WO2019096735A1 - Feuillard magnétique à grains orientés et procédé de fabrication d'un tel feuillard magnétique - Google Patents

Feuillard magnétique à grains orientés et procédé de fabrication d'un tel feuillard magnétique Download PDF

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Publication number
WO2019096735A1
WO2019096735A1 PCT/EP2018/080926 EP2018080926W WO2019096735A1 WO 2019096735 A1 WO2019096735 A1 WO 2019096735A1 EP 2018080926 W EP2018080926 W EP 2018080926W WO 2019096735 A1 WO2019096735 A1 WO 2019096735A1
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Prior art keywords
strip
ppm
cold
melt
annealing
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PCT/EP2018/080926
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German (de)
English (en)
Inventor
Christian Hecht
Carsten Schepers
Andreas Allwardt
Ludger Lahn
Heiner Schrapers
Original Assignee
Thyssenkrupp Electrical Steel Gmbh
Thyssenkrupp Ag
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Application filed by Thyssenkrupp Electrical Steel Gmbh, Thyssenkrupp Ag filed Critical Thyssenkrupp Electrical Steel Gmbh
Publication of WO2019096735A1 publication Critical patent/WO2019096735A1/fr

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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
    • 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
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • C21D9/561—Continuous furnaces for strip or wire with a controlled atmosphere or vacuum
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • C21D1/76—Adjusting the composition of the atmosphere
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1255—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest with diffusion of elements, e.g. decarburising, nitriding
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
    • C21D8/1283—Application of a separating or insulating coating
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
    • C21D8/1288—Application of a tension-inducing coating
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • H01F1/18—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 with insulating coating
    • 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
    • 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
    • H01F1/14783—Fe-Si based alloys in the form of sheets with insulating coating

