WO2023121308A1 - Feuille d'acier électrique non orientée, son procédé de fabrication et noyau de moteur la comprenant - Google Patents

Feuille d'acier électrique non orientée, son procédé de fabrication et noyau de moteur la comprenant Download PDF

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WO2023121308A1
WO2023121308A1 PCT/KR2022/020985 KR2022020985W WO2023121308A1 WO 2023121308 A1 WO2023121308 A1 WO 2023121308A1 KR 2022020985 W KR2022020985 W KR 2022020985W WO 2023121308 A1 WO2023121308 A1 WO 2023121308A1
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steel sheet
oriented electrical
base material
electrical steel
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PCT/KR2022/020985
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English (en)
Korean (ko)
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권수빈
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주식회사 포스코
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Publication of WO2023121308A1 publication Critical patent/WO2023121308A1/fr

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    • 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
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • C21D7/04—Modifying the physical properties of iron or steel by deformation by cold working of the surface
    • C21D7/06—Modifying the physical properties of iron or steel by deformation by cold working of the surface by shot-peening or the like
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1222—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
    • C21D8/1233—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
    • 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
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • C22C38/18—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
    • C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
    • C23G1/08—Iron or steel
    • 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
    • H—ELECTRICITY
    • H02—GENERATION; CONVERSION OR DISTRIBUTION OF ELECTRIC POWER
    • H02K—DYNAMO-ELECTRIC MACHINES
    • H02K15/00—Methods or apparatus specially adapted for manufacturing, assembling, maintaining or repairing of dynamo-electric machines
    • H02K15/02—Methods or apparatus specially adapted for manufacturing, assembling, maintaining or repairing of dynamo-electric machines of stator or rotor bodies

Definitions

  • One embodiment of the present invention relates to a non-oriented electrical steel sheet, a manufacturing method thereof, and a motor core including the same. Specifically, an embodiment of the present invention increases the shot ball projection during scale removal, strengthens pickling, suppresses the concentration of Mn on the surface of the steel sheet, and controls the element content in the insulating film, so that the coating after stress relief annealing It relates to a non-oriented electrical steel sheet with improved bonding force, a method for manufacturing the same, and a motor core including the same.
  • Non-oriented electrical steel sheets are mainly used in motors that convert electrical energy into mechanical energy, and excellent magnetic properties of non-oriented electrical steel sheets are required to demonstrate high efficiency in the process.
  • eco-friendly technology has recently been attracting attention, it is considered very important to increase the efficiency of motors that account for the majority of the total electrical energy consumption.
  • the demand for non-oriented electrical steel sheets having excellent magnetic properties is also increasing.
  • the magnetic properties of non-oriented electrical steel are mainly evaluated by iron loss and magnetic flux density.
  • Iron loss means energy loss that occurs at a specific magnetic flux density and frequency
  • magnetic flux density means the degree of magnetization obtained under a specific magnetic field. The lower the iron loss, the more energy efficient motors can be manufactured under the same conditions, and the higher the magnetic flux density, the smaller the motor or the lower the copper loss. It is important.
  • the characteristics of the non-oriented electrical steel sheet to be considered also vary according to the operating conditions of the motor.
  • W15/50 which is the iron loss when a 1.5T magnetic field is applied at a commercial frequency of 50Hz, as the most important.
  • W15/50 core loss is the most important, and depending on the main operating conditions, core loss at different frequencies or applied magnetic fields is evaluated.
  • magnetic properties are often important at low fields of 1.0T or less and high frequencies of 400 Hz or more. characteristics will be evaluated.
  • the non-oriented electrical steel sheet In order to manufacture products such as motors or transformers from non-oriented electrical steel sheet, the non-oriented electrical steel sheet must be slit into a specific shape. In this process, stress is applied to the non-oriented electrical steel sheet, and stress relief annealing is performed to remove this stress.
