US20230193413A1 - Method for producing an no electric strip of intermediate thickness - Google Patents

Method for producing an no electric strip of intermediate thickness Download PDF

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US20230193413A1
US20230193413A1 US17/285,333 US201817285333A US2023193413A1 US 20230193413 A1 US20230193413 A1 US 20230193413A1 US 201817285333 A US201817285333 A US 201817285333A US 2023193413 A1 US2023193413 A1 US 2023193413A1
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electrical steel
cold
steel strip
strip
oriented electrical
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Olaf Fischer
Karl Telger
Anton Vidovic
Nina Maria Winkler
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ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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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
    • 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
    • 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
    • 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
    • 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-oriented electrical steel strip having a specific composition and texture, a process for the production thereof, comprising at least the following process steps (A) provision of a hot-rolled, optionally separately heat-treated, non-oriented electrical steel strip, preferably by the conventional manufacturing route via a continuous casting plant or by thin slab manufacture, in a thickness of from 1 to 4 mm, (B) cold rolling of the electrical steel strip from step (A) to a thickness of from 0.5 to 0.8 mm in order to obtain a first cold-rolled strip, (C) intermediate heat treatment of the first cold-rolled strip from step (B) at a temperature of from 700 to 1100° C.
  • step (D) cold rolling of the intermediate-heat-treated, first cold-rolled strip from step (C) to a thickness of from 0.24 to 0.36 mm in order to obtain a second cold-rolled strip and (E) final heat treatment of the second cold-rolled strip from step (D) at a temperature of from 900 to 1100° C. in order to obtain the non-oriented electrical steel strip.
  • Non-oriented (NO) electrical steel strip is used for increasing the magnetic flux in iron cores of rotating electric machines, i.e. in motors and generators. Future highly efficient electric machines, e.g. electric motors having high speeds of rotation for traction drives of electric vehicles, will require specific types of NO electrical steel strip having a low magnetic loss at high frequencies and high magnetic polarization or induction with high permeability.
  • WO 2015/170271 A1 describes, for example, an NO electrical steel strip or sheet which has a low loss as a function of the thickness and is made of a steel which contains, apart from iron and unavoidable impurities, (in % by weight), from 0.001 to 0.01% of C, from 1.8 to 6.0% of Si, from 0.2 to 4.0% of Al, from 0.2 to 3.0% of Mn, from 0.0005 to 0.01% of S, from 0.001 to 0.01% of N and in which the ratio of Mn content to S content is more than 100 and the ratio of Al content to N content is more than 200.
  • the steel having such a composition is cast to give slabs having a thickness of greater than or equal to 20 mm, which are optionally reheated in the range from 1000 to 1330° C. and subsequently hot rolled in the range from 1300 to 700° C. to give a hot-rolled strip having a degree of deformation of from 70 to 99% in order to obtain a hot-rolled strip thickness of from 2.5 to 12 mm.
  • the hot-rolled strip is cold rolled with a total degree of deformation of at least 80%.
  • a first cold rolling step is carried out with a degree of deformation of from 20 to 70% at a temperature below 300° C.
  • the cold-rolled strip is subjected to an intermediate heat treatment at from 700 to 1100° C. for a time of from 10 to 900 s.
  • the second cold rolling step is followed by a second cold rolling step with a degree of deformation in the range from 20 to 70% to a final thickness of from 0.15 to 0.5 mm.
  • the second cold rolling step can be repeated a third time with additional heat treatment.
  • the cold-rolled strip obtained is subsequently subjected to a recrystallization heat treatment in which it is heat treated at a temperature of at least 800° C., but at a heat treatment temperature of less than 1200° C., for a time of from 10 to 900 s.
  • An optimal texture is in this case achieved by the process-related setting of the orientation of the grains in the electrical steel strip by means of two-stage manufacture with intermediate heat treatment during cold rolling, so that the grains have an energetically favorable crystallographic direction for magnetic reversals in the plane of the metal sheet. Due to a dehardened structure in the second rolling step, the two-stage cold rolling process with intermediate thickness allows simplified and sometimes more precise manufacture of lower final thicknesses of the highly silicized electrical steel strip.
  • non-oriented electrical steel strips as are provided in step (A) of the process of the invention are known per se to a person skilled in the art.
  • the thickness of the non-oriented electrical steel strip provided in step (A) is preferably from 1 to 4 mm, particularly preferably from 1.5 to 2.4 mm.
  • non-oriented electrical steel strip preferably has the following composition (all figures in % by weight)
  • the steel analysis which is preferably used for the purposes of the invention contains Si in an amount of from 2.1 to 3.6% by weight, preferably from 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 for performing the invention, the formability deteriorates and the magnetic flux density is reduced too greatly.
