EP2840157B1 - Bande ou tôle électrique à grains non orientés et procédé de production d'une bande ou tôle électrique à grains non orientés - Google Patents

Bande ou tôle électrique à grains non orientés et procédé de production d'une bande ou tôle électrique à grains non orientés Download PDF

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EP2840157B1
EP2840157B1 EP13180889.1A EP13180889A EP2840157B1 EP 2840157 B1 EP2840157 B1 EP 2840157B1 EP 13180889 A EP13180889 A EP 13180889A EP 2840157 B1 EP2840157 B1 EP 2840157B1
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Prior art keywords
strip
oriented electrical
sheet
grain
weight
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German (de)
English (en)
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EP2840157A1 (fr
Inventor
Dorothée Dr. Dorner
Olaf Dr.-Ing. Fischer
Karl Dr. Telger
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel Europe AG
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Priority to EP13180889.1A priority Critical patent/EP2840157B1/fr
Application filed by ThyssenKrupp Steel Europe AG filed Critical ThyssenKrupp Steel Europe AG
Priority to PCT/EP2014/065729 priority patent/WO2015024723A1/fr
Priority to BR112016003059-1A priority patent/BR112016003059B1/pt
Priority to CN201480046092.5A priority patent/CN105473751B/zh
Priority to US14/912,381 priority patent/US20160203897A1/en
Priority to JP2016535380A priority patent/JP6480446B2/ja
Priority to KR1020167007264A priority patent/KR102298564B1/ko
Publication of EP2840157A1 publication Critical patent/EP2840157A1/fr
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    • 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
    • H01F1/16—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 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
    • C21D8/02—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
    • C21D8/0236—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
    • C21D8/02—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
    • C21D8/0273—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
    • C21D8/1216—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
    • C21D8/1227—Warm 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
    • C21D8/1272—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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/02—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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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