  • the present invention it is intended to provide a non-oriented electrical steel sheet, a manufacturing method thereof, and a motor core including the same. Specifically, in one embodiment of the present invention, by increasing the shot ball projection during scale removal, strengthening pickling, suppressing the concentration of Mn on the surface of the steel sheet, and adjusting the element content in the insulating film, the coating after stress relief annealing It is intended to provide a non-oriented electrical steel sheet with improved bonding force, a method for manufacturing the same, and a motor core including the same.
  • the non-oriented electrical steel sheet by weight, Si: 2.0 to 6.5%, Al: 0.1 to 1.3%, Mn: 0.3 to 2.0%, and the balance of Fe and unavoidable impurities.
  • Si 2.0 to 6.5%
  • Al 0.1 to 1.3%
  • Mn 0.3 to 2.0%
  • the balance of Fe and unavoidable impurities Including an insulating film positioned on the base material, the steel sheet base material after stress relief annealing satisfies Expression 1 below, and the insulating film satisfies Expression 2 below.
  • [Mn(1)] is the Mn concentration (wt%) at a depth of 1 ⁇ m from the interface between the base material and the insulating film toward the inside of the base material
  • [Mn(10)] is at a depth of 10 ⁇ m represents the Mn concentration of
  • Equation 2 [Fe], [Al], [Mn], and [Mg] represent the contents (wt%) of Fe, Al, Mn, and Mg at the center of the insulation film thickness direction.)
  • the steel sheet base material may further contain at least one of Cr: 0.2% or less (excluding 0%), Sn: 0.06% or less (excluding 0%), and Sb: 0.06% or less (excluding 0%).
  • the steel plate base material may further include 0.005% by weight or less of one or more of C, N, S, Ti, Nb, and V.
  • the steel sheet base material contains at least one of Cu: 0.01 to 0.2 wt%, P: 0.100 wt% or less, B: 0.002 wt% or less, Mo: 0.01 wt% or less, Mg: 0.005 wt% or less, and Zr: 0.005 wt% or less. can include more.
  • the base material of the steel sheet may have an average grain size of 5 to 50 ⁇ m.
  • the deposition amount of the insulating film may be 500 to 1500 mg/m 2 .
  • a method for manufacturing a non-oriented electrical steel sheet according to an embodiment of the present invention is a slab containing, by weight, Si: 2.0 to 6.5%, Al: 0.1 to 1.3%, Mn: 0.3 to 2.0%, the balance Fe, and unavoidable impurities.
  • the step of removing the scale by projecting a short ball on the steel plate in an amount of 15 kg / (m 2 min) to 35 kg / (m 2 min) and pickling may be immersed in pickling liquid for 5 seconds to 120 seconds.
  • the average particle size of the short ball is 0.3 to 0.8 mm, and it can be projected for 5 to 30 seconds.
  • the material of the short ball is not particularly limited, but Fe-based alloys may be used.
  • the step of annealing the cold-rolled sheet may be annealed at a temperature of 700 to 900 ° C.
  • a step of annealing the hot-rolled sheet may be further included prior to the step of removing the scale.
  • a motor core includes a stator formed by stacking a plurality of non-oriented electrical steel sheets, and the non-oriented electrical steel sheet in the stator contains, by weight, Si: 2.0 to 6.5%, Al: 0.1 to 1.3%. , Mn: 0.3 to 2.0%, and a steel sheet base material containing Fe and unavoidable impurities, and an insulating film located on the steel plate base material, the steel plate base material satisfies the following formula 1, and the insulating film satisfies the following formula 2 .
  • [Mn(1)] is the Mn concentration (wt%) at a depth of 1 ⁇ m from the interface between the base material and the insulating film toward the inside of the base material
  • [Mn(10)] is at a depth of 10 ⁇ m represents the Mn concentration of
  • Equation 2 [Fe], [Al], [Mn], and [Mg] represent the contents (wt%) of Fe, Al, Mn, and Mg at the center of the insulation film thickness direction.)
