EP2612942B1 - Bande ou tôle électrique non orientée vers la corne, composant ainsi fabriqué et procédé de production d'une bande ou tôle électrique non orientée vers la corne - Google Patents

Bande ou tôle électrique non orientée vers la corne, composant ainsi fabriqué et procédé de production d'une bande ou tôle électrique non orientée vers la corne Download PDF

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Publication number
EP2612942B1
EP2612942B1 EP12150315.5A EP12150315A EP2612942B1 EP 2612942 B1 EP2612942 B1 EP 2612942B1 EP 12150315 A EP12150315 A EP 12150315A EP 2612942 B1 EP2612942 B1 EP 2612942B1
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Prior art keywords
annealing
strip
electrical steel
oriented electrical
sheet
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EP12150315.5A
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German (de)
English (en)
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EP2612942A1 (fr
Inventor
Dr. Dorothée Dorner
Dr. Olaf Fischer
Dr. Karl Telger
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel Europe AG
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Priority to PL12150315T priority Critical patent/PL2612942T3/pl
Application filed by ThyssenKrupp Steel Europe AG filed Critical ThyssenKrupp Steel Europe AG
Priority to EP12150315.5A priority patent/EP2612942B1/fr
Priority to CA2825852A priority patent/CA2825852C/fr
Priority to AU2012364385A priority patent/AU2012364385B2/en
Priority to RU2013144581/02A priority patent/RU2605730C2/ru
Priority to CN201280019922.6A priority patent/CN103687974B/zh
Priority to US14/118,720 priority patent/US9637805B2/en
Priority to BR112013020464-8A priority patent/BR112013020464B1/pt
Priority to KR1020137025479A priority patent/KR101587967B1/ko
Priority to JP2014523348A priority patent/JP5750196B2/ja
Priority to MX2013009017A priority patent/MX2013009017A/es
Priority to PCT/EP2012/075966 priority patent/WO2013102556A1/fr
Publication of EP2612942A1 publication Critical patent/EP2612942A1/fr
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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
    • 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
    • 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
    • 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
    • C21D8/1272—Final recrystallisation annealing
    • 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
    • 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
    • C22C38/004—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
    • 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
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/05—Grain orientation

Definitions

  • the invention relates to a non-grain oriented electrical steel strip or sheet for electrical applications, an electrical component made from such an electrical steel strip or sheet, and a method for producing an electrical steel strip or sheet.
  • 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 poured into slabs, which are then hot rolled into a hot strip, which optionally annealed, then pickled and then cold rolled to a cold-rolled strip of 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 object of the invention was to provide a NO electrical steel strip or sheet and a manufactured from such a sheet or strip component for electrical applications, the increased strength, in particular a higher yield strength, and at the same time has good magnetic properties, in particular a low loss of magnetization at high frequencies.
  • a method for producing such a NO electrical strip or sheet should be given.
  • the solution according to the invention of the above-mentioned object with respect to the component for electrical applications is that such a component is produced from an electrical steel sheet or strip according to the invention.
  • a non-grain-oriented electrical steel strip or sheet for electrotechnical applications obtained in accordance with the invention is thus made from a steel consisting of (in% by weight) 1.0-4.5% Si, in particular 2.4-3.4% Si, to 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, up to 0, 01% N, in particular up to 0.006% N, up to 0.012% S, in particular up to 0.006% S, 0.1 - 0.5% Ti, and 0.1 - 0.3% P and the remainder of iron and unavoidable Impurities is, wherein for the ratio% Ti /% P of Ti content% Ti to P content% P applies 1 . 0 ⁇ % Ti / % P ⁇ 2 . 0th
  • the invention uses FeTi phosphides (FeTiP) to increase the strength.
  • FeTiP FeTi phosphides
  • Form precipitates and increase the strength of NO electrical steel strip or sheet by particle hardening.
  • a particularly practical embodiment of the inventive alloy of an electrical strip or sheet is obtained when the contents of the steel of Si, C, N, S, Ti and P are each optionally (in wt .-%) to 2.4 - 3, 4% Si, up to 0.005% C, up to 0.006% N, up to 0.006% S, up to 0.5% Ti or up to 0.3% P.
  • up to 2.0% Al and up to 1.0% Mn can be present in the steel according to the invention.
  • the invention uses to increase the strength instead of the carbonitrides usually used for FeTi phosphides. In this way, on the one hand the magnetic aging can be avoided, which can occur as a result of high C and / or N contents.