Definitions

  • Grain-oriented electrical steel strip and method for producing such
  • the present invention relates to a grain-oriented electrical steel, wherein during its production, a high-temperature annealing in a
  • Temperature range of 700 to 900 ° C and the electrical steel during this high temperature annealing has a certain nitrogen content N, a process for its preparation and the use of such an electrical tape.
  • EP 1 025 268 B1 discloses a method for the production of grain-oriented electrical steel sheet, which after a hot rolling step and a
  • WO 2017/037019 A1 likewise discloses a method for the production of grain-oriented electrical steel strip.
  • This method comprises an annealing step after the cold rolling of the electrical strip, in which an oxide layer is formed on the surface. This oxide layer is determined by means of FTIR spectroscopy examined. From the FTIR investigation it is then determined how the
  • EP 1752548 A1 and EP 1752549 A1 disclose processes for the production of grain-oriented electrical steel. These methods also each comprise an annealing step in which the cold-rolled electrical steel is annealed recrystallizing and decarburizing, and which preferably takes place in an ammonia atmosphere.
  • the control of the nitridic phase during the annealing is important because it already at temperatures below the secondary crystallization temperature with the
  • Annealing atmosphere can interact. Too low a set nitridic phase manifests itself in too low an inhibition effect and, consequently, in higher core losses, while an over-adjusted nitridic phase can both shift the secondary crystallization temperature above the inhibitor dissolution temperature and produce an inhomogeneous forsterite layer, resulting in insufficient
  • the object of the present invention is therefore to a
  • Adhesive strength of Forsterit layer has on the surface, in particular, the interlocking of the glass layer is to be improved with the base material. Furthermore, it is an object of the present invention to provide a method for To provide a corresponding grain-oriented electrical tape.
  • step (G) annealing the cold strip from step (F) at a temperature of 700 to 900
  • step (K) optional final annealing of the cold strip wherein in step (I) the electrical steel has a nitrogen content N according to the following formula (1): in which
  • electrical steel is understood to mean an electrical steel produced by rolling suitably composed steel and blanks divided therefrom and intended for the production of parts for electrotechnical applications.
  • Grain-oriented electrical tapes of the type in question are particularly suitable for applications in which a particularly low loss of magnetization is in the foreground and high demands are placed on the permeability or polarization. Such requirements exist in particular for parts for
  • the method according to the invention may comprise, in addition to the further steps explicitly described herein, which are carried out in the conventional production of electrical tapes in order to achieve optimized magnetic properties or properties which are important for practical use. These include, for example, reheating the precursor obtained after the casting of the steel, descaling the hot strip before cold rolling or, in the case of multi-stage cold rolling, respectively performed between the cold rolling stages in a conventional manner
  • Step (A) of the process according to the invention comprises the melting of a molten steel containing (in each case in% by weight)
  • step (A) of the process according to the invention preference is given to
  • Melted molten steel containing (in wt .-%) 2 to 4 Si, 0.01 to 0.1 C, 0.01 to 0.065 Al and 0.002 to 0.02 N, and in each case optionally 0.005 to 0.5 Cu, 0.005 to 0.060 S and also optionally each 0 to 0.3 Cr, Mn, Ni, Mo, P, As, Sn, Sb, Se, Te, B or Bi, the remainder contains iron and unavoidable impurities.
  • Step (A) of the process according to the invention can be carried out by all methods known to the person skilled in the art.
  • a molten steel of known composition is preferably melted.
  • This melt is then treated by secondary metallurgy.
  • This treatment is first preferably carried out in a vacuum plant in order to adjust the chemical composition of the steel in the required narrow analysis margins and preferably to achieve low hydrogen contents of at most 10 ppm in order to reduce the risk of To minimize the occurrence of strand breakthroughs when casting the molten steel to a minimum.
  • step (A) the use of a ladle furnace for slag conditioning would also be possible, followed by treatment in a vacuum system for adjusting the chemical composition of the molten steel within narrow analytical limits.
  • this combination is associated with the disadvantage that in the case of casting delays the
  • step (A) it is also possible in step (A) to use only the ladle furnace.
  • this has the disadvantage that the analysis accuracy is not as good as in the treatment in a vacuum system and also high
  • Hydrogen contents in the casting melt can occur with the risk of strand breakthroughs.
  • step (A) it is further preferred in step (A) to use only the vacuum system.
  • the immersion spouts clog in the sequence and thus the sequence must be canceled.
  • step (B) of the process according to the invention the molten steel produced in step (A) is then cast into a starting material.