  • the motor core according to an embodiment of the present invention further includes a rotor formed by stacking a plurality of non-oriented electrical steel sheets, and the non-oriented electrical steel sheet contains, by weight, Si: 2.0 to 6.5%, Al: 0.1 to 1.3%. , Mn: 0.3 to 2.0%, and a steel sheet base material containing Fe and unavoidable impurities, and an insulating film located on the steel plate base material, and the steel plate base material may have an average grain size of 5 to 50 ⁇ m.
  • the non-oriented electrical steel sheets included in the stator and the rotor may be non-oriented electrical steel sheets derived from the same coil.
  • a difference in Si, Al, and Mn contents between the non-oriented electrical steel sheets included in the stator and the rotor may be 0.20% by weight or less.
  • the present invention it is possible to suppress the concentration of Mn on the surface of the steel sheet by increasing the shot ball projection amount and strengthening pickling during scale removal. Through this, the bonding strength of the coating after stress relief annealing is improved.
  • the element content in the insulating film is controlled, and through this, the stability of the coating after stress relief annealing is improved.
  • first, second and third are used to describe, but are not limited to, various parts, components, regions, layers and/or sections. These terms are only used to distinguish one part, component, region, layer or section from another part, component, region, layer or section. Accordingly, a first part, component, region, layer or section described below may be referred to as a second part, component, region, layer or section without departing from the scope of the present invention.
  • % means weight%, and 1ppm is 0.0001 weight%.
  • the meaning of further including an additional element means replacing and including iron (Fe) as much as the additional amount of the additional element.
  • a non-oriented electrical steel sheet according to an embodiment of the present invention includes a steel sheet base material and an insulating film positioned on the steel sheet base material.
  • the steel sheet base material according to an embodiment of the present invention includes Si: 2.0 to 6.5%, Al: 0.1 to 1.3%, Mn: 0.3 to 2.0%, the balance Fe and unavoidable impurities, by weight%.
  • Si Silicon
  • Si serves to lower the iron loss by increasing the specific resistance of the material, and when too little is added, the effect of improving the high frequency iron loss may be insufficient. Conversely, if too much is added, the hardness of the material increases and the cold rolling property is extremely deteriorated, resulting in poor productivity and punching performance. Therefore, Si may be added within the above range. More specifically, it may include 2.5 to 5.0% by weight. More specifically, it may include 3.0 to 4.0% by weight.
  • Aluminum (Al) serves to lower iron loss by increasing the resistivity of the material. If too little is added, there is no effect on reducing high-frequency iron loss, and fine nitrides may be formed to deteriorate magnetism. Conversely, if too much is added, it can cause problems in all processes such as steelmaking and continuous casting, greatly reducing productivity. Therefore, Al may be added within the above range. More specifically, it may contain 0.5 to 1.2% by weight. More specifically, it may contain 0.7 to 1.0% by weight.
  • Manganese (Mn) is an element that serves to improve iron loss and form sulfides by increasing the resistivity of materials. If too little Mn is added, sulfides may be finely precipitated to deteriorate magnetism. Conversely, if too much Mn is added, the formation of ⁇ 111 ⁇ texture, which is unfavorable to magnetism, may be promoted and the magnetic flux density may decrease. Therefore, Mn may be added within the above-mentioned range. More specifically, 0.5 to 1.5 wt % of Mn may be included.
  • the specific resistance may be 55 to 80 ⁇ cm.
  • the steel sheet base material may further contain at least one of Cr: 0.2% or less (excluding 0%), Sn: 0.06% or less (excluding 0%), and Sb: 0.06% or less (excluding 0%).
  • Chromium serves to reduce iron loss by increasing the resistivity of the material. It also serves to prevent diffusion of Mn from the base material into the insulating film in the stress relief annealing step. Therefore, Cr may be added within the above range. More specifically, it may contain 0.010 to 0.10% by weight. More specifically, it may include 0.050 to 0.040% by weight. As described above, when an additional element is further included, Fe, which is the remainder, is replaced and included.
