intermediate annealing of the first cold strip from step (B) at a temperature of 700 to 1100 ° C.
• step (D) cold rolling the annealed first cold strip from step (C) to a thickness of 0.24 to 0 , 36 mm to obtain a second cold strip, and (E) final annealing the second cold strip from step (D) at a temperature of 900 to 1100 ° C to the to get grain-oriented electrical steel.
• Non-grain oriented (NO) electrical steel is used to increase the magnetic flux in iron cores from rotating electrical machines, i.e. used in motors and generators.
• NO electrical machines i.e. Electric motors with high speeds for traction drives of electric vehicles
• special NO electrical steel grades with a low magnetic loss at high frequencies and high magnetic polarization or induction with high permeability are required.
• WO 2015/170271 A1 describes a NO electrical steel strip or sheet which has a low loss depending on the thickness and is made from a steel which, in addition to iron and unavoidable impurities (in% by weight), ranges from 0.001 to 0 , 01% C, 1.8 to 6.0% Si, 0.2 to 4.0% AI, 0.2 to 3.0% Mn, 0.0005 to 0.01% S, 0.001 to 0.01 % N contains and in which the ratio of Mn content to S content is over 100 and the ratio Al content to N content is over 200.
• the steel thus assembled is cast into slabs with a thickness greater than or equal to 20 mm, which are optionally reheated between 1000 and 1330 ° C and then hot rolled between 1300 and 700 ° C to a hot strip with a degree of deformation of 70 to 99%, to obtain a hot strip thickness of 2.5 to 12 mm.
• the hot strip is cold rolled with a total degree of forming of at least 80%.
• a first cold rolling step takes place with a degree of deformation of 20 to 70% at a temperature below 300 ° C.
• the cold strip is subjected to intermediate annealing at 700 to 1100 ° C for a time between 10 to 900 s.
• the cold strip obtained is subjected to a recrystallizing annealing, in which it is temperature of at least 800 ° C, but less than 1200 ° C annealing temperature for a period of 10 to 900 s.
• the object of the invention was to provide a NO electrical strip or sheet and a component made from such a sheet or strip for electrotechnical applications, which has low magnetic loss losses and at the same time high polarization values, achieved by an improved Texture, possesses.
• these low magnetic reversal losses are to be found under standardized conditions at 1.5 T and 50 Hz and high polarization values J2500 and J5000, but also low magnetic reversal losses at higher basic frequencies of e.g. 400 Hz, 700 Hz, 1000 Hz or more can be achieved.
• These low magnetic reversal losses and high polarizations are said to have, in particular, non-grain-oriented electrical steel strips with a silicon content of 2.1 to 3.4% by weight of Si.
• a method for producing such a NO electrical strip or sheet should be specified which has good processability, in particular at low final thicknesses.
• step (B) cold rolling the electrical strip from step (A) to a thickness of 0.5 to 0.8 mm to obtain a first cold strip
• step (C) intermediate annealing of the first cold strip from step (B) at a temperature of 700 to 1100 ° C. in order to obtain an intermediate annealed first cold strip
• step (D) cold rolling the annealed first cold strip from step (C) to a thickness of 0.24 to 0.36 mm to obtain a second cold strip
• step (E) Final annealing of the second cold strip from step (D) at a temperature of 900 to 1100 ° C to obtain the non-grain oriented electrical steel.
• An optimal texture is achieved in this case by the process-related adjustment of the orientation of the grains in the electrical steel through a two-stage production with intermediate annealing during cold rolling, so that the grains have an energetically favorable crystallographic direction for magnetic reversal in the sheet metal plane.
• the two-stage cold rolling process with intermediate thickness allows a simplified and sometimes more precise production of lower final thicknesses of the highly silicated electrical steel due to a softened structure in the second rolling step.
• step (A) of the method according to the invention are known per se to the person skilled in the art.