  • the ratio of Ti content% Ti to P content% P satisfies the condition specified in claim 1, according to which the ratio of the titanium content to the phosphorus content of the electrical steel strip or sheet according to the invention is greater than or equal to 1.0 and at the same time less than or equal to 2.0.
  • the electrical steel sheet or strip assembled in accordance with the invention has a sufficient number and sufficient distribution of FeTiP particles, in addition to sufficiently high strength also to ensure good electromagnetic properties.
  • a harmful excess of phosphorus is avoided, which would lead to embrittlement in the electrical steel strip or sheet according to the invention.
  • an excessive excess of titanium is avoided by the ratio predetermined according to the invention. Such an excess of Ti could lead to the formation of titanium nitrides, which would adversely affect the magnetic properties of the electrical steel strip or sheet.
  • the invention is based on the recognition that a maximum of the present invention used effect of the simultaneous presence of Ti and P is achieved in a non-grain oriented electrical sheet or strip according to the invention, if its contents of Ti and P with the smallest possible deviations of the stoichiometric ratio of 1.55.
  • a particularly important embodiment of the invention provides that the ratio% Ti /% P of the Ti content% Ti to the P content% P applies 1 . 43 ⁇ % Ti / % P ⁇ 1 . 67th
  • the FeTiP particles made possible by the steel composition according to the invention regularly have a diameter which is much smaller than 0.1 ⁇ m. This takes into account the effect that although the strength of a material increases with the number of lattice defects, such as foreign atoms, dislocations, grain boundaries or particles of another phase, these lattice defects have a negative influence on the magnetic characteristics of a material.
  • the negative influence is, as known per se, the strongest when the particle size is in the range of the Bloch wall thickness (transition region between magnetic domains with different magnetization), d. H. is about 0.1 microns.
  • This negative influence occurs in an electrical steel sheet according to the invention at most in a highly minimized form.
  • FeTiP particles may also be present in the material according to the invention which are significantly larger than 0.1 ⁇ m. However, these influence the properties of a product according to the invention at most to a negligible extent.
  • Micro-alloying elements such as Nb, Zr or V, are no longer needed in conjunction with high levels of carbon or nitrogen. Higher contents of C and N have a negative impact on the magnetic properties of the correspondingly assembled non-grain oriented electrical steel strip or sheet because they entail undesirable magnetic aging of the materials during practical use. According to the invention, therefore, the increase in strength is achieved by particle hardening, namely by the presence of FeTiP precipitates, but not with the help of carbon and / or nitrogen whose presence would lead to aging effects.
  • electrical tapes or sheets composed according to the present invention regularly have remagnetization losses P 1.0 / 400 at a polarization of 1.0 Tesla and a frequency of 400 Hz at a thickness of the electrical steel or sheet of 0.5 mm of at most 65 W / kg and at a thickness of 0.35 mm at most 45 W / kg.
  • they regularly increase the yield strength of at least 60 MPa.
  • 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 obtained according to the invention.
  • 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 corresponding to the specification according to the invention (Si: 1.0-4.5%, Al: up to 2.0%, Mn: up to 1.0%, C: up to 0.01% , N: up to 0.01%, S: up to 0.012%, Ti: 0.1-0.5%, P: 0.1-0.3%, remainder iron and unavoidable impurities, data in% by weight.
  • % wherein for the ratio% Ti /% P of the Ti content% Ti to the P content% P is 1.0 ⁇ % Ti /% P ⁇ 2.0) are melted and cast to a starting material, in which it in conventional manufacturing can be a slab or thin slab.
  • a starting material in which it in conventional manufacturing can be a slab or thin slab.
  • 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 of 1000 - 1150 ° C and ends with a hot rolling end temperature of 700 - 920 ° C, in particular 780 - 850 ° C.
  • the resulting hot strip can then be cooled to a coiling temperature and coiled into a coil.
  • the coiler temperature is ideally chosen so that precipitation of the Fe-Ti phosphides is avoided in order 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 FeTiP 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 of between 390 and 550 MPa and remagnetization losses of P 1.0 / 400 which are less than 27 W / kg at a strip thickness of 0.35 mm and a strip thickness of 0, 5 mm less than 47 W / kg, can be particularly reliable achieved in accordance with a first variant of the method according to the invention that the cold strip in the course of the final annealing undergoes a continuous furnace in the two-stage Kurzzeitglühung in which the cold strip in the first annealing stage d.1) first annealed over an annealing period of 1 - 100 s at an annealing temperature of at least 900 ° C and at most 1150 ° C and then in a second annealing stage d.2) over an annealing period of 30 - 120 s at an annealing temperature of 500 - 850 ° C.