Definitions

  • the invention relates to a method for producing an electrical strip or sheet as well as a non-grain-oriented electrical strip or sheet produced by use of this method for electrical applications.
  • a NO electric steel strip or sheet having a yield strength of at least 60 kg-f / mm 2 (about 589 MPa) and made of a steel containing, in addition to iron and unavoidable impurities (in% by weight) to to 0.04% C, 2.0 - less than 4.0% Si, up to 2.0% Al, up to 0.2% P and at least one element from the group "Mn, Ni", wherein the Sum of the contents of Mn and Ni is at least 0.3% and at most 10%.
  • the thus composed steel is according to the US 5,084,112 shed to slabs, which subsequently closed hot rolled into a hot strip, which is optionally annealed, then pickled and then cold rolled to a cold strip having a given final thickness. Finally, the cold strip obtained is subjected to a recrystallizing annealing, in which it is annealed at a temperature of at least 650 ° C, but less than 900 ° C annealing temperature.
  • the electrical steel produced by this process has a predominantly ferritic microstructure containing up to 50% martensite by volume and, in addition to iron and unavoidable impurity (in% by weight), contains up to 0.0400% C, 0.2-6.5 % Si, 0.05-10.0% Mn, up to 0.30% P, up to 0.020% S, up to 15% Al, up to 0.0400% N, and further as Ausscheidungstruckner one or two or more elements from the group "Ni, Mo, Ti, Nb, Co and W" in amounts of up to 10.0 wt .-%.
  • Zr, Cr, B, Cu, Zn, Mg and Sn may also be present as precipitating agents in the steel in amounts of up to 10% by weight each.
  • the precipitates formed in the steel from said elements should be in the form of an intermetallic compound having a number density of more than 20 / ⁇ m 3 and a diameter of at most 0.050 ⁇ m.
  • the composition of the steel is in each case chosen so that the precipitates of Fe, Zr and Si are regularly present in binary form.
  • Non-grain oriented electrical steel sheet is known to have low iron loss.
  • the Sb content should preferably be 0.001-0.05%, especially 0.001-0.005%, whereas in the case that no Sb is present, the Sn content is 0.002-0.1 %, in particular 0.002 to 0.01% should be.
  • the JP 2010-121150 A finally discloses a non-grain oriented electrical steel sheet which has excellent machinability in combination with to have excellent magnetic properties.
  • This non-oriented electrical steel sheet intended especially for a rotary machine has a sheet thickness of 0.15-0.50 mm and a steel composition containing (in mass) up to 0.02% C, 1.0-4.0% Si, O.
  • the object of the invention was to provide a method by which NO electrical steel strip or sheet for electrical applications can be produced which has increased strengths, in particular a higher yield strength, and at the same time good magnetic properties Properties, in particular a low loss of magnetization at high frequencies.
  • this object has been achieved according to the invention in that the production steps specified in claim 1 are run through in the production of a NO electrical strip or sheet.
  • the solution according to the invention of the above-mentioned object with respect to a non-grain-oriented electrical steel sheet or strip is that this is produced by using the method according to the invention.
  • An inventively produced non-oriented electrical steel strip or sheet for electrical applications is thus made of a steel consisting of (in wt .-%) 2.0 - 4.5% Si, 0.03 - 0.3% Zr, and optionally in addition up to 2.0% Al, in particular up to 1.5% Al, up to 1.0% Mn, up to 0.01% C, in particular up to 0.006%, particularly advantageously up to 0.005% C, to to 0.01% N, in particular up to 0.006% N, up to 0.01% S, in particular up to 0.006% S, up to 0.015% P, in particular up to 0.006% P and the remainder being iron and unavoidable impurities ,
  • ternary Fe-Si-Zr precipitates are present in the microstructure of the electrical strip or sheet. These increase the strength of the steel according to the invention by precipitation or particle hardening.
  • the respective Fe-Si-Zr precipitates are formed as finely as possible in terms of their spatial extent.
  • their average diameter is preferably well below 100 nm.
  • Such small Fe-Si-Zr precipitations increase the strength of NO electrical steel strip or sheet of the type according to the invention, without losing the magnetic properties in applications for engine construction and the like important high frequency bands to deteriorate significantly.
  • the Fe-Si-Zr precipitates used according to the invention for increasing the strength hinder the movement of the Bloch walls only slightly due to their small size and thus cause at most a slight increase in the Ummagnetmaschineswe P 1.0 and P 1.5 compared to conventional, less solid electrical tapes and sheets.
  • the Bloch wall is the transition region between magnetic domains with different magnetization.
  • a non-grain oriented electrical steel sheet according to the invention has Si and Zr in levels adjusted to the desired formation of the Fe-Si-Zr precipitates comes.
  • Si at least 2.0 wt .-% Si are required, the Fe-Si-Zr precipitates then adjust particularly reliable in the desired frequency and distribution, if the Si content is at least 1.6 wt .-%, in particular at least 2.4 wt .-%, is.
  • the Si content is limited to at most 4.5 wt .-%, optimally the Si content, the upper limit of 3.5 wt .-% , in particular 3.4 wt .-%, does not exceed.
  • Levels of at least 0.03 wt% are required to form the desired ternary Zr precipitates. For this effect to occur particularly reliably, at least 0.07% by weight Zr, in particular at least 0.08% by weight Zr, may be added to the steel according to the invention. At levels greater than 0.3 wt% Zr, no significant increases in the property improvements caused by the presence of sufficient levels of Zr can be observed. An optimum effect of Zr in an electrical steel strip or sheet according to the invention can be achieved if the Zr content is limited to at most 0.25% by weight.
  • the steel from which the electrical steel strip or sheet is made according to the invention may contain contents of further alloying elements which are added in a manner known per se for adjusting its properties.
  • elements suitable for this purpose are, in particular, Al and Mn in the contents indicated here.
  • the invention does not have to rely on carbides, nitrides or carbonitrides to increase the strength, the C and N contents of an electric sheet or strip according to the invention can be minimized. In this way, the risk of magnetic aging is prevented, which can occur as a result of high C or N contents.
  • the electrical tapes or sheets assembled according to the invention generally increase the yield strength by at least 20 MPa compared with conventionally assembled electrical tapes or sheets in which no measures to increase the strength have been taken. The strength increases with the fineness of the precipitates. Strength increases of 100 - 200 MPa are possible with further refined precipitations.
  • the inventive method is designed so that it enables the reliable production of a non-grain-oriented electrical tape or sheet according to the invention.
  • a hot strip composed in the manner explained above for the non-grain-oriented electrical sheet or strip according to the invention is provided, which is subsequently cold-rolled and subjected to a final annealing as a cold-rolled strip.