  • This starting material may according to the invention be for example a slab, a thin slab or a cast strip.
  • a strand is first produced from the melt by casting.
  • a strand is preferably poured for this purpose, which has a thickness of, for example, 25 mm to 150 mm.
  • the aim is to avoid the formation of nitridic precipitates prior to hot rolling and during hot rolling as much as possible in order to make extensive use of the possibility of a controlled production of such precipitates during the cooling of the hot strip.
  • LCR Liquid Core Reduction
  • SR Soft Reduction
  • Thickness reduction of a cast strand can be used alone or in combination.
  • the strand thickness is reduced at the core liquid inside the strand just below the mold.
  • LCR is used in the prior art in thin slab continuous casters primarily to achieve lower hot strip thicknesses, especially for higher strength steels.
  • LCR can reduce the reduction in the number of passes or the rolling forces in the rolling mills of the hot strip mill with the result that the work roll wear of the rolling mills and the scale porosity of the rolling mills
  • Hot bands can be reduced and the tape can be improved.
  • the thickness reduction achieved by LCR according to the invention is preferably in the range of 5 mm to 30 mm.
  • Under SR is meant the targeted reduction in thickness of the strand in the swamp tip near Enderstarrung.
  • the SR aims to reduce mitigation and core porosity.
  • the achievable by the SR reduction, in particular the silicon Mitsenigerung in the subsequently hot-rolled precursors allows a homogenization of the chemical
  • SR achieved thickness reduction, for example 0.5 to 5 mm.
  • thin slabs are preferably produced in step (B) of the process according to the invention.
  • the usually emerging from the casting mold strand is bent at lower points and guided in a horizontal direction.
  • the strand cast from the melt at a temperature of 700 to 1000 ° C, preferably 850 to 950 ° C, bent and directed, cracks can be avoided on the surface of the separated from the strand thin slabs which may otherwise be due, in particular, to edge cracks in the strand.
  • the steel used according to the invention has a good ductility at the strand surface or in the edge region, so that it can follow well the deformations occurring during bending and straightening. Of the thus cast strand thin slabs are divided in a conventional manner.
  • Step (C) of the process according to the invention comprises the hot rolling of the starting material from step (B), in particular the thin slabs produced a hot strip.
  • the starting material obtained in step (B) the starting material obtained in step (B),
  • the starting material in particular a thin slab, preferably heated in an oven to the appropriate hot rolling start temperature and then fed to the hot rolling.
  • the temperature at which the starting material, in particular a thin slab, enter the furnace is preferably above 650 ° C.
  • the residence time in the oven should be less than 60 minutes in order to avoid adhesive scale.
  • the hot rolling is preferably carried out in step (C) following the first forming pass in the two-phase region (a / g). Also, this measure has the goal of reducing the formation of nitridic precipitates in the course of hot rolling as far as possible in order to control these excretions via the cooling conditions on the outlet roller table behind the last
  • the AIN is kept in solution at these temperatures.
  • Another positive aspect of hot rolling in the two-phase mixed area is the grain refining effect.
  • End product affects. Furthermore, the avoidance of nitridic precipitations during hot rolling is further supported, for example, in that a degree of deformation of at least 40% is achieved in the first forming pass, in order to have only relatively small stitch reductions in the last stands for achieving the desired end strip thickness. In this respect, therefore, preferred is the scored over the first two Umformstiche
  • the reduction in stitching in the last stand should preferably be limited to a maximum of 30%, more preferably less than 20%, and it is also favorable for an optimum warm rolling result in view of the desired properties if the reduction in the penultimate stand of the finishing train is less than 25 % is.
  • Hot strip precipitations which would adversely affect the magnetic properties of the final product, benefit from early cooling of the hot strip behind the last mill stand of the finishing train. According to a practical embodiment of the invention, it is therefore preferable to start with the water cooling within a maximum of five seconds after leaving the last mill stand.
  • the aim is to have the shortest possible break times, for example, of one second and less.
  • the cooling of the hot strip can be known to the expert
  • Step (D) of the process of the invention comprises coiling the hot strip obtained in step (C) into a coil.
  • the reel temperature should preferably be in the temperature range of 500 to 780 ° C. Overlying temperatures would on the one hand lead to undesirably coarse precipitates and on the other hand the Beizbarkeit
  • a so-called short-distance reel is preferably used, which is arranged directly after the compact cooling zone.