  • the already existing FeTiP precipitates are dissolved in the first annealing stage d.1) and a complete recrystallization of the microstructure is achieved.
  • the second annealing stage d.2) then the targeted excretion of FeTiP particles.
  • the long-term annealing optionally carried out in the hood furnace may be followed by the two-stage short-time annealing at which the cold strip at temperatures of 550-660 ° C over a Annealing time of 0.5 - 20 h is annealed.
  • the achievable by this additional Langzeitglühung increase in yield strength is regularly at least 50 MPa.
  • Non-grain oriented electrical sheets or tapes having yield strengths of 500-800 MPa and remagnetization losses P 1.0 / 400 of less than 45 W / kg for 0.35 mm thick electrical sheets or tapes can also be produced thereby according to a second variant of the inventive method in that the final annealing is carried out as a short-time annealing, in which the cold strip is annealed in the continuous furnace for an annealing period of 20 to 250 seconds at an annealing temperature of 750 to 900 ° C. Due to the lower annealing temperature in this case no complete recrystallization of the microstructure is achieved. However, the desired strength-increasing FeTiP precipitates form.
  • FeTiP precipitates are formed which are finer than the FeTiP precipitates present in the non-grain oriented electrical sheets or tapes of the invention produced in accordance with the first embodiment discussed above. It can be through the illustrated here third variant of the invention Method in comparison to the above-explained second variant to achieve improvements in Ummagnetleitersppe.
  • a short-time annealing in the continuous furnace can also be carried out, in which the respective cold strip is annealed at 750 ° C.-900 ° C. over an annealing period of 20 to 250 seconds.
  • This additional Kurzzeitglühung can improve the degree of recrystallization of the structure. Along with this, an improvement in the loss of magnetization is to be expected.
  • the cold strip in the course of the third variant of the inventive method between the long-term annealing and the Kurzzeitglühung optionally a deformation with a degree of deformation of at least 0.5 % and at most 12%.
  • a forming step which is usually carried out as an additional cold-rolling step, furthermore contributes to the improvement of the flatness of the non-grain-oriented electrical sheet or strip obtained at the end of this process variant according to the invention.
  • the effects achieved with the optionally additionally carried out cold deformation can be achieved particularly reliably if the degrees of deformation of the cold deformation amount to 1 to 8%.
  • the final annealing may be followed by a smoothing pass carried out in a conventional manner.
  • 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.
  • the slabs were brought to 1250 ° C temperature and with a hot rolling start temperature of 1020 ° C and a hot rolling end temperature of 840 ° C to hot-rolled into a 2 mm thick hot strip.
  • the respective hot strip has been cooled to a reel temperature T reel . Subsequently, a typical cooling in the coil has been simulated.
  • the samples produced from the steel according to the invention have somewhat of 3.9-4.8 W / kg for 0.5 mm thick sheets and less than 3.7 W / kg for 0.35 mm thick sheets higher Ummagnetleitersmanne P 1.5 than that from the Reference steel produced samples. Again, the reel temperature has no significant influence.
  • the magnetic reversal losses P 1.0 for the invention and the reference samples are very close to each other.
  • the samples with the higher temperature T low of 700 ° C show here in the case of 0.5 mm thick sheets with less than 39 W / kg at 400 Hz and less than 180 W / kg at 1 kHz lower Ummagnetleitersppe P 1.0 than the reference material. In the case of the 0.35 mm thick sheets, the same loss of magnetization is achieved as with the reference material.
  • the slabs were reheated to 1250 ° C and then hot rolled to hot strip with a hot strip thickness of 2.1 mm and 2.4 mm, respectively.
  • the hot rolling start temperature was in each case 1020 ° C.
  • the hot rolling end temperature was in each case 840 ° C.
  • the resulting hot strips were then reeled at a reel temperature of 620 ° C.
  • the hot strips thus obtained were cold rolled without prior hot strip annealing to 0.35 mm thick cold strip.
  • a two-stage Kurzzeitglühung has been completed in a continuous furnace.
  • annealing times t G1 are met and there also mentioned respective maximum annealing temperatures T max1 achieved while the second stage respectively in the annealing times t G2 also shown in Table 5 at the same there maximum annealing temperatures T max2 has been completed.
  • the mechanical and magnetic properties determined on the thus obtained final annealed NO-electric sheet samples in transverse direction Q and longitudinal direction L are also listed in Table 5.
