WO2022234901A1 - Feuille d'acier électrique à texture (001) et son procédé de fabrication - Google Patents

Feuille d'acier électrique à texture (001) et son procédé de fabrication Download PDF

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WO2022234901A1
WO2022234901A1 PCT/KR2021/013581 KR2021013581W WO2022234901A1 WO 2022234901 A1 WO2022234901 A1 WO 2022234901A1 KR 2021013581 W KR2021013581 W KR 2021013581W WO 2022234901 A1 WO2022234901 A1 WO 2022234901A1
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steel sheet
electrical steel
mns
less
ferrite
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PCT/KR2021/013581
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Korean (ko)
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허남회
최인석
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주식회사 썸백
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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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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

Definitions

  • the present invention is (001) It relates to an electrical steel sheet composed of a texture and a method for manufacturing the same.
  • Electrical steel sheet plays an important role in determining the energy efficiency of electrical equipment, because electrical steel sheet is used as an iron core material in rotating equipment such as motors and generators and stationary equipment such as small transformers. This is because it converts energy into energy.
  • the magnetic properties of the electrical steel sheet include iron loss (W 15/50/kg or W 10/400/kg ) and magnetic flux density ( B 8 or B 50 ). So the lower the better. On the other hand, when an external magnetic field is applied, as the magnetic flux density indicating the ease of magnetization is larger, the desired magnetic flux density can be obtained even when a small current is applied. good night.
  • iron loss can be reduced by adding Si, Al, Mn, etc., which are alloying elements with high specific resistance.
  • Si silicon
  • Mn alloying elements with high specific resistance
  • non-oriented electrical steel sheets are composed of a ⁇ 111 ⁇ uvw> texture, and (001) including a [100] crystal axis that is an easy magnetization axis. Since the surface fraction is about 5 to 10%, the magnetic properties are not excellent. For example, in the case of 0.35 mm thickness, as the amount of Si and Al added decreases, the magnetic flux density (B 50 ) increases to about 1.65 to 1.71 Tesla, but the corresponding iron loss (W 15/50 ) is also about 2 W/kg to about 3 W increase to /kg.
  • the magnetic flux density (B 50 ) increases to about 1.67 Tesla to 1.70 Tesla, but the corresponding iron loss (W 15/50 ) is about 2.4 W/kg to 3.55 W
  • the increase to /kg is unavoidable.
  • the current non-oriented electrical steel sheet production process shows (001) high magnetic properties. Since the area fraction of the crystal grains cannot be increased to about 5 to 10% or more, iron loss reduction is being pursued by adding a large amount of Si, Al, Mn, etc., which increase the specific resistance.
  • (001) including the [100] direction which is the axis of easy magnetization in the electrical steel sheet It is desirable to dramatically increase the area fraction of crystal grains and significantly lower the area fraction of ⁇ 111 ⁇ crystal grains that impair magnetic properties.
  • Mn evaporates from the surface at the same time as the decarburization reaction during heat treatment in a relatively low temperature region of 950° C. to 1050° C. and high vacuum, and surface oxidation occurs due to a relatively low temperature region even in a high vacuum, so that manganese from the inside of the steel sheet to the surface It is impossible to avoid the formation of a surface demanganese layer and a surface oxide film, which are harmful to magnetic properties due to a decrease in concentration.
  • the cross-sectional structure of the steel sheet obtained through the above inventions is (001) in the decarburization reaction direction from the surface of the steel sheet to the inside of the steel sheet during heat treatment, as can be seen in Academic Documents 1 and 2 Since the ferrite ( ⁇ ) grains grow from both surfaces of the steel sheet to the inside of the steel sheet, it is characterized by a shape in which grain growth finally meets at the center of the steel sheet.
  • the Mn addition amount is 0.5% or less
  • the amount of MnS precipitation is small during hot rolling and cooling, hot-rolled sheet annealing and cold-rolled steel sheet final annealing.
  • the electrical steel sheet according to an embodiment of the present invention is, by weight, Si: 2.0% to 4.0%, Mn: more than 0.5% and 2.0% or less, S: 0.01% or less (excluding 0%) , C: 0.01% or less (excluding 0%), N: 0.01% or less (excluding 0%), the remainder including Fe and other unavoidable impurities, (001) It is composed of grains and shows the maximum surface strength (001)
  • the angle ( ⁇ ) between the [100] crystal direction in the texture and the rolling direction satisfies 6 ⁇ ⁇ ⁇ 25 ⁇ , and may be characterized as having a thickness of 0.1 mm or more by single-stage cold rolling.
  • the electrical steel sheet according to an example of the present invention has an average (001)
  • the grain diameter penetrates the steel plate thickness, and the average (001)
  • the grain diameter may be 1 to 50 times the thickness of the steel sheet, and the average (001)
  • the grain diameter may be 0.4 to 12 mm.