  • inventive method in the production of the hot strip preferably carried out so that the hot strip obtained sulfide and / or nitridic precipitates having an average particle diameter less than 150 nm and an average density of at least 0.05 microns -2 is achieved.
  • Such a hot strip has optimal conditions for the effective control of grain growth during the subsequent process steps.
  • the thickness of the hot strip obtained according to the invention is preferably 1.5 to 3.5 mm, more preferably 2 to 2.7 mm.
  • the hot strip thus produced can optionally be annealed after reeling or before cold rolling.
  • step (F) the hot strip is rolled in one or more cold rolling steps to a cold strip.
  • step (F) the hot strip is rolled in one or more cold rolling steps to a cold strip.
  • multi-stage cold rolling between the cold rolling steps
  • the thickness of the cold strip obtained according to the invention is preferably 0.10 to 0.35 mm, more preferably 0.15 to 0.23 mm.
  • Step (G) of the process of the invention comprises annealing the cold strip at a temperature of 700 to 900 ° C, preferably 800 to 900 ° C.
  • Step (G) of the process according to the invention can in principle be carried out in all devices known to the person skilled in the art.
  • step (G) is carried out such that a dew point DP corresponds to the following equation (2) is present, and thus the nitrogen concentration in the material after step (G) is adjusted so that the following equation (1) is satisfied, where
  • N mean nitrogen content in the material after process step G in ppm.
  • the annealing in step (G) is preferably carried out in an atmosphere in which the dew point DP indicated in ° C corresponds to the equation (2) mentioned above.
  • Al si means the content of aluminum in the melt, which has been used in step (A) of the method according to the invention.
  • the unit of Al si is ppm.
  • values for Al si are preferably 100 to 650 ppm, particularly preferably 150 to 550 ppm, very particularly preferably 200 to 400 ppm.
  • N (melt) means the nitrogen content in the melt which has been used in step (A) of the process according to the invention.
  • the unit of N (melt) is ppm. Values for N (melt) according to the invention are preferably from 20 to 200 ppm, more preferably from 40 to 150 ppm, most preferably from 60 to 120 ppm.
  • the present invention preferably relates to the process according to the invention, wherein step (G) takes place at a dew point DP of from 20 to 90 ° C., more preferably from 30 to 70 ° C.
  • the nitrogen concentration N in the material results after step (G) according to equation (1).
  • N means the nitrogen content in the material after process step G in ppm.
  • the unit of N is ppm.
  • the nitrogen content N is preferably from 70 to 180 ppm, more preferably from 90 to 160 ppm.
  • step (G) of the process according to the invention is preferably a
  • step (G) of the process according to the invention is preferably carried out under certain conditions with regard to the dew point of the furnace atmosphere and the nitrogen concentration in the material after step (G), it is possible according to the invention to provide a grain-oriented electrical steel which is characterized by particularly low remagnetization losses and a particularly good Liability of the forsterite layer (magnesium silicate layer), which is formed in step (I) of the method according to the invention is characterized.
  • an annealing separator layer may be applied to at least one surface of the cold strip of step (G), preferably such an annealing separator layer is applied to both surfaces of the cold strip of step (G).
  • the annealing separator is typically MgO.
  • Annealing separator prevents the turns of a coil wound from the cold strip from welding together during subsequent high-temperature annealing.
  • Step (I) of the method according to the invention comprises
  • step (I) the electrical steel has a nitrogen content N according to the following formula (1): in which
  • Step (! Of the method according to the invention is under certain
  • Step (I) of the process according to the invention is preferably carried out at a temperature of 700 to 900 ° C.
  • Step (I) of the process according to the invention is typically carried out in a hood furnace under protective gas.
  • selective texture growth in the cold strip results in a structural texture which contributes significantly to the magnetic properties.
  • a forsterite layer is formed on the strip surfaces, often referred to in technical literature as "glass film.”
  • the steel material is cleaned by diffusion processes occurring during the high-temperature annealing.
  • step (I) according to the invention a grain-oriented electrical steel is obtained in which the toothing of the glass film with the
  • Base material is surprisingly improved.
  • This improved adhesive strength can be determined, for example, according to the method disclosed in EP 2 022 874 A1 by bending over conical mandrels with different diameters. The use of a conical mandrel allows all bending radii to be measured in one step.
  • the grain-oriented electrical strip according to the invention preferably exhibits a bending radius of less than 7.5 mm, preferably less than 5 mm.