  • the steel analysis which is preferably used according to the invention contains Al in an amount of from 0.3 to 1.2% by weight, preferably from 0.3 to 0.75% by weight.
  • Al has the effect of likewise increasing the specific electrical resistance.
  • the minimum amount of Al should be at least 0.3% by weight, since otherwise the specific electrical resistance is too low and the magnetic loss is thus too high. If more than 1.2% by weight of Al is used in performing the invention, the cold formability deteriorates, in a particular case in combination with Si contents above 2.9% by weight.
  • the steel analysis which is preferably used according to the invention contains Mn in an amount of from 0.01 to 0.5% by weight, preferably from 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 thus too high. If more than 0.5% by weight of Mn is used for performing the invention, the magnetic flux density decreases.
  • the hot-rolled, non-oriented electrical steel strip used in step (A) of the process of the invention can contain an element selected from the group consisting of up to 0.05% by weight of Cr, up to 0.005% by weight of Zr, up to 0.04% by weight of Ni, up to 0.05% by weight of Cu, up to 0.005% by weight of Ca, up to 0.005% by weight of at least one rare earth metal, up to 0.005% by weight of Co and mixtures thereof.
  • unavoidable impurities are P, Ti, C, S, B and/or N.
  • P is present, it tends to result in segregations which can be evened out only with difficulty and impairs the cold formability, the weldability and the oxidation resistance. If present, P is present in an amount of from 0.005 to 0.03% by weight.
  • Ti is present, it increases the strength, in particular by 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 from 0.001 to 0.006% by weight.
  • C is to be avoided where possible.
  • C can be bound by carbide formers, for example Ti, Nb, Mo, Zr, W or Ta, and forms too large an amount of undesirable carbides (Al, Ti, Cr). If present, C is present in an amount of up to 0.005% by weight. If C is present in larger amounts, the magnetic aging which is then present increases the magnetic losses to an unacceptable extent.
  • 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 of up to 0.005% by weight.
  • N preference is given to the content of N being very low in order to reduce the formation of disadvantageous Al nitrides and/or Ti nitrides.
  • Al nitrides can impair the magnetic properties. If present, N is present in an amount of not more than 0.005% by weight.
  • C, S, Ti and N are preferably present in the material of the invention in a total amount of not more than 0.01% by weight.
  • step (A) of the process of the invention is preferably carried out by means of the conventional manufacturing route via a continuous casting plant or by thin slab manufacture. Both processes are known to a person skilled in the art.
  • the hot-rolled, optionally separately heat-treated, electrical steel strip from step (A) can preferably be used directly in step (B) of the process of the invention.
  • the present invention relates to the process according to the invention in which a bell heat treatment is carried out at a temperature of from 640 to 900° C., preferably at a temperature of from 650 to 800° C., after step (A), i.e. before step (B).
  • Step (B) of the process of the invention comprises cold rolling of the electrical steel strip from step (A) to a thickness of from 0.5 to 0.8 mm in order to obtain a first cold-rolled strip.
  • the cold rolling in step (B) is carried out with a degree of cold rolling of from 30 to 90%, particularly preferably from 60 to 80%.
  • Step (B) of the process of the invention results in a first cold-rolled strip. This is preferably transferred directly to step (C) of the process of the invention.
  • Step (C) of the process of the invention comprises intermediate heat treatment of the first cold-rolled strip from step (B) at a temperature of from 700 to 1100° C. in order to obtain an intermediate-heat-treated, first cold-rolled strip.
  • Step (C) of the process of the invention is preferably carried out at a temperature of from 900 to 1050° C.
  • step (C) can be carried out in any apparatus known to a person skilled in the art.
  • Step (C) of the process of the invention is particularly preferably carried out in a continuous furnace.
  • Step (D) of the process of the invention comprises cold rolling of the intermediate-heat-treated, first cold-rolled strip from step (C) to a thickness of from 0.24 to 0.36 mm in order to obtain a second cold-rolled strip.
  • step (D) of the process of the invention the intermediate-heat-treated, first cold-rolled strip obtained from step (C) is cold rolled in one or more steps to a thickness of from 0.24 to 0.36 mm.
  • Step (D) of the process of 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 from 30 to 90%, particularly preferably from 40 to 80%.
  • Step (D) of the process of the invention results in a second cold-rolled strip.
  • the formulations “first cold-rolled strip” and “second cold-rolled strip” are employed according to the invention to distinguish the cold-rolled strips from step (B) and from step (D).
  • the second cold-rolled strip obtained in step (D) is preferably transferred directly to step (E) of the process of the invention.
  • Step (E) of the process of the invention comprises the final heat treatment of the second cold-rolled strip from step (D) at a temperature of from 900 to 1100° C. in order to obtain the non-oriented electrical steel strip.
  • Step (E) of the process of the invention is preferably carried out at a temperature of from 950 to 1050° C.