  • the electrical steel sheet according to an example of the present invention is (001)
  • the area fraction of the grains may be 50% or more
  • the magnetic flux density (B 50 ) is 1.70 Tesla or more
  • the iron loss (W 15/50 ) to the steel sheet thickness ratio is 3 to 12 Watts/kg/mm It may be characterized .
  • the electrical steel sheet composed of (001) texture according to the present invention is, by weight, Si: 2.0% to 4.0%, Mn: more than 0.5% and 2.0% or less, S: 0.01% or less (excluding 0%), C: 0.01 % or less (excluding 0%), N: 0.01% or less (excluding 0%), the remainder including Fe and other unavoidable impurities, (001) It is composed of grains and shows the maximum surface strength (001)
  • the angle ( ⁇ ) between the [100] crystal direction in the texture and the rolling direction satisfies 6 ⁇ ⁇ ⁇ 25 ⁇ , and has a thickness of 0.1 mm or more by single-stage cold rolling, (001)
  • the area fraction of the crystal grains becomes 50% or more, and the magnetic flux density (B 50 ) and iron loss (W 15/50 ) of 1.70 Tesla or more and the steel sheet thickness ratio to 3 to 12 Watts/kg/mm can be achieved.
  • 1 is a state diagram showing the change in the existence region of ferrite ( ⁇ ), MnS precipitates and austenite ( ⁇ ) according to temperature according to the amount of Mn, which is an austenite ( ⁇ ) stabilizing element, in an Fe-2%Si-0.002%S alloy system; It is a drawing obtained by using the ThermoCalc program with the built-in TCFE 9 database, which is used universally for calculation.
  • FIG. 2 is a state diagram showing the change in the existence region of ferrite ( ⁇ ), MnS precipitates and austenite ( ⁇ ) according to temperature according to the amount of Mn, which is an austenite ( ⁇ ) stabilizing element, in the Fe-3.1%Si-0.002%S alloy system; It is a drawing obtained by using the ThermoCalc program with the built-in TCFE 9 database, which is used universally for calculation.
  • FIG. 3 is a state diagram showing the change in the presence region of ferrite ( ⁇ ), MnS precipitates, and austenite ( ⁇ ) according to temperature according to the amount of Mn, which is an austenite ( ⁇ ) stabilizing element, in the Fe-4%Si-0.002%S alloy system; It is a drawing obtained by using the ThermoCalc program with the built-in TCFE 9 database, which is used universally for calculation.
  • Example 4 is (001) in Example 4 below; A diagram showing the change in the content of Si atoms and Mn atoms as they enter the steel sheet from the surface of the steel sheet after final annealing in steel grade D with a grain area fraction of 98% and a steel sheet thickness of 0.1 mm (100 ⁇ m).
  • Example 5 is an orientation distribution function (ODF) for a steel sheet B having a (001) grain area fraction of 96% and a steel sheet thickness of 0.1 mm (100 ⁇ m) in Example 5 below ⁇ 001 ⁇ ⁇ 130 > It is a diagram showing the collective organization.
  • ODF orientation distribution function
  • FIG. 6 is a view showing the ODF of FIG. 5 in an etch-fit structure.
  • % means % by weight.
  • (001) used in the present invention Face is the crystallographic (001) of the grains constituting the electrical steel sheet.
  • the plane means the plane parallel to the plate plane of the electrical steel sheet.
  • the plate surface of the electrical steel sheet means the xy plane when the rolling direction (RD direction) of the steel sheet is the x-axis width direction (TD direction) is the y-axis.
  • the texture was measured using EBSD (Electron Backscatter Diffraction), and the surface strength for each orientation was calculated and analyzed using an orientation distribution function (ODF). Also, (001) The area fraction of the crystal grains was measured using the Etch-pit method and an optical microscope.
  • the average grain diameter was obtained using a conventional grain size calculation method using an optical microscope.
  • the surface strength of the aggregate means the relative strength based on the intensity 1 of the disordered organization without any aggregate structure.
  • the present inventors have repeatedly studied a method for increasing magnetic flux density while lowering iron loss, and have found that it is possible to simultaneously improve iron loss characteristics and magnetic flux density characteristics when manufacturing an electrical steel sheet satisfying the following configuration. came to the conclusion of the invention.
  • the electrical steel sheet according to an example of the present invention is, by weight, Si: 2.0% to 4.0%, Mn: more than 0.5% and 2.0% or less, S: 0.01% or less (excluding 0%), C: 0.01% or less (excluding 0%), N: 0.01% or less (excluding 0%), the remainder including Fe and other unavoidable impurities, (001) It is composed of grains and shows the maximum surface strength (001)
  • the angle ( ⁇ ) between the [100] crystal direction in the texture and the rolling direction satisfies 6 ⁇ ⁇ ⁇ ⁇ 25 ⁇ , and may be characterized as having a thickness of 0.1 mm or more by single-stage cold rolling.