  • the final annealed cold-rolled strip obtained after the final annealing then represents the electrical strip or sheet assembled and produced according to the invention, the strength of which is significantly improved by the presence of Fe-Si-Zr precipitates in its microstructure compared to a conventional NO electrical sheet or strip Therefore, it is particularly suitable for the production of electrical components and assemblies that are exposed to high dynamic loads in practical use.
  • the manufacture of the hot strip provided according to the invention can be carried out conventionally as far as possible.
  • a molten steel having a composition according to the invention corresponding composition Si: 2.0 to 4.5 wt .-%, Zr: 0.03 to 0.3 wt .-%, Al: up to 2.0 wt. %, Mn: up to 1.0% by weight, C: up to 0.01% by weight, N: up to 0.01% by weight, S: up to 0.01% by weight , P: up to 0.015 wt .-%, balance iron and unavoidable impurities
  • a starting material which may be a slab or thin slab in conventional manufacturing. Since the precipitation formation processes according to the invention take place only after solidification, it is in principle also possible to cast the molten steel into a cast strip, which is then hot rolled into a hot strip.
  • the starting material thus produced can then be brought to a pre-material temperature of 1020-1300 ° C.
  • the starting material is, if necessary, reheated or kept at the respective target temperature by utilizing the casting heat.
  • the thus heated starting material can then be hot rolled to a hot strip having a thickness which is typically 1.5-4 mm, in particular 2-3 mm.
  • the hot rolling starts in a conventional manner at a hot rolling start temperature in the finishing scale of 1000 - 1150 ° C and ends with a hot rolling end temperature of 700 - 920 ° C, especially 780 - 850 ° C.
  • the resulting hot strip can then be cooled to a coiling temperature and coiled into a coil.
  • the reel temperature is ideally chosen so that a precipitation of strength-increasing particles is still avoided at this time to avoid problems during subsequent cold rolling.
  • the reel temperature for this purpose, for example, at most 700 ° C.
  • the hot strip can be subjected to a hot strip annealing.
  • the supplied hot strip is cold rolled to a cold strip having a thickness typically in the range of 0.15-1.1 mm, especially 0.2-0.65 mm.
  • the final annealing contributes significantly to the formation of the Fe-Si-Zr particles used in the present invention for increasing the strength.
  • By varying the annealing conditions of the final annealing it is possible to optimize the material properties optionally in favor of a higher strength or a lower loss of core loss.
  • Non-grain-oriented electrical sheets or tapes according to the invention having yield strengths in the range of 350-500 MPa and remagnetization losses P 1.0 / 400 which are less than 35 W / kg at a strip thickness of 0.3 mm and a strip thickness of 0, 5 mm less than 45 W / kg, can be particularly reliable achieved by the inventively assembled cold strip is subjected in the course of the final annealing of a completed in the course of two-stage annealing.
  • the cold strip is annealed at an annealing temperature of 900 - 1150 ° C for 1 - 300 s. Subsequently, the cold strip is held in a second annealing stage at a temperature of 600 - 800 ° C for 50 - 120 s. Then the cold strip is cooled to a temperature below 100 ° C.
  • the possibly existing Fe-Si-Zr precipitates are dissolved in the first annealing stage and complete recrystallization of the microstructure is achieved. In the further annealing stages, the targeted precipitation of the Fe-Si-Zr particles then takes place.
  • the obtained, non-grain oriented electrical steel strip or sheet material may be finally subjected to a conventional flash annealing.
  • this flash annealing can still be performed in the coil of the manufacturer of NO-electric strip or sheet according to the invention, or it can first be divided from the produced in the inventive manner electrical strip or sheet, the blanks processed at the final processor, then the Be subjected to flash annealing.
  • Fig. 1 shows a diagram in which the target temperature profile during the final annealing of the electrical tapes and sheets produced in the manner explained below is shown.
  • the blocks were brought to 1250 ° C temperature and hot rolled with a hot rolling start temperature of 1020 ° C and a hot rolling end temperature of 840 ° C to a 2 mm thick hot strip.
  • the respective hot strip has been cooled to a reel temperature T HasPel of 620 ° C. Subsequently, a typical cooling in the coil has been simulated.
  • Some samples of the hot-rolled strip Zr1, Zr2 according to the invention and samples of the reference steels Ref1, Ref2 were then subjected to a hot strip annealing at a temperature of 740 ° C. for a period of 2 hours and then each to cold strips with a final thickness of 0, 5 mm or 0.3 mm cold rolled.
  • a final annealing was carried out in which the respective cold strip sample was first heated at a heating rate of 10 K / s over a period of 105 seconds from room temperature to an annealing temperature of 1090 ° C. Thereafter, the samples were held at the annealing temperature for a period of 15 seconds and then cooled at a cooling rate of 20 K / sec to an intermediate temperature of 700 ° C. At this intermediate temperature, the samples were held for over 60 seconds.
  • the mechanical and magnetic properties are upper yield strength R eH , lower yield strength R eL , tensile strength R m , the ratio Re / Rm of the mean yield strength Re to the tensile strength Rm, the uniform elongation A g , each measured at a frequency of 50 Hz
  • Correction loss P 1.0 loss of magnetization loss at a polarization of 1.0 T
  • P 1.5 loss of magnetization loss at a polarization of 1.5 T
  • each measured at 50 Hz each polarization J 2500 polarization at a magnetic field strength of 2500 A / m
  • J5000 polarization at a magnetic field strength of 5000 A / m
  • Table 3 the same information is given for 0.5 mm thick samples, which consist of the steels Zr1 or Zr2 according to the invention and of the reference steels Ref1 or Ref2 and have not been subjected to hot strip annealing.
  • Table 4 gives the corresponding values for 0.3 mm thick samples consisting of the Zr2 steel according to the invention or the reference steel Ref2 and subjected to a hot strip annealing
  • Table 5 the corresponding values for 0.3 mm thick specimens are given consisting of the steel according to the invention Zr2 or the reference steel Ref2 and have not undergone hot strip annealing.
  • the samples produced from the steels according to the invention have somewhat higher core losses than the samples produced from the reference steels.
  • the remagnetization losses of the samples according to the invention and of the reference samples hardly differ.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Electromagnetism (AREA)
  • Manufacturing & Machinery (AREA)
  • Dispersion Chemistry (AREA)
  • Power Engineering (AREA)
  • Soft Magnetic Materials (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
  • Iron Core Of Rotating Electric Machines (AREA)
  • Manufacture Of Motors, Generators (AREA)