  • step (E) can be carried out in any apparatus known to a person skilled in the art.
  • Step (C) of the process of the invention is particularly preferably carried out in a continuous furnace.
  • step (E) of the process of the invention the non-oriented electrical steel strip of the invention having the above-described advantageous properties is obtained.
  • Step (E) of the process of the invention can be followed by process steps known to a person skilled in the art, for example cutting, cleaning, reeling-up, etc.
  • All heat treatments in the process of the invention are preferably carried out at above 500° C. in an atmosphere which does not oxidize iron.
  • Magnetic properties which cannot be obtained in the combination of the features losses and polarization by means of single-stage cold rolling can be obtained by means of the process of the invention, in particular by the two-stage cold rolling with intermediate heat treatment.
  • the intermediate heat treatment dehardens the structure, as a result of which the force or energy required for the subsequent cold rolling steps to obtain the resulting intermediate thickness for the second cold rolling step is decreased and a lower final thickness can thus also be manufactured more precisely.
  • the present invention therefore also provides the non-oriented electrical steel strip produced by the process of the invention.
  • a non-oriented electrical steel strip which can be made in a low thickness and displays particularly high polarization values J2500 and J5000 in combination with low magnetic losses both at low frequencies of, for example, 50 Hz and at high frequencies of, for example, 400 or 700 Hz can be provided by the production process of the invention, in particular by means of the steps (B), (C) and (D).
  • the present invention also provides the non-oriented electrical steel strip which has the following composition and texture (all figures in % by weight)
  • step (C) influences the recrystallization and thus changes the texture. It can be shown by means of the examples according to the invention and the comparative examples that a less sharply pronounced texture is formed after the final heat treatment than in the case of a single-stage cold rolling after the final heat treatment.
  • the microstructure is, according to the invention, set by means of two-stage cold rolling with an intermediate heat treatment so that an optimized texture is obtained.
  • the intensity of the texture in the crystallographic direction or fiber ⁇ should be increased and the magnetically unfavorable ⁇ -fiber ( ⁇ 111 ⁇ BN) should be reduced.
  • This can be shown, for example, by the orientation distribution function (OVF) and the orientation density (ODF) along the fibers.
  • the differences in the strength of the texture due to the process procedures with and without intermediate thickness can be established by determining orientation distribution functions (OVF).
  • OVF orientation distribution functions
  • five samples per example are measured by means of X-ray diffraction (XRD). 30 ⁇ m are removed beforehand from each side of the sample by chemical surface treatment in order to rule out surface effects.
  • the ⁇ 110 ⁇ , ⁇ 200 ⁇ and ⁇ 211 ⁇ pole figures are subsequently determined for each of the five samples using Co-K ⁇ and the average of these measurements is calculated.
  • the OVF is then determined from these average pole figures by means of a program.
  • sections of the orientation densities f(g) of the fibers ( ⁇ , ⁇ , ⁇ , ⁇ ) can be depicted and the intensities I in particular orientations compared.
  • the texture difference caused by the process procedures with and without intermediate thickness can be established via the difference between the intensities of the orientation densities f(g) of the ⁇ -fiber, which has a positive effect on the magnetic properties, with the orientation ⁇ 110 ⁇ 001>, and the magnetically unfavorable ⁇ -skeletal line in the ⁇ -fiber with the orientation ⁇ 554 ⁇ 225>, corresponding to I ⁇ , ⁇ 554 ⁇ 225> ⁇ I ⁇ , ⁇ 110 ⁇ 001> , which according to the invention is ⁇ 3.
  • the present invention preferably provides the non-oriented electrical steel strip according to the invention which has a final thickness of from 0.24 to 0.36 mm.
  • final thickness means the thickness of the non-oriented electrical steel strip after the second cold rolling step.
  • the present invention preferably provides the non-oriented electrical steel strip according to the invention, where the polarization J2500/50 at 2500 A/m and 50 Hz and the magnetic loss P 1.5/50 at 1.5 T and 50 Hz satisfy the following relationships:
  • the magnetic losses P can, according to the invention, be determined by all methods known to a 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: Methods of measurement of the magnetic properties of electrical steel strip and sheet by means of an Epstein frame”.
  • appropriate electrical steel sheets are cut into longitudinal and transverse strips and measured as mixed sample in the Epstein frame.
  • the non-oriented electrical steel strip described here characterizes an anisotropy of the magnetic loss values at 1.5 T and 50 Hz in the longitudinal and transverse direction of less than 20%.
  • the present invention also provides for the use of a non-oriented electrical steel strip according to the invention in iron cores of rotating electric machines, in particular in electric motors and generators.
  • FIG. 1 shows the improvement according to the invention in the case of hot-rolled strip material which has not been bell heat treated from examples 1, 2, 5 and 6.