  • (001) Electrical steel sheet composed of texture is (001)
  • the area fraction of the crystal grains becomes 50% or more, and the magnetic flux density (B 50 ) and iron loss (W 15/50 ) of 1.70 Tesla or more and the steel sheet thickness ratio to 3 to 12 Watts/kg/mm can be achieved.
  • Such excellent properties are achieved by excessive precipitation of MnS during reheating and annealing through the addition of excess Mn of more than 0.5% and 2.0% or less, and thereby preventing intensive segregation of S on the surface of the steel sheet during final annealing (001) This can be achieved by preventing the surface energy of the ⁇ 111 ⁇ crystal plane from being lower than that of the crystal plane.
  • MnS precipitates that hinder grain growth are decomposed through reducing gas so that Mn cations (Mn 2+) are dissolved in the steel sheet in an atomic state (Mn) again, and S anions (S 2 - ) are combined with reducing gas such as hydrogen gas.
  • reducing gas such as hydrogen gas.
  • the electrical steel sheet according to an example of the present invention is (001)
  • the grain area fraction may be 70% or more, and more preferably 90% or more.
  • the magnetic flux density (B 50 ) may be 1.72 Tesla or more, more preferably 1.74 Tesla or more, and most preferably 1.76 Tesla or more, and the upper limit thereof is not particularly limited, but may be, for example, 2.0 Tesla.
  • the iron loss (W 15/50 ) to the steel plate thickness ratio may be 3 to 12 Watts/kg/mm.
  • the electrical steel sheet according to an example of the present invention has an average (001)
  • the grain diameter penetrates the steel plate thickness, and the average (001)
  • the grain diameter may be 1 to 50 times the thickness of the steel sheet, and more preferably average (001)
  • the grain diameter may be 5 to 35 times the thickness of the steel sheet. In this range, both low iron loss and high magnetic flux density characteristics can be secured. More specifically, the average (001) The grain diameter may be 0.4 to 12 mm, and may be less than 0.4 to 5 mm.
  • the electrical steel sheet according to an example of the present invention has (001) indicating the maximum surface strength.
  • the angle ( ⁇ ) between the [100] crystal direction in the texture and the rolling direction may satisfy 6 ⁇ ⁇ ⁇ ⁇ 25 ⁇ , more preferably 10 ⁇ ⁇ ⁇ ⁇ 18 ⁇ , even more preferably 12 ⁇ ⁇ ⁇ ⁇ 16 ° can be satisfied.
  • the surface of the steel sheet is characterized in that there is no demanganese layer and surface oxide film. Through this, low iron loss and high magnetic flux density characteristics can be secured at the same time.
  • the Si is a major element added to increase the specific resistance of the steel to lower the eddy current loss during iron loss, and when it is less than 2.0%, (001) due to the presence of the austenite ( ⁇ ) phase during heat treatment Since the texture is not smoothly developed, it is difficult to obtain high magnetic flux density and extremely low iron loss characteristics, and when it is added in excess of 4.0%, plate breakage occurs during cold rolling.
  • Si is limited to 2.0% to 4.0% by weight.
  • Mn more than 0.5% and less than 2.0%
  • the Mn exhibits a strong effect of lowering iron loss by increasing the specific resistance along with Si, Al, etc., but when it is present inside the electrical steel sheet after forming MnS precipitates by combining with sulfur, (001) not only interferes with grain growth, Mn is added up to 0.3% in the current non-oriented electrical steel sheet composed of ⁇ 111 ⁇ texture because it interferes with the movement of the magnetic domain and causes an increase in iron loss and a decrease in magnetic flux density. For this reason, the non-oriented electrical steel sheet composed of ⁇ 111 ⁇ texture is suppressed as much as possible by final annealing within 3 minutes in a temperature range of 900 to 1100°C, thereby maximally suppressing MnS production.
  • the MnS generation start curve draws a C curve, and the C curve moves to a relatively high temperature and short time region as the amount of Mn and S added increases. Due to the existence of the C curve, MnS is precipitated inside the steel sheet during cooling after hot rolling, and additional generation of MnS is essential while the cold-rolled steel sheet is heated up to the final annealing temperature and maintained at the final annealing temperature at a certain heating rate.
  • the electrical steel sheet according to an embodiment of the present invention may satisfy the following relational expression (1).
  • [Mn] 0 is the content (% by weight) of manganese atoms (Mn) in the slab
  • [Mn] 1 is the content (% by weight) of manganese atoms (Mn) in the steel sheet after final annealing.
  • MnS precipitates are decomposed during final annealing after MnS precipitation, and Mn is dissolved back into the steel in an atomic state, so the content of Mn in the steel sheet after final annealing with the slab This can be almost identical.