• the thickness of the non-grain-oriented electrical tape provided in step (A) is preferably 1 to 4 mm, particularly preferably 1.5 to 2.4 mm.
• non-grain-oriented electrical steel known to the person skilled in the art can be used.
• the non-grain-oriented hot strip which is provided in step (A), preferably has the following composition (all data in% by weight)
• the steel analysis preferably used according to the invention contains Si in an amount of 2.1 to 3.6% by weight, preferably 2.7 to 3.4% by weight.
• Si has the effect of increasing the specific electrical resistance and reducing the magnetic losses.
• the minimum amount of Si should be at least 2.1% by weight, since otherwise the specific electrical resistance is too low and thus the magnetic loss is too high and an austenite-ferrite phase transformation is to be avoided. If more than 3.6% by weight of Si is used according to the invention, the formability deteriorates and the magnetic flux density is reduced too much.
• the steel analysis which is preferably used according to the invention contains Al in an amount of 0.3 to 1.2% by weight, preferably 0.3 to 0.75% by weight. % By weight.
• AI has the effect in the non-grain-oriented electrical steel according to the invention that it also increases the specific electrical resistance.
• the minimum amount of AI should be at least 0.3% by weight, otherwise the specific electrical resistance is too low and the magnetic loss is too high. If more than 1.2% by weight of Al is used according to the invention, the cold formability deteriorates, in particular in combination with Si contents from 2.9% by weight.
• the steel analysis preferably used according to the invention contains Mn in an amount of 0.01 to 0.5% by weight, preferably 0.07 to 0.3% by weight.
• Mn has the effect of increasing the specific electrical resistance.
• the minimum amount of Mn should be at least 0.01% by weight, since otherwise the specific electrical resistance is too low and the magnetic loss is too high. If more than 0.5% by weight of Mn is used according to the invention, the magnetic flux density is reduced.
• the hot-rolled, non-grain-oriented electrical steel used in step (A) of the method according to the invention can be an element selected from the group consisting of up to 0.05% by weight Cr, up to 0.005% by weight Zr, up to 0 , 04% by weight Ni, up to 0.05% by weight Cu, up to 0.005% by weight Ca, up to 0.005% by weight of at least one rare earth metal, up to 0.005% by weight Co and mixtures thereof contain.
• P, Ti, C, S, B and / or N are considered inevitable impurities in the context of the present invention.
• P is present, it tends to segregate, which is difficult to balance, and worsens cold formability, weldability, and oxidation resistance. If present, P is present in an amount of 0.005 to 0.03% by weight.
• Ti is present, it increases the strength, in particular through the formation of Ti carbides, and the corrosion resistance. Titanium precipitates influence the recrystallization of the grains in the slab. If present, Ti is present in an amount of 0.001 to 0.006% by weight.
• C should be avoided if possible.
• C can be set by carbide formers, for example Ti, Nb, Mo, Zr, W or Ta, and forms too many undesirable carbides (Al, Ti, Cr). If present, C is present in an amount up to 0.005% by weight. If C is present in higher quantities, then the magnetic aging that is present increases the magnetic losses to an unacceptable order.
• S If S is present, it forms sulfides, for example MnS, CuS and / or (Cu, Mn) S, which are bad for the magnetic properties of the material. If present, S is present in an amount up to 0.005% by weight.
• the N content is as low as possible in order to reduce the formation of disadvantageous Al and / or Ti nitrides.
• Al nitrides can impair the magnetic properties. If present, N is present in an amount of at most 0.005% by weight.
• C, S, Ti and N are present in the material according to the invention in total at most in an amount of 0.01% by weight.
• step (A) of the process according to the invention is preferably carried out via the conventional production route via a continuous casting plant or via thin slab production. Both methods are known to the person skilled in the art.
• step (A) can preferably be used directly in step (B) of the process according to the invention.
• the present invention relates to the method according to the invention, wherein after step (A), ie before step (B), a hood annealing takes place at a temperature of 640 to 900 ° C., preferably at a temperature of 650 to 800 ° C.