  • Tin (Sn) and antimony (Sb) are segregated elements at grain boundaries, suppressing the diffusion of nitrogen through grain boundaries, suppressing ⁇ 111 ⁇ texture harmful to magnetism, and increasing advantageous ⁇ 100 ⁇ texture for magnetic properties. added to improve When too much Sn and Sb are added, crystal grain growth is hindered, resulting in deterioration of magnetism and poor rolling properties. Therefore, Sn and Sb may be added within the above range. More specifically, Sn: 0.005 to 0.050% by weight and Sb: 0.005 to 0.050% by weight may be included. More specifically, Sn: 0.01 to 0.02% by weight and Sb: 0.01 to 0.02% by weight may be included.
  • the steel sheet base material contains at least one of Cu: 0.01 to 0.2 wt%, P: 0.100 wt% or less, B: 0.002 wt% or less, Mo: 0.01 wt% or less, Mg: 0.005 wt% or less, and Zr: 0.005 wt% or less. can include more.
  • Copper (Cu) serves to form a sulfide together with Mn.
  • CuMnS may finely precipitate and degrade magnetism if too little is added. If too much Cu is added, high-temperature brittleness may occur and cracks may be formed during playing or hot rolling. More specifically, 0.05 to 0.10 wt% of Cu may be included.
  • Phosphorus (P) not only serves to increase the specific resistance of the material, but also segregates at the grain boundary to improve the texture to increase the specific resistance and lower the iron loss, so it can be additionally added.
  • P may be added in the above range. More specifically, 0.001 to 0.090% by weight of P may be included. More specifically, 0.005 to 0.085% by weight of P may be included.
  • the steel plate base material may further include 0.005% by weight or less of one or more of C, N, S, Ti, Nb, and V.
  • C When carbon (C) is added in large amounts, it expands the austenite region, increases the phase transformation period, and inhibits the grain growth of ferrite during annealing to increase iron loss. When used after processing from a product to an electrical product, iron loss is increased by magnetic aging. Therefore, C may be added within the above range. More specifically, 0.003% by weight or less of C may be included.
  • S is preferably added as low as possible because it forms fine sulfides inside the base material to suppress crystal grain growth and weaken iron loss. When a large amount of S is included, it may combine with Mn to form precipitates or cause high temperature brittleness during hot rolling. Accordingly, S may be further included in an amount of 0.005% by weight or less. Specifically, it may further include 0.0030% by weight or less of S. More specifically, 0.0001 to 0.0030% by weight of S may further be included.
  • N Nitrogen (N) forms nitride by strongly combining with Al, Ti, etc. to suppress crystal grain growth, and when precipitated, it is preferable to contain less because it interferes with magnetic domain movement. Therefore, N may be added in the above range. More specifically, 0.003% by weight or less of N may be included.
  • titanium (Ti), niobium (Nb), and vanadium (V) are also strong carbonitride-forming elements, it is preferable not to add them as much as possible, and each content is 0.005% by weight or less.
  • the balance includes Fe and unavoidable impurities.
  • unavoidable impurities they are impurities introduced during the steelmaking step and the grain-oriented electrical steel sheet manufacturing process, and since they are well known in the relevant field, a detailed description thereof will be omitted.
  • the addition of elements other than the above-described alloy components is not excluded, and may be variously included within a range that does not impair the technical spirit of the present invention. When additional elements are included, they are included in place of Fe, which is the remainder.
  • the non-oriented electrical steel sheet according to an embodiment of the present invention may have an average grain size of 5 to 50 ⁇ m. If the average grain size is too small, magnetic properties are inferior, and crystal grain growth is limited even after stress relief annealing (SRA), so that magnetism may be inferior even after SRA. If the average grain size is too large, mechanical strength may be inferior. More specifically, the average grain size may be 10 to 35 ⁇ m.
  • SRA stress relief annealing
  • the average grain size may be 10 to 35 ⁇ m.
  • the average grain size described above is a characteristic before SRA.
  • the base material of the steel sheet may satisfy Equation 1 below.
  • [Mn(1)] is the Mn concentration (wt%) at a depth of 1 ⁇ m from the interface between the base material and the insulating film toward the inside of the base material
  • [Mn(10)] is at a depth of 10 ⁇ m represents the Mn concentration of
  • the steel sheet base material according to an embodiment of the present invention has a concentration gradient in which the concentration of Mn increases from the surface to the inside.