  • FIG. 2 shows the improvement according to the invention in the case of hot-rolled strip material which has been bell heat treated from examples 3, 4, 7, 8, 13, 14 and 15 to 18.
  • FIG. 3 shows the orientation densities of the ODF along the ⁇ -fibers in Euler space at ⁇ 1 at 90°, ⁇ 2 at 45° and ⁇ in the range from 0° to 90° for example 1.
  • FIG. 6 shows orientation densities of the ODFs along the ⁇ -fibers in Euler space at ⁇ 1 of from 0° to 90°, ⁇ 2 at 0° and ⁇ at 45° for example 2.
  • compositions 1, 2 and 3 as per table 1 are used.
  • Composition 1 as per table 1 is used in example 1.
  • Examples 5, 6, 7 and 8 according to the invention and comparative samples 1, 2, 3 and 4 were produced.
  • the slab obtained after melting of a composition 1 from table 1 was in each case hot rolled, optionally subjected to a hot-rolled strip bell heat treatment at 740° C. and cold rolled to an intermediate thickness of 0.70 mm.
  • the material was subsequently subjected to intermediate heat treatment at 1000° C., cold rolled to a final thickness of 0.34 mm and then subjected to final heat treatment in the range from 1000° C. to 1080° C.
  • the comparative sample 4 was hot rolled after melting, subjected to hot-rolled strip heat treatment, directly cold rolled to a final thickness of 0.34 mm and subjected to final heat treatment at 1000° C.
  • Comparative example 3 results from the standard process, i.e. single-stage cold rolling with hot-rolled strip bell heat treatment. For details, see table 2.
  • the characteristic magnetic values i.e. J100, J5000, J2500, P1.5/50 and P1.0/400, were in each case determined for samples with and without intermediate thickness after final heat treatment.
  • Examples 11, 12 and 13 according to the invention having the composition 2 as per table 1, example 14 having the composition 3 and comparative examples 9 and 10 having the composition 2 of table 1 were produced under the conditions shown in table 3.
  • Formula 1 (for hot-rolled strip material which has not been bell heat treated): J 2500/50 > ⁇ 0.045*P 15/50 2 +0.3*P 15/50 +1.085
  • orientation of the crystal coordinate system relative to the sample coordinate system can be depicted by the OVF by each point in a space spanned by the Euler angles ⁇ 1 , ⁇ 2 and ⁇ being assigned an orientation density f(g) or intensity I.
  • orientation distribution functions can be depicted with the aid of the intensity of fibers in sectional areas of this space.
  • the ⁇ -fiber and the ⁇ -fiber are examined.
  • the orientation densities f(g) of the ⁇ -fiber and ⁇ -fiber were plotted for the course of Euler angles of from 0 to 90°.
  • FIGS. 3 to 6 show the course of the OVF versus the angle ⁇ for the ⁇ -fiber and the angle ⁇ 1 for the ⁇ -fiber.
  • the specific positions ⁇ 554 ⁇ 225>, ⁇ 110 ⁇ 001> and more are drawn in.
  • the samples 1, 3 and 9 of the single-stage manufacture have the main intensity of their texture in the vicinity of the magnetically poor ⁇ -fiber or the ⁇ -skeletal line (see ⁇ 554 ⁇ 225> in the ⁇ -fiber).
  • the ⁇ -fiber at ⁇ 554 ⁇ 225> contributes to a worsened texture since the ideal ⁇ -fiber can be shifted by the manufacture by some degrees, which is referred to as ⁇ -skeletal line.
  • a skeletal line refers to a connecting line of points of greatest intensity through Euler space and intensity fluctuations along this can be interpreted as fluctuations within the manufacturing tolerance. For this reason, the maximum intensity I of the ⁇ -fiber shifts to the ⁇ -fiber at ⁇ 1 at 90°, ⁇ 2 at 45° and ⁇ at 60° and orientation ⁇ 554 ⁇ 225>.
  • the process according to the invention of two-stage manufacture reduces the orientation density of this disadvantageous ⁇ -fiber texture value at ⁇ 554 ⁇ 225> (see table 3 and FIGS. 3 to 6 ).
  • the ⁇ -fiber which does not contain any magnetically difficult magnetization reversal direction, is occupied more strongly in the case of the two-stage manufacture according to the invention than in the case of the single-stage manufacture.
  • the individual values are shown in table 4.
  • the process of the invention makes it possible to produce a non-oriented electrical steel strip which displays particularly low magnetic losses both at low frequencies and at high frequencies and displays good rollability so that it can be rolled particularly thin. It can therefore be used advantageously in rotating electric machines, in particular in electric motors and generators.

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US17/285,333 2018-10-15 2018-10-15 Method for producing an no electric strip of intermediate thickness Pending US20230193413A1 (en)

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