• Step (B) of the method according to the invention comprises cold rolling the electrical strip from step (A) to a thickness of 0.5 to 0.8 mm in order to obtain a first cold strip.
• step (B) of the method according to the invention the hot-rolled electrical steel obtained from step (A) is cold-rolled to a thickness of 0.5 to 0.8 mm, preferably 0.6 to 0.75 mm.
• Step (B) of the method according to the invention is preferably carried out at a temperature of up to 240 ° C.
• the cold rolling in step (B) is carried out with a degree of cold rolling of 30 to 90%, particularly preferably 60 to 80%.
• step (B) of the method according to the invention a first cold strip is obtained. This is preferably transferred directly to step (C) of the process according to the invention.
• Step (C) of the process according to the invention comprises intermediate annealing of the first cold strip from step (B) at a temperature of 700 to 1100 ° C. in order to obtain an intermediate annealed first cold strip.
• Step (C) of the process according to the invention is preferably carried out at a temperature of 900 to 1050 ° C. According to the invention, step (C) can take place in any device known to the person skilled in the art. Step (C) of the process according to the invention is particularly preferably carried out in a continuous furnace.
• Step (D) of the method according to the invention comprises cold rolling the annealed first cold strip from step (C) to a thickness of 0.24 to 0.36 mm in order to obtain a second cold strip.
• step (D) of the process according to the invention the intermediate annealed first cold strip obtained from step (C) is cold rolled in one or more steps to a thickness of 0.24 to 0.36 mm.
• Step (D) of the process according to the invention is preferably carried out at a temperature of up to 240 ° C.
• the cold rolling in step (D) is carried out with a degree of cold rolling of 30 to 90%, particularly preferably 40 to 80%.
• a second cold strip is obtained.
• the formulations “first cold strip” and “second cold strip” are used to differentiate the cold strips from step (B) or step (D) by name.
• the second cold strip obtained in step (D) is preferably transferred directly to step (E) of the process according to the invention.
• Step (E) of the method according to the invention comprises the final annealing of the second cold strip from step (D) at a temperature of 900 to 1100 ° C. in order to obtain the electrical steel which is not grain-oriented.
• Step (E) of the process according to the invention is preferably carried out at a temperature of 950 to 1050 ° C.
• step (E) can take place in any device known to the person skilled in the art.
• Step (C) of the process according to the invention is particularly preferably carried out in a continuous furnace.
• step (E) of the method according to the invention the non-grain-oriented electrical steel according to the invention having the advantageous properties described above is obtained.
• Step (E) of the method according to the invention can be followed by method steps known to the person skilled in the art, for example trimming, cleaning, reeling, etc.
• All anneals in the process according to the invention are preferably carried out above 500 ° C. in a non-iron oxidizing atmosphere.
• Magnetic properties can be represented by the method according to the invention, in particular by the two-stage cold rolling with intermediate annealing, which cannot be represented with a combination of the characteristics loss and polarization with a single-stage cold rolling.
• the structure is softened by the intermediate annealing, which means that the required force or energy requirement for the subsequent cold rolling steps is reduced for the intermediate thickness obtained for the second cold rolling step, and thus a smaller final thickness can also be manufactured more precisely.
• the present invention therefore also relates to the non-grain-oriented electrical steel produced by the method according to the invention.
• a non-grain-oriented electrical steel can be provided, which is possible due to the possibility of producing small thicknesses and particularly high polarization values J2500 and J5000 in combination with low ones Magnetic reversal losses are distinguished both at low frequencies of, for example, 50 Hz and at high frequencies of, for example, 400 or 700 Hz.
• the present invention also relates to the non-grain-oriented electrical steel, it having the following composition and texture (all figures in% by weight)
• the recrystallization is influenced by the intermediate annealing according to the invention (step (Q) and thus the texture is changed.)