  • the Mn of the base material diffuses into the coating in the stress relief annealing step, and the properties of the coating change, thereby deteriorating the bonding strength of the coating.
  • high-frequency iron loss which is a magnetic characteristic
  • the value of [Mn(1)]/[Mn(10)] may be 0.3 to 0.7.
  • the concentration of Mn by thickness can be analyzed through glow discharge spectroscopy (GDS).
  • the insulating film is located on the surface of the base material of the steel sheet.
  • the insulating film 20 serves to insulate between the non-oriented electrical steel sheets when a product is manufactured by laminating the non-oriented electrical steel sheets.
  • the insulating film may be treated with an organic, inorganic, or organic/inorganic composite film, and may be formed by treating with another insulating film.
  • concentration of Mn on the surface side of the steel sheet base material is prevented, and thus, diffusion of Mn into the insulating film can be suppressed.
  • the insulating film may satisfy Equation 2 below.
  • 0.5 to 30% by weight of Fe, 1 to 20% by weight of Al, 0.5 to 5% by weight of Mn, and 0.1 to 10% by weight of Mg may be included.
  • Some of Al, Mn, and Mg, which are components in the insulation coating, are components diffused from the base material of the steel sheet.
  • the content of Al, Mn, Mg, etc. in the insulating film is high, the insulating property of the insulating film may be deteriorated.
  • the bonding strength between the insulating film and the base material may be weakened.
  • a method for manufacturing a non-oriented electrical steel sheet includes the steps of hot-rolling a slab to prepare a hot-rolled sheet; removing scale present on the surface of the hot-rolled sheet; Cold-rolling the scale-removed hot-rolled sheet to prepare a cold-rolled sheet; It includes the steps of annealing a cold-rolled sheet and forming an insulating film on the surface of the cold-rolled sheet.
  • a slab is hot rolled.
  • the alloy components of the slab have been described in the above-described alloy components of the non-oriented electrical steel sheet, overlapping descriptions will be omitted. Since the alloy components are not substantially changed during the manufacturing process of the non-oriented electrical steel sheet, the alloy components of the non-oriented electrical steel sheet and the slab are substantially the same.
  • the slab includes Si: 2.0 to 6.5%, Al: 0.1 to 1.3%, Mn: 0.3 to 2.0%, and the balance Fe and unavoidable impurities, by weight%.
  • the slabs may be heated prior to hot rolling.
  • the heating temperature of the slab is not limited, but the slab can be heated to 1100 to 1250 ° C. If the slab heating temperature is too high, precipitates that harm magnetism may be re-dissolved and finely precipitated after hot rolling.
  • a hot-rolled sheet is manufactured by hot-rolling the slab.
  • the thickness of the hot-rolled sheet may be 2 to 3.0 mm.
  • Hot-rolled sheet annealing is preferably performed in the manufacture of a high-grade electrical steel sheet without phase transformation, and is effective in improving the magnetic flux density by improving the texture of the final annealed sheet.
  • the step of annealing the hot-rolled sheet may be annealed at a temperature of 850 to 1200 °C. If the hot-rolled sheet annealing temperature is too low, it is difficult to expect the effect of increasing the magnetic flux density because the structure does not grow or grows finely below. If the annealing temperature of the hot-rolled sheet is too high, the magnetic properties are rather deteriorated, and the rolling workability may be deteriorated due to deformation of the plate shape. Hot-rolled sheet annealing is performed to increase orientation favorable to magnetism, if necessary, and can be omitted. The annealed hot-rolled sheet may be pickled.
  • the scale present on the surface of the hot-rolled sheet is removed.
  • the concentration of Mn on the surface of the steel sheet is suppressed through the removal of the oxide layer before final annealing by increasing the amount of shot balls and strengthening pickling.