  • a sample of the finally heat-treated samples according to the first variant has subsequently been subjected to additional long-term annealing in a hood furnace.
  • the annealing times t GH and maximum annealing temperatures T maxH are shown in Table 6.
  • the mechanical and magnetic properties determined on the additionally long-time annealed NO electric sheet in the transverse direction Q and in the longitudinal direction L are likewise recorded in Table 6. It can be seen that the supplementary long-term annealing achieved a significant increase in the yield strength R e and the tensile strength R m , whereas the magnetic properties did not deteriorate significantly.
  • samples of the cold strips have been subjected to long-term annealing at different temperatures T maxH in the hood furnace over an annealing time t GH .
  • the respective temperatures T maxH and the respective annealing time t GH are listed in Table 7.
  • Table 7 also shows the mechanical and magnetic properties determined on the long-time-annealed NO-electric sheet samples obtained in the transverse direction Q and in the longitudinal direction L.
  • samples of the cold strips have been subjected to single-stage short-time annealing at different temperatures T maxD in the continuous furnace over an annealing time t GD .
  • the respective temperatures T maxD and the respective annealing time t GD are listed in Table 8.
  • Table 8 also shows the mechanical and magnetic properties determined on the long-time-annealed NO electric-sheet samples obtained in the transverse direction Q and in the longitudinal direction L.
  • the invention accordingly relates to a non-grain-oriented electrical steel sheet or sheet comprising, in addition to iron and unavoidable impurities (in% by weight) Si: 1.0-4.5%, Al: up to 2.0%, Mn: up to 1.0%, C: up to 0.01%, N: up to 0.01%, S: up to 0.012%, Ti: 0.1-0.5%, P: 0.1-0 , 3%, wherein the ratio% Ti /% P of the Ti content% Ti to the P content% P is 1.0 ⁇ % Ti /% P ⁇ 2.0.
  • An inventive non-grain oriented electrical steel strip or sheet and made of such a sheet or strip components for electrical applications are characterized by increased Strengths and at the same time good magnetic properties.
  • the NO sheet or strip according to the invention can be produced by cold-rolling a hot strip consisting of a steel with the above-mentioned composition into a cold strip and subjecting this cold strip to a final annealing.
  • the invention provides various variants of this final annealing available. Table 1 variant Si al Mn C N S Ti P TiP 2, 99 0,004 0.58 0,006 0.0021 ⁇ 0.001 0.148 0,100 Ref 2.96 0,006 0, 64 0,006 0.0021 0.001 0.001 0,004 Balance iron and unavoidable impurities, data in% by weight stolen According to the invention? Hot strip annealing?

Claims (15)

  1. Feuillard ou tôle magnétique à grains non orientés pour des applications électrotechniques, fabriqué(e) à partir d'un acier qui, en plus de contenir du fer et des impuretés inévitables, se compose (% en poids) de
    Si : de 1,0 % à 4,5 %
    Al : jusqu'à 2,0 %,
    Mn : jusqu'à 1,0 %,
    C : jusqu'à 0,01 %,
    N : jusqu'à 0,01 %,
    S : jusqu'à 0,012 %,
    Ti : de 0,1 % à 0,5 %,
    P : de 0,1 % à 0,3 %,
    où, pour le rapport % Ti / % P de la teneur en Ti exprimée par % Ti, relativement à la teneur en P exprimée par % P, s'applique l'équation 1 , 0 ≤ % Ti / % P ≤ 2 , 0.
    Figure imgb0009
  2. Feuillard ou tôle magnétique à grains non orientés selon la revendication 1, caractérisé(e) en ce que pour le rapport % Ti / % P de la teneur en Ti exprimée par % Ti, relativement à la teneur en P exprimée par % P, s'applique l'équation 1 , 43 ≤ % Ti / % P ≤ 1 , 67.
    Figure imgb0010
  3. Feuillard ou tôle magnétique à grains non orientés selon l'une ou l'autre des revendications précédentes, caractérisé(e) en ce que sa teneur en Si est comprise entre 2,4 % en poids et 3,4 % en poids.
  4. Feuillard ou tôle magnétique à grains non orientés selon l'une quelconque des revendications précédentes, caractérisé(e) en ce que sa teneur en C est au maximum de 0,006 % en poids.
  5. Feuillard ou tôle magnétique à grains non orientés selon l'une quelconque des revendications précédentes, caractérisé(e) en ce que sa teneur en N est au maximum de 0,006 % en poids.