Claims (10)

  1. Procédé pour générer une bande ou une tôle magnétique sans grains orientés, qui possède dans sa structure des précipitations de Fe-Zr-Si ternaires, le procédé comprenant les étapes de travail suivantes :
    a) mise à disposition d'un feuillard laminé à chaud, lequel se compose d'un acier qui, outre du fer et des impuretés inévitables, contient (en % massiques)
    Si: 2.0 - 4.5%,
    Zr: 0.03 - 0.3%,
    Al: jusqu'à 2.0%,
    Mn: jusqu'à 1.0%,
    C: jusqu'à 0.01%,
    N: jusqu'à 0.01%,
    S: jusqu'à 0.01%,
    P: jusqu'à 0.015%;
    b) laminage à froid du feuillard laminé à chaud en un feuillard laminé à froid et
    c) recuit final du feuillard laminé à froid,
    - le recuit final du feuillard laminé à froid étant réalisé en deux phases,
    - le feuillard laminé à froid étant maintenu, dans la première phase du recuit final, à une température de recuit de 900 à 1100 °C pendant 1 à 300 s et, dans la deuxième phase du recuit final, à une température de recuit de 600 à 800 °C pendant 50 à 120 s et
    - le feuillard laminé à froid étant refroidi, après la deuxième phase du recuit final, à une température inférieure à 100 °C.
  2. Bande ou tôle magnétique sans grains orientés pour applications électrotechniques, des précipitations de Fe-Zr-Si ternaires étant présentes dans la structure de la bande ou tôle magnétique à l'état laminé à froid et après recuit final, caractérisée en ce qu'elle est fabriquée en appliquant le procédé selon la revendication 1.
  3. Bande ou tôle magnétique sans grains orientés selon la revendication 2, caractérisée en ce que sa teneur en Si est au minimum égale à 2,5 % massiques.
  4. Bande ou tôle magnétique sans grains orientés selon l'une des revendications 2 ou 3, caractérisée en ce que sa teneur en Si est au maximum égale à 3,5 % massiques.
  5. Bande ou tôle magnétique sans grains orientés selon l'une des revendications 2 à 4, caractérisée en ce que sa teneur en Zr est au minimum égale à 0,08 % massique.
  6. Bande ou tôle magnétique sans grains orientés selon l'une des revendications 2 à 5, caractérisée en ce que sa teneur en Zr est au maximum égale à 0,25 % massique.
  7. Bande ou tôle magnétique sans grains orientés selon l'une des revendications 2 à 6, caractérisée en ce que sa teneur en C est au maximum égale à 0,006 % massique.
  8. Bande ou tôle magnétique sans grains orientés selon l'une des revendications 2 à 7, caractérisée en ce que sa teneur en N est au maximum égale à 0,006 % massique.
  9. Bande ou tôle magnétique sans grains orientés selon l'une des revendications 2 à 8, caractérisée en ce que sa teneur en S est au maximum égale à 0,006 % massique.
  10. Bande ou tôle magnétique sans grains orientés selon l'une des revendications 2 à 9, caractérisée en ce que sa perte par inversion magnétique P1,0/400 à une polarisation de 1,0 Tesla et une fréquence de 400 Hz est au maximum de 65 W/kg pour une épaisseur de la bande ou de la tôle magnétique de 0,5 mm et au maximum de 45 W/kg pour une épaisseur de 0,3 mm.
EP13180889.1A 2013-08-19 2013-08-19 Bande ou tôle électrique à grains non orientés et procédé de production d'une bande ou tôle électrique à grains non orientés Active EP2840157B1 (fr)