  • the step of removing the scale includes removing the scale by projecting a short ball onto the steel sheet in an amount of 15 to 35 kg/(m 2 ⁇ min). If the projection amount of the shot ball is too small, the oxide layer remains and amplifies the surface segregation phenomenon of Mn. As a result, Mn diffusion into the insulating film is increased in the stress relief annealing step. Conversely, if the projected amount of the short ball is too large, the surface of the steel plate is greatly damaged, so the upper limit can be adjusted appropriately. More specifically, it may be projected onto the steel sheet in an amount of 17 to 30 kg/(m 2 min). Even if the same amount per area is projected, a difference occurs in securing the fine crystal grains according to the length of time to be projected, so in one embodiment of the present invention, the amount of projection according to time and area is defined.
  • the average particle size of the short ball is 0.1 to 1 mm, and it can be projected for 1 second to 60 seconds. More specifically, the average particle size of the short ball is 0.3 to 0.8 mm, and it can be projected for 5 to 30 seconds.
  • the average particle size of the shotball and the shotball projection time can also affect the surface nucleation site.
  • the material of the short ball is not particularly limited, but Fe-based alloys may be used.
  • the pickling solution is not particularly limited, and hydrochloric acid and sulfuric acid may be used. If the concentration of the pickling solution and the immersion time are too low or too short, the roughness of the steel sheet damaged by short balls is not improved, and thus Mn diffuses to the surface through the defective portion during final annealing. This phenomenon may be a problem in maintaining the bonding strength of the insulating film in the stress relief annealing step. Conversely, if the concentration of the pickling solution and the immersion time are too high or too long, a large amount of damage to the surface of the steel sheet may occur. More specifically, pickling may be performed by immersing in pickling liquid for 5 to 120 seconds. The concentration of the pickling solution may be 5 to 30 wt%.
  • the bonding force of the insulating film may be weakened or surface defects may occur. More specifically, [thrown amount] / [immersion time] may be 0.5 to 2. More specifically, it may be 0.75 to 1.5.
  • the hot-rolled sheet is cold-rolled to manufacture a cold-rolled sheet.
  • Cold rolling is final rolling to a thickness of 0.15 mm to 0.65 mm.
  • secondary cold rolling may be performed after primary cold rolling and intermediate annealing, and the final reduction ratio may be in the range of 50 to 95%.
  • the cold-rolled sheet is annealed.
  • Cold-rolled sheet annealing is performed for 10 to 1000 seconds within a range of 700 to 900° C. so that the grain size in the cross section of the steel sheet is 10 to 50 ⁇ m. If the cold-rolled sheet annealing temperature is too low, the crystal grains are small and iron loss may be deteriorated. If the temperature is too high, grains may be coarsened and mechanical strength may be reduced. More specifically, it may be annealed in the range of 750 to 850 °C.
  • an insulating film can be formed after cold-rolled sheet annealing.
  • the insulating coating may be treated with organic, inorganic, and organic/inorganic composite coatings, and may be treated with other insulating coatings.
  • it may be formed by applying an insulating film-forming composition containing 40 to 70% by weight of metal phosphate and 0.5 to 10% by weight of silica.
  • the stress relief annealing step is performed at a temperature of 700° C. to 850° C. for 10 minutes to 300 minutes.
  • the motor core includes a stator formed by stacking a plurality of non-oriented electrical steel sheets, and the non-oriented electrical steel sheet contains, by weight, Si: 2.0 to 6.5%, Al: 0.1 to 1.3 %, Mn: 0.3 to 2.0%, and includes a steel sheet base material containing Fe and unavoidable impurities and an insulating film located on the steel plate base material, the steel plate base material satisfies the following formula 1, and the insulating film satisfies the following formula 2 do.
  • [Mn(1)] is the Mn concentration (wt%) at a depth of 1 ⁇ m from the interface between the base material and the insulating film toward the inside of the base material
  • [Mn(10)] is at a depth of 10 ⁇ m represents the Mn concentration of
  • the motor core according to an embodiment of the present invention further includes a rotor formed by stacking a plurality of non-oriented electrical steel sheets, and the non-oriented electrical steel sheet is weight%, Si: 2.0 to 6.5%, Al: 0.1 to 1.3%, Mn: 0.3 to 2.0%, the balance Fe and unavoidable impurities, and an insulating film positioned on the steel sheet base material, and the steel sheet base material may have an average grain size of 5 to 50 ⁇ m.