  6. Feuillard ou tôle magnétique à grains non orientés selon l'une quelconque des revendications précédentes, caractérisé(e) en ce que sa teneur en S est au maximum de 0,006 % en poids.
  7. Feuillard ou tôle magnétique à grains non orientés selon l'une quelconque des revendications précédentes, caractérisé(e) en ce que sa perte par inversion de magnétisation P1,0/400, dans le cas d'une polarisation de 1,0 tesla et d'une fréquence de 400 Hz, est au maximum de 65 W/kg dans le cas d'une épaisseur de 0,5 mm du feuillard ou de la tôle magnétique et au maximum de 45 W/kg dans le cas d'une épaisseur de 0,35 mm.
  8. Composant pour des applications électrotechniques, fabriqué dans un feuillard ou une tôle magnétique fourni(e) selon l'une quelconque des revendications 1 à 7.
  9. Procédé de production d'un feuillard ou d'une tôle magnétique à grains non orientés, au cours duquel sont exécutées les étapes de travail suivantes :
    a) fourniture d'un feuillard laminé à chaud qui est réalisé dans un acier qui, en plus de contenir du fer et des impuretés inévitables, se compose (% en poids) de
    Si : de 1,0 % à 4,5 %
    Al : jusqu'à 2,0 %,
    Mn : jusqu'à 1,0 %,
    C : jusqu'à 0,01 %,
    N : jusqu'à 0,01 %,
    S : jusqu'à 0,012 %,
    Ti : de 0,1 % à 0,5 %,
    P : de 0,1 % à 0,3 %,
    où, pour le rapport % Ti / % P de la teneur en Ti exprimée par % Ti, relativement à la teneur en P exprimée par % P, s'applique l'équation 1 , 0 ≤ % Ti / % P ≤ 2 , 0 ;
    Figure imgb0011
    b) laminage à froid du feuillard laminé à chaud pour former un feuillard laminé à froid, et
    c) recuit final du feuillard laminé à froid.
  10. Procédé selon la revendication 9, caractérisé en ce que le feuillard laminé à froid, lors du recuit final, est soumis à un recuit de courte durée réalisé en deux étapes dans le four à passage continu, recuit de courte durée pendant lequel le feuillard laminé à froid,
    d.1) dans une première étape de recuit, est d'abord recuit à une température de recuit au moins de 900°C et au maximum de 1150°C, sur une durée de recuit allant de 1 s à 100 s et, ensuite,
    d.2) dans une deuxième étape de recuit, est recuit à une température de recuit comprise entre 500°C et 850°C, sur une durée de recuit allant de 30 s à 120 s.
  11. Procédé selon la revendication 10, caractérisé en ce que le feuillard laminé à froid, après la deuxième étape du recuit de courte durée, est soumis dans un four à hotte, à une température de recuit comprise entre 550°C et 660°C, à un recuit de longue durée s'étendant sur une durée de recuit allant de 0,5 h à 20 h.
  12. Procédé selon la revendication 9, caractérisé en ce que le recuit final du feuillard laminé à froid est effectué comme un recuit de courte durée, au cours duquel le feuillard laminé à froid est recuit dans le four à passage continu, à une température de recuit comprise entre 750°C et 900°C, sur une durée allant de 20 s à 250 s.
  13. Procédé selon la revendication 9, caractérisé en ce que le recuit final est réalisé comme un recuit de longue durée, au cours duquel le feuillard laminé à froid est recuit dans le four à hotte, à une température de recuit comprise entre 600°C et 850°C, sur une durée de recuit allant de 0,5 h à 20 h.
  14. Procédé selon la revendication 13, caractérisé en ce que le recuit final comprend en outre un recuit de courte durée effectué après le recuit de longue durée, recuit de courte durée au cours duquel le feuillard laminé à froid est soumis, dans un four à passage continu, à une température de recuit comprise entre 750°C et 900°C, sur une durée de recuit allant de 20 s à 250 s.
  15. Procédé selon la revendication 14, caractérisé en ce que le feuillard laminé à froid est soumis, entre le recuit de longue durée et le recuit de courte durée, à une déformation ayant un degré de déformation au moins de 0,5 % et au maximum de 12 %.