  • the optional step (J) of the method according to the invention comprises applying an insulating layer to the surface of the cold strip having the forsterite layer. Suitable materials which can act as an insulating layer are, for example, phosphates, silicates or mixtures thereof. Corresponding processes are known per se to the person skilled in the art. Characterized in that in the high-temperature treatment in step (I) a certain
  • inventive method to apply in a single pass a thicker and more uniform insulation layer therefore preferably relates to the method according to the invention, wherein in step (J) an insulating layer is applied in a single pass.
  • step (J) of the method according to the invention can be thermally directed.
  • Corresponding methods for this purpose are likewise known to the person skilled in the art.
  • the optional step (K) of the process according to the invention comprises a final annealing of the cold strip according to the invention.
  • stress relief annealing the cold strip is stress relieved.
  • This final annealing can be carried out before or after the assembly of the steel flat product produced in the manner described above into the blanks required for further processing.
  • Final annealing which is carried out after the blanks have been cut, may be supplemented by the additional costs incurred during the division process
  • the grain-oriented electrical strip produced according to the invention is characterized by the fact that it has low core losses and, due to a high degree of toothing of the forsterite layer with the surface of the electrical strip, good adhesion of the forsterite layer.
  • the grain-oriented electrical steel produced according to the invention shows a bending radius smaller than 7.5 mm, preferably smaller than 5 mm.
  • the present invention therefore also relates to a grain-oriented electrical steel produced by the
  • the present invention also relates to a grain oriented electrical steel, wherein a high temperature annealing step is carried out during its production in which the electrical steel has a nitrogen content N according to the following formula (1): in which
  • the grain-oriented electrical strip according to the invention is subjected to high-temperature annealing during its production. At this
  • the grain-oriented electrical strip according to the invention has a glass film (magnesium silicate layer), which is connected to the base material by a particularly high toothing and therefore the adhesive strength of the glass film is markedly increased.
  • the invention shows produced komoriented electrical steel a bending radius of less than 7.5 mm, preferably less than 5 mm.
  • the electrical strip according to the invention is preferably obtained by the method according to the invention.
  • the grain-oriented electrical strip according to the present invention preferably has a magnesium silicate layer on at least one surface, wherein in a DRIFT spectrum of the magnesium silicate layer at least one peak in the range 960 to 975 cm -1 (A) and at least one peak in the range of 976 to 990 cm -1 , wherein the peak height of the at least one peak in the region (A) is higher than the peak height of the at least one peak in the region (B).
  • DRIFT Diffuse Reflection Fourier Transform Infrared Spectroscopy
  • an IR light beam is directed onto the sample surface by means of concave mirrors and the reflected light is also detected by means of concave mirrors, see, for example, Beasley et al., "Comparison of
  • the electrical strip according to the invention is characterized in that it has a magnesium silicate layer, ie a so-called forsterite layer, which has at least two peaks in a DRIFT spectrum of this layer, at least one peak in a wavenumber range of 960 to 975 cm -1 (range (A)), and at least one peak in one
  • Wavelength range from 976 to 990 cm -1 . Furthermore, the peak height of the at least one peak in the region (A) is higher than the peak height of the
  • Invention means "higher” that the at least one peak in the range (A) to at least 5%, preferably at least 30%, is higher than the at least one peak in the region (B).
  • the ratio of the peak height of the at least one peak in the region (A) to the peak height of the at least one peak in the region (B) is greater than 1, 0, preferably greater than or equal to 1, 1, particularly preferably greater than or equal to 1.3 ,
  • the electrical strip according to the invention is particularly suitable in
  • Power transformers are Power transformers, distribution transformers, small transformers or to be used in rotating electrical machines.
  • the present invention therefore further relates to the use of the electrical strip according to the invention in power transformers,
  • Distribution transformers Small transformers or in rotating electrical machines.
  • Grain-oriented electrical tapes 1 to 14 were obtained by the steps of melting a molten steel containing the alloying elements shown in Table 1, casting the molten steel into a thin slab, hot rolling the thin slab at a temperature of 1050 ° C. into a hot strip, and tumbling the hot strip at a temperature from 700 ° C to a coil, cold rolling the hot strip in 5 steps to a thickness between 0.23 and 0.3 mm, annealing the cold strip at a temperature of 700 to 900 ° C according to those given in Table 2
  • Comparative Examples V15 to V28 were prepared. These differ from the examples according to the invention in that equations (1) and (2) are not satisfied.
  • Table 1 Compositions of the melts used, remainder Fe and unavoidable impurities