  • the characteristics of the non-oriented electrical steel sheet before SRA are derived, and the steel sheet base material may have an average grain size of 5 to 50 ⁇ m. Since the steel components and average grain size of the non-oriented electrical steel sheet have been described in relation to the aforementioned non-oriented electrical steel sheet, overlapping descriptions will be omitted.
  • stator and rotor are punched out in an approximate donut or disc shape.
  • stator and the rotor are manufactured by punching the stator and the rotor from coils of separate non-oriented electrical steel sheets, the remaining punched parts are scrapped, which leads to an increase in process cost and a waste of resources and energy.
  • scrap processing can be minimized.
  • the non-oriented electrical steel sheets included in the stator and the rotor may be non-oriented electrical steel sheets derived from the same coil.
  • the meaning derived from the same coil means that steel components such as Si, Al, and Mn in the non-directional included in the stator and the rotor are substantially the same. Specifically, it means that the difference in Si, Al and Mn contents between the stator and the rotor is 0.20% by weight or less. More specifically, it means that the difference in Si, Al and Mn content between the stator and the rotor is 0.10% by weight or less.
  • the difference in Si, Al and Mn content between the stator and the rotor is 0.05% by weight or less. More specifically, it means that the difference in Si, Al and Mn content between the stator and the rotor is 0.01% by weight or less.
  • Components of the insulating film may also be substantially the same between the stator and the rotor.
  • a slab composed of Tables 1 and 2 below and the balance of Fe and other unavoidably added impurities was prepared.
  • the slab was heated to 1150° C., and hot finish rolling was performed at 850° C. to produce a hot-rolled sheet having a thickness of 2.3 mm.
  • the hot-rolled hot-rolled sheet was annealed at 1100° C. for 4 minutes.
  • a steel shortball with an average diameter of 0.5 ⁇ m was blasted at the projection amount listed in Table 3 to remove scale, and pickled in a 20 wt% aqueous hydrochloric acid solution for the time listed in Table 3 below.
  • cold rolling was performed to obtain a sheet thickness of 0.27 mm, and cold-rolled sheet annealing was performed at 800° C. for 5 minutes.
  • the insulating film was formed to a thickness of 0.5 ⁇ m using an insulating film composition containing 50% by weight of Al phosphate and 5% by weight of silica.
  • Iron loss and magnetic flux density were measured as averages in the rolling direction and in the vertical direction of rolling with a single sheet tester by cutting 5 specimens with a width of 60 mm ⁇ a length of 60 mm ⁇ the number of sheets for each specimen.
  • the strength was measured through a tensile test, and the standard of the tensile test piece was JIS13-A.
  • Shortball throw amount/ immersion time Shortball throw amount (kg/min m2) short ball throw time (candle) immersion time (candle) Mn1 Mn10 [Mn1] /[Mn10]
  • Insulation film note Fe Al Mn Mg (Al+2*Mn+Mg)/10 Expression 2 Satisfaction One 2.93 9.81 1.35 9.25 2.176 O 2 2.75 9.11 2.7 8.87 2.338 O 3 2.93 7.39 3.63 8.94 2.359 O 4 3.05 8.38 3.9 9.35 2.553 O 5 2.56 7.74 3.25 9.09 2.333 O 6 2.81 8.61 4.5 8.94 2.655 O 7 3.01 10.12 2.94 8.78 2.478 O 8 2.67 8.51 1.05 9.27 1.988 O 9 No cold rolling 10 2.88 6.23 5.16 9.1 2.565 O 11 2.86 9.25 5.36 8.9 2.887 X 12 2.64 8.86 0.75 8.93 1.929 O 13 1.25 8.17 6.6 8.85 3.022 X 14 1.85 11.11 0.69 8.64 2.113 X 15 1.68 8.35 1.53 8.62 2.003 X 16 1.98 10.82 0.57 8.79 2.075 X 17 1.67 6.88 0.63 8.85 1.699 X 18 2.38 7.06 2.25 8.93 2.049 O 19 2.