• the examples according to the invention and the comparative examples show that a less sharp texture is formed after the final annealing than in a single-stage cold rolling after the final annealing.
• the microstructure is set according to the invention by means of two-stage cold rolling with intermediate annealing in such a way that an optimized texture is obtained.
• the intensity of the texture in the crystallographic direction or fiber should be a ( ⁇ 110>
• This can be demonstrated, for example, by the orientation distribution function (OVF) and the orientation density (ODF) along the fibers.
• orientation distribution functions By determining orientation distribution functions (OVF), the differences in texture can be determined based on the procedures with and without intermediate thickness. For this purpose, five samples are measured per example using X-ray diffractometry (XRD). The chemical surface treatment removes 30 pm from each side of the sample beforehand in order to exclude surface effects. Then ⁇ 110 ⁇ -, ⁇ 200 ⁇ -, and the ⁇ 21 l ⁇ pole figures for each of the five samples are determined with Co-Ka and the mean value is calculated from these measurements. The OVF is then determined from these mean pole figures using a program. In order to be able to compare the OVFs better, sections of the orientation densities f (g) of the fibers (a, y, z, e) can be represented and the intensities I can be compared in certain orientations.
• XRD X-ray diffractometry
• the difference in texture due to the procedures with and without intermediate thickness can be determined by the difference in the intensities of the orientation densities f (g) of the z-fiber, which has a positive effect on the magnetic properties, with the orientation ⁇ 110 ⁇ ⁇ 001>, and the magnetically poor y- Fix the skeleton line in the e-fiber with the orientation ⁇ 554 ⁇ ⁇ 225>, accordingly , ⁇ 554 ⁇ ⁇ 225 > - , aio ⁇ ⁇ ooi > . which is ⁇ 3 according to the invention.
• the present invention preferably relates to the non-grain-oriented electrical steel according to the invention, it having a final thickness of 0.24 to 0.36 mm.
• final thickness means the thickness of the non-grain-oriented electrical strip after the second cold rolling step.
• the present invention further preferably relates to the non-grain-oriented electrical steel according to the invention, the following relationships applying to the polarization J2500 / 50 at 2500 A / m and 50 Hz and the magnetic reversal loss R 1i 5/5 o at 1.5 T and 50 Hz: not hot strip haubengeglühtem material: J2500 / 50> -0.045 * P 15/5 0 2 + 0.3 * P 15/5 o + 1.085 (1)
• the magnetic reversal losses P can be determined according to the invention by all methods known to the person skilled in the art, in particular by means of an Epstein frame, in particular in accordance with DIN EN 60404-2: 2009-01: Magnetic materials - Part 2: Method for determining the magnetic properties of electrical steel and sheet metal Help of an epstein frame ”. Corresponding electrical sheets are cut into longitudinal and transverse strips and measured as a mixed sample in the Epstein frame.
• the non-grain-oriented electrical tape described here characterizes an anisotropy of the magnetic loss values at 1.5 T and 50 Hz in the longitudinal and transverse directions of less than 20%.
• the present invention also relates to the use of a non-grain-oriented electrical band according to the invention in iron cores of rotating electrical machines, in particular in electric motors and generators.
• FIG. 1 shows the improvement according to the invention in the case of non-hot-strip annealed material from examples 1, 2, 5 and 6.
• FIG. 2 shows the improvement according to the invention in hot-strip annealed material from Examples 3, 4, 7, 8, 13, 14 and 15 to 18.
• FIG. 3 shows the orientation densities of the ODF along the e fibers in the Euler space at fi at 90 °, cp 2 at 45 ° and f in the range from 0 ° to 90 ° for example 1.
• FIG. 6 shows orientation densities of the ODFs along the z fibers in the Euler space at cp-i from 0 ° to 90 °, cp 2 at 0 ° and f at 45 ° for example 2.
• Example 1 composition 1 according to Table 1 is used.
• Examples 5, 6, 7 and 8 and comparative samples 1, 2, 3 and 4 according to the invention were produced.