EP12150315.5A 2012-01-05 2012-01-05 Bande ou tôle électrique non orientée vers la corne, composant ainsi fabriqué et procédé de production d'une bande ou tôle électrique non orientée vers la corne Active EP2612942B1 (fr)

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EP12150315.5A EP2612942B1 (fr) 2012-01-05 2012-01-05 Bande ou tôle électrique non orientée vers la corne, composant ainsi fabriqué et procédé de production d'une bande ou tôle électrique non orientée vers la corne
PL12150315T PL2612942T3 (pl) 2012-01-05 2012-01-05 Elektrotechniczna stalowa taśma lub blacha o ziarnie niezorientowanym, element wytwarzany z niej i sposób wytwarzania elektrotechnicznej stalowej taśmy lub blachy o ziarnie niezorientowanym
JP2014523348A JP5750196B2 (ja) 2012-01-05 2012-12-18 無方向性電磁鋼ストリップ又はシート、それから製造される部品及び無方向性電磁鋼ストリップ又はシートの製造方法
RU2013144581/02A RU2605730C2 (ru) 2012-01-05 2012-12-18 Полоса или лист электротехнической стали с неориентированной зернистой структурой, изготовленный из них конструктивный элемент и способ производства полосы или листа электротехнической стали с неориентированной зернистой структурой
CN201280019922.6A CN103687974B (zh) 2012-01-05 2012-12-18 非晶粒取向的磁性钢带或磁性钢板、由其所制成的部件和非晶粒取向的磁性钢带或磁性钢板的制造方法
US14/118,720 US9637805B2 (en) 2012-01-05 2012-12-18 Non-grain-oriented electrical steel strip or sheet, component manufactured from it and method for producing a non-grain-oriented electrical steel strip or sheet
CA2825852A CA2825852C (fr) 2012-01-05 2012-12-18 Bande ou tole magnetique a grains non orientes, composant fabrique en ladite tole ou bande, et procede de production d'une bande ou tole magnetique a grains non orientes
KR1020137025479A KR101587967B1 (ko) 2012-01-05 2012-12-18 무방향성 전기 강 스트립 또는 시트, 그로부터 제조된 부품, 및 무방향성 전기 강 스트립 또는 시트를 제조하는 방법
AU2012364385A AU2012364385B2 (en) 2012-01-05 2012-12-18 Non-grain-oriented electrical steel strip or sheet, component produced therefrom, and method for producing a non-grain-oriented electrical steel strip or sheet
MX2013009017A MX2013009017A (es) 2012-01-05 2012-12-18 Tira o hoja de acero electrico de grano no orientado, componente fabricado de ella y metodo para la produccion de una tira o hoja de acero electrico de grano no orientado.
PCT/EP2012/075966 WO2013102556A1 (fr) 2012-01-05 2012-12-18 Bande ou tôle magnétique à grains non orientés, composant fabriqué en ladite tôle ou bande, et procédé de production d'une bande ou tôle magnétique à grains non orientés
BR112013020464-8A BR112013020464B1 (pt) 2012-01-05 2012-12-18 Tira ou chapa de aço elétrico com grão não orientado para aplicações eletrotécnicas

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WO2018188766A1 (fr) * 2017-04-11 2018-10-18 Thyssenkrupp Steel Europe Ag Produit plat en acier laminé à froid, recuit sur base, et procédé de fabrication s'y rapportant
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DE102018201622A1 (de) 2018-02-02 2019-08-08 Thyssenkrupp Ag Nachglühfähiges, aber nicht nachglühpflichtiges Elektroband
CN108486453B (zh) * 2018-03-27 2020-03-31 东北大学 一种低铁损高磁感无取向硅钢板的制备方法
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US11041222B2 (en) 2017-05-15 2021-06-22 Thyssenkrupp Ag Non-oriented electrical steel strip for electric motors

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EP2612942A1 (fr) 2013-07-10
CN103687974A (zh) 2014-03-26
CA2825852C (fr) 2016-04-19
US9637805B2 (en) 2017-05-02
CN103687974B (zh) 2016-12-21
BR112013020464B1 (pt) 2019-06-11
BR112013020464A2 (pt) 2016-10-18
MX2013009017A (es) 2014-03-05
KR20130125828A (ko) 2013-11-19
RU2013144581A (ru) 2015-04-20
CA2825852A1 (fr) 2013-07-11
US20140083573A1 (en) 2014-03-27
PL2612942T3 (pl) 2015-03-31
AU2012364385B2 (en) 2015-08-06
JP2014529008A (ja) 2014-10-30
RU2605730C2 (ru) 2016-12-27
WO2013102556A1 (fr) 2013-07-11
AU2012364385A1 (en) 2013-08-22
KR101587967B1 (ko) 2016-01-22

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