  • steel No. 1 to 7 can confirm that the effect is excellent.
  • the short ball projection amount / immersion time is small, Mn1 / Mn10 is high, or Equation 2 is not satisfied, so that the magnetic flux density before / after stress relief annealing, iron loss after stress relief annealing, adhesion, and surface characteristics are part of it. there is.

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Abstract

Une feuille d'acier électrique non orientée selon un mode de réalisation de la présente invention comprend : un matériau de base de feuille d'acier comprenant, en % en poids, 1,0 à 6,5 % de Si, 0,1 à 1,3 % d'Al, 0,3 à 2,0 % de Mn et le reste étant du Fe et des impuretés inévitables ; et un film d'isolation positionné sur le matériau de base de feuille d'acier, le matériau de base de feuille d'acier satisfaisant la formule 1 suivante et le film d'isolation satisfaisant la formule 2 suivante. [Formule 1] 0,1 ≤ [Mn (1)]/[Mn (10)] ≤ 1,0 [Formule 2] [Fe] ≥ [Al] + [Mn] + [Mg]/10. (Dans la formule 1, [Mn(1)] est la concentration (% en poids) de Mn à une profondeur de 1 µm à partir de l'interface entre le matériau de base et le film d'isolation vers l'intérieur du matériau de base, et [Mn(10)] représente la concentration de Mn à une profondeur de 10 µm. Dans la formule 2, [Fe], [Al], [Mn] et [Mg] représentent les quantités (% en poids) de Fe, Al, Mn et Mg au centre, dans le sens de l'épaisseur, du film d'isolation.)
PCT/KR2022/020985 2021-12-22 2022-12-21 Feuille d'acier électrique non orientée, son procédé de fabrication et noyau de moteur la comprenant WO2023121308A1 (fr)

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Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0920966A (ja) * 1995-05-02 1997-01-21 Sumitomo Metal Ind Ltd 磁気特性と打ち抜き性に優れた電磁鋼板
KR20190003783A (ko) * 2016-08-05 2019-01-09 신닛테츠스미킨 카부시키카이샤 무방향성 전자 강판, 무방향성 전자 강판의 제조 방법 및 모터 코어의 제조 방법
JP2021038458A (ja) * 2019-08-30 2021-03-11 Ｊｆｅスチール株式会社 無方向性電磁鋼板およびその製造方法
WO2021117325A1 (fr) * 2019-12-09 2021-06-17 Ｊｆｅスチール株式会社 Tôle d'acier électromagnétique non orientée, noyau de moteur et procédés pour fabriquer respectivement ladite tôle d'acier et ledit noyau de moteur
KR102297753B1 (ko) * 2019-12-18 2021-09-03 주식회사 포스코 Sra후 철손이 낮은 고강도 무방향성 전기강판과 이의 제조방법

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0920966A (ja) * 1995-05-02 1997-01-21 Sumitomo Metal Ind Ltd 磁気特性と打ち抜き性に優れた電磁鋼板
KR20190003783A (ko) * 2016-08-05 2019-01-09 신닛테츠스미킨 카부시키카이샤 무방향성 전자 강판, 무방향성 전자 강판의 제조 방법 및 모터 코어의 제조 방법
JP2021038458A (ja) * 2019-08-30 2021-03-11 Ｊｆｅスチール株式会社 無方向性電磁鋼板およびその製造方法
WO2021117325A1 (fr) * 2019-12-09 2021-06-17 Ｊｆｅスチール株式会社 Tôle d'acier électromagnétique non orientée, noyau de moteur et procédés pour fabriquer respectivement ladite tôle d'acier et ledit noyau de moteur
KR102297753B1 (ko) * 2019-12-18 2021-09-03 주식회사 포스코 Sra후 철손이 낮은 고강도 무방향성 전기강판과 이의 제조방법

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