• the slab obtained was hot-rolled, optionally subjected to hot-strip hood annealing at 740 ° C. and cold-rolled to an intermediate thickness of 0.70 mm.
• the material was then annealed at 1000 ° C, cold rolled to a final thickness of 0.34 mm and then finally annealed between 1000 ° C to 1080 ° C.
• the comparative sample 4 was hot-rolled after melting, subjected to hot strip annealing, cold-rolled directly to a final thickness of 0.34 mm and finally annealed at 1000 ° C.
• Comparative sample 3 results from the standard process, ie single-stage cold rolling with hot strip hood annealing, for details see table 2.
• the magnetic parameters, ie J 100 , J5000, J2500, Pi , 5 / 5o and Ri , o / 400 . were determined for samples with and without intermediate thickness after the final annealing.
• the values for the polarization J are 50 Hz and 400 Hz higher than the values of the comparable comparative examples of the same thickness of 0.35 mm over the field strength range up to saturation for both frequencies tested.
• Formula 1 (for non hot strip annealed material): J2500 / 50> -0.045 * P15 / 50 2 + 0.3 * P15 / 50 + 1.085
• Formula 2 (for hot-rolled hood annealed material): J2500 / 50> -0.045 * P15 / 50 2 + 0.28 * P15 / 50 + 1, 165
• Radiographic texture determinations were carried out with CoKa radiation and the ⁇ 100 ⁇ , ⁇ 200 ⁇ and ⁇ 21 l ⁇ pole figures of the final annealed samples 1, 3, 5, 7, 9, 11, 12 and 14 were determined. For better measurement statistics, 5 x-ray samples were measured from each of the samples. The orientation distribution functions (OVF) were calculated from the mean pole figures.
• the orientation of the crystal coordinate system relative to the sample coordinate system can be represented by the OVF by assigning an orientation density f (g) or intensity I to each point in a space spanned by the Euler angles fi, cp 2 and f.
• orientation distribution functions can be mapped using the intensity of fibers in the cut surfaces of this room.
• the e and z fibers are considered here.
• the orientation densities f (g) of the z and e fibers were plotted for the course of Euler angles from 0 to 90 °.
• FIGS. 3 to 6 show the course of the OVF against the angle f for the e-fiber and against the angle q ⁇ for the z-fiber.
• the special locations ⁇ 554 ⁇ ⁇ 225>, ⁇ 110 ⁇ ⁇ 001> and others are shown.
• Samples 1, 3 and 9 of the one-stage production have the main intensity of their texture in the vicinity of the magnetically poor g-fiber or the g-skeleton line (see ⁇ 554 ⁇ ⁇ 225> in the e-fiber).
• the e-fiber contributes to a deteriorated texture at ⁇ 554 ⁇ ⁇ 225>, since the ideal g-fiber can shift by a few degrees during production, which is referred to as the g-skeleton line.
• a skeleton line denotes a connecting line of points of highest intensity through the Euler space and intensity fluctuations along this can be interpreted as a fluctuation within the fault tolerance. Therefore, the maximum intensity I of the y fiber shifts towards the e fiber at cp-i at 90 °, cp 2 at 45 ° and f at 60 ° and orientation ⁇ 554 ⁇ ⁇ 225>.
• the inventive method of two-stage production reduces the orientation density of this poor e-fiber texture value at ⁇ 554 ⁇ ⁇ 225> (see Table 3 and Figures 3 to 6).
• the z-fiber which contains no magnetically heavy magnetic reversal direction, is more heavily occupied in the two-stage production according to the invention than in the one-stage production.
• the individual values are listed in Table 4.
• a non-grain-oriented electrical steel strip can be produced by the method according to the invention, which is characterized by particularly low magnetic loss both at low and high frequencies and good rollability, so that it can be rolled particularly thin. It can therefore be used advantageously in rotating electrical machines, in particular in electric motors and generators.

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• 2018
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