Priority Applications (7)

Application Number Priority Date Filing Date Title
EP13180889.1A EP2840157B1 (fr) 2013-08-19 2013-08-19 Bande ou tôle électrique à grains non orientés et procédé de production d'une bande ou tôle électrique à grains non orientés
BR112016003059-1A BR112016003059B1 (pt) 2013-08-19 2014-07-22 Tira magnética ou chapa magnética de grãos não orientados, componente produzido a partir da mesma e método para a produção de uma tira magnética ou chapa magnética de grãos não orientados
CN201480046092.5A CN105473751B (zh) 2013-08-19 2014-07-22 非晶粒取向的电工钢带或电工钢板、由其制成的部件及用于制造非晶粒取向的电工钢带或电工钢板的方法
US14/912,381 US20160203897A1 (en) 2013-08-19 2014-07-22 Non-grain-oriented electrical steel strip or electrical steel sheet, component produced therefrom, and methods for producing same
PCT/EP2014/065729 WO2015024723A1 (fr) 2013-08-19 2014-07-22 Bande d'acier ou tôle magnétique non à grains orientés, élément obtenu à partir de celle-ci et procédé permettant de produire une bande d'acier ou une tôle magnétique non à grains orientés
JP2016535380A JP6480446B2 (ja) 2013-08-19 2014-07-22 無方向性の電磁鋼片または電磁鋼板、およびこれから製造された部品、並びに無方向性の電磁鋼片または電磁鋼板の製造方法
KR1020167007264A KR102298564B1 (ko) 2013-08-19 2014-07-22 무방향성 전기 강철 스트립 또는 전기 강판, 이로부터 제조되는 부품, 및 무방향성 전기 강철 스트립 또는 전기 강판을 제조하기 위한 방법

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP13180889.1A EP2840157B1 (fr) 2013-08-19 2013-08-19 Bande ou tôle électrique à grains non orientés et procédé de production d'une bande ou tôle électrique à grains non orientés

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KR (1) KR102298564B1 (fr)
CN (1) CN105473751B (fr)
BR (1) BR112016003059B1 (fr)
WO (1) WO2015024723A1 (fr)

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DE102017208146B4 (de) 2017-05-15 2019-06-19 Thyssenkrupp Ag NO-Elektroband für E-Motoren
DE102018201622A1 (de) 2018-02-02 2019-08-08 Thyssenkrupp Ag Nachglühfähiges, aber nicht nachglühpflichtiges Elektroband
DE102018201618A1 (de) * 2018-02-02 2019-08-08 Thyssenkrupp Ag Nachglühfähiges, aber nicht nachglühpflichtiges Elektroband
WO2020094230A1 (fr) 2018-11-08 2020-05-14 Thyssenkrupp Steel Europe Ag Bande ou tôle électrique pour applications de moteur électrique haute fréquence présentant une polarisation améliorée et de faibles pertes par inversion magnétique
CN109453833B (zh) * 2018-12-10 2023-12-22 李赫川 一种生物安全中生命维持系统用装置
DE102019113291A1 (de) * 2019-05-20 2020-11-26 Thyssenkrupp Steel Europe Ag Blech für die Herstellung einer elektromagnetischen Komponente, insbesondere eines Statorpakets oder eines Rotorpakets, sowie Verfahren zur Herstellung einer elektromagnetischen Komponente
JP7364143B2 (ja) 2021-04-01 2023-10-18 大成建設株式会社 チャタテムシの防除方法、チャタテムシの防除空調システム、チャタテムシフリー施設

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GB2057500B (en) * 1979-09-07 1983-05-18 British Steel Corp Electro magnetic steels
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JP4833523B2 (ja) 2004-02-17 2011-12-07 新日本製鐵株式会社 電磁鋼板とその製造方法
JP4389691B2 (ja) * 2004-06-22 2009-12-24 住友金属工業株式会社 回転子用無方向性電磁鋼板およびその製造方法
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JP6480446B2 (ja) 2019-03-13
EP2840157A1 (fr) 2015-02-25
KR102298564B1 (ko) 2021-09-07
JP2016535168A (ja) 2016-11-10
CN105473751A (zh) 2016-04-06
CN105473751B (zh) 2018-01-12
BR112016003059B1 (pt) 2020-03-10
WO2015024723A1 (fr) 2015-02-26
US20160203897A1 (en) 2016-07-14
KR20160044569A (ko) 2016-04-25

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