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Abstract

La présente invention concerne un feuillard magnétique à grains orientés, dont le procédé de fabrication comprend un recuit haute température effectué dans une plage de températures de 700 à 900 °C, le feuillard magnétique présentant, au cours de ce recuit haute température, une teneur en azote N déterminée. L'invention concerne également un procédé de fabrication d'un tel feuillard magnétique.
PCT/EP2018/080926 2017-11-20 2018-11-12 Feuillard magnétique à grains orientés et procédé de fabrication d'un tel feuillard magnétique WO2019096735A1 (fr)

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DE102017220721.3 2017-11-20
DE102017220721.3A DE102017220721A1 (de) 2017-11-20 2017-11-20 Optimierung des Stickstofflevels während der Haubenglühung III

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EP0525467A2 (fr) * 1991-07-10 1993-02-03 Nippon Steel Corporation Tôle d'acier au silicium à grains orientés ayant des propriétés de pellicule de verre primaire excellentes
JPH07310124A (ja) * 1994-05-16 1995-11-28 Nippon Steel Corp 磁気特性、被膜特性の優れた厚い板厚の一方向性電磁鋼板の製造方法
EP0699771A1 (fr) * 1994-05-13 1996-03-06 Nippon Steel Corporation Séparateur de recuit ayant une réactivité haute pour tÔles en acier électrique à grains orientés et procédé pour former un revêtement
JPH08246053A (ja) * 1995-03-02 1996-09-24 Nippon Steel Corp グラス被膜の良好な方向性電磁鋼板の製造方法
EP1025268B1 (fr) 1997-10-15 2002-05-08 ThyssenKrupp Stahl AG Procede de production d'une tole electrique a grains orientes avec une faible perte par inversion magnetique et une polarisation elevee
EP1752549A1 (fr) 2005-08-03 2007-02-14 ThyssenKrupp Steel AG Procédé de fabrication de bande d'acier magnétique à grains orientés
EP1752548A1 (fr) 2005-08-03 2007-02-14 ThyssenKrupp Steel AG Procédé de fabrication de bande en acier magnétique à grains orientés
EP2022874A1 (fr) 2006-05-19 2009-02-11 Nippon Steel Corporation Tôle d'acier électromagnétique directionnel comportant un film de revêtement isolant de tension élevéee, et prodécédé de traitement du film de revêtement isolant
CN102758127B (zh) * 2011-04-28 2014-10-01 宝山钢铁股份有限公司 具有优异磁性能和良好底层的高磁感取向硅钢生产方法
US9038429B2 (en) * 2008-12-31 2015-05-26 Baoshan Iron & Steel Co., Ltd. Method for manufacturing grain-oriented silicon steel with single cold rolling
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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS50134917A (fr) * 1974-04-17 1975-10-25
EP0525467A2 (fr) * 1991-07-10 1993-02-03 Nippon Steel Corporation Tôle d'acier au silicium à grains orientés ayant des propriétés de pellicule de verre primaire excellentes
EP0699771A1 (fr) * 1994-05-13 1996-03-06 Nippon Steel Corporation Séparateur de recuit ayant une réactivité haute pour tÔles en acier électrique à grains orientés et procédé pour former un revêtement
JPH07310124A (ja) * 1994-05-16 1995-11-28 Nippon Steel Corp 磁気特性、被膜特性の優れた厚い板厚の一方向性電磁鋼板の製造方法
JPH08246053A (ja) * 1995-03-02 1996-09-24 Nippon Steel Corp グラス被膜の良好な方向性電磁鋼板の製造方法
EP1025268B1 (fr) 1997-10-15 2002-05-08 ThyssenKrupp Stahl AG Procede de production d'une tole electrique a grains orientes avec une faible perte par inversion magnetique et une polarisation elevee
EP1752549A1 (fr) 2005-08-03 2007-02-14 ThyssenKrupp Steel AG Procédé de fabrication de bande d'acier magnétique à grains orientés
EP1752548A1 (fr) 2005-08-03 2007-02-14 ThyssenKrupp Steel AG Procédé de fabrication de bande en acier magnétique à grains orientés
EP2022874A1 (fr) 2006-05-19 2009-02-11 Nippon Steel Corporation Tôle d'acier électromagnétique directionnel comportant un film de revêtement isolant de tension élevéee, et prodécédé de traitement du film de revêtement isolant
US9038429B2 (en) * 2008-12-31 2015-05-26 Baoshan Iron & Steel Co., Ltd. Method for manufacturing grain-oriented silicon steel with single cold rolling
CN102758127B (zh) * 2011-04-28 2014-10-01 宝山钢铁股份有限公司 具有优异磁性能和良好底层的高磁感取向硅钢生产方法
WO2017037019A1 (fr) 2015-08-28 2017-03-09 Thyssenkrupp Electrical Steel Gmbh Procédé de fabrication d'une tôle magnétique à grains orientés et tôle magnétique à grains orientés

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Title
BEASLEY ET AL.: "Comparison of transmission FTIR, ATR and DRIFT sprecta", JOURNAL OF ARCHEOLOGICAL SIENCE, vol. 46, June 2014 (2014-06-01), pages 16 - 2, XP029021898, DOI: doi:10.1016/j.jas.2014.03.008

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