  • [Mn] 1 is 0T point (surface), (1/100)T point, (1/20)T point, (1/10)T point, and 1/2T point in the thickness (T) direction from the surface of the steel sheet. It may be an average value after analyzing the Mn content in the (center), and the upper limit of [Mn] 0 ⁇ 1.05 considers the measurement error during the experiment.
  • iron loss is significantly reduced (001)
  • Mn is added in an amount of at least 0.5% or more, and high (001) even in a thick steel sheet
  • Final annealing is performed at a relatively high temperature for a long time to obtain the aspect ratio.
  • (001) due to the generation of austenite ( ⁇ ) phase during final annealing.
  • the development of the collective tissue may be insufficient and the magnetic properties may be poor.
  • the Mn addition amount is limited to more than 0.5% and not more than 2.0%.
  • the amount of S added is limited to 0.01% or less.
  • the austenite ( ⁇ ) region is enlarged during final annealing (001)
  • the content of C is limited to 0.01% or less because it suppresses grain growth and forms carbides by combining with Fe and Ti, etc., thereby lowering magnetic flux density and increasing iron loss.
  • N forms a nitride by strongly bonding with Al, Ti, etc.
  • the austenite ( ⁇ ) region expands during final annealing (001) It is preferable to contain as little as possible in order to suppress crystal grain growth, and in the present invention, the amount of N added is limited to 0.01% by weight or less.
  • the remainder is composed of Fe and other unavoidable impurities.
  • alloy elements and component ranges to be included without impairing the effects of the present invention are as follows.
  • Figure 1 shows the temperature of ferrite ( ⁇ ), MnS precipitates and austenite ( ⁇ ) according to the amount of Mn, which is an austenite ( ⁇ ) stabilizing element, in an Fe-2%Si-0.002%S alloy system containing S. It is a diagram showing changes in the existence area. 1 is a ferrite ( ⁇ ) in which the austenite ( ⁇ ) phase does not exist in the temperature range from 1000° C. to about 1035° C. or less, even if Mn is added more than 0.5% and 0.7% in the Fe-2%Si-0.002%S alloy system. + MnS region is shown. In addition, when the amount of S added is increased, the amount of MnS precipitated increases.
  • FIG. 3 shows the presence region of ferrite ( ⁇ ), MnS precipitates and austenite ( ⁇ ) according to temperature according to the amount of Mn, which is an austenite ( ⁇ ) stabilizing element, in a Fe-4%Si-0.002%S alloy system containing S. It is a diagram showing change. In the Fe-4%Si-0.002%S alloy system in which Si, which is a ferrite ( ⁇ ) stabilizing element, is added in large amounts, austenite ( ⁇ ) phase does not exist in the entire temperature range even when Mn is significantly added up to about 2.8%. Non-ferrite ( ⁇ ) + MnS or ferrite ( ⁇ ) single phase is shown. Similarly in the alloy system of FIGS.
  • Example 4 is (001) in Example 4 below;
  • the content of Si and Mn in the steel sheet after final annealing is almost the same as the content of Si and Mn in the slab, regardless of the depth of the steel sheet, and it can be seen that the precipitated MnS is almost completely decomposed.
  • the manufacturing method of an electrical steel sheet having such excellent iron loss characteristics and magnetic flux density characteristics is a) by weight, Si: 2.0% to 4.0%, Mn: more than 0.5% and 2.0% or less, S: 0.01% or less (excluding 0%) ), C: 0.01% or less (excluding 0%), N: 0.01% or less (excluding 0%), reheating the slab containing the remainder Fe and other unavoidable impurities to 950 to 1250 °C;
  • the electrical steel sheet steel slab satisfying the above composition is reheated to 950 ° C. to 1250 ° C. and then hot rolled. If the reheating temperature is less than 950 °C, excessive force is required during hot rolling, which puts a strain on the equipment or it is difficult to perform smooth hot rolling. limited to
  • the reheated slab is hot-rolled to obtain a hot-rolled steel sheet.
  • the hot-rolled steel sheet manufactured as described above may be cold-rolled after pickling without annealing, or hot-rolled steel sheet annealing may be performed before cold rolling for tissue homogenization.
  • the hot-rolled steel sheet annealing temperature may be a ferrite ( ⁇ ) + MnS precipitate temperature in which an austenite ( ⁇ ) phase does not exist in the region of 800°C to 1250°C, and a single phase of ferrite ( ⁇ ) or ferrite ( ⁇ ) and MnS precipitates are mixed. In this range, precipitation of MnS is active, and the S content in the steel can be minimized. It can promote the growth of crystal grains.
  • the annealing temperature of the hot-rolled steel sheet is lower than 800°C, the grain structure is not uniform, and when it exceeds 1250°C, the surface defects of the hot-rolled sheet are excessive due to excessive grain growth.
  • the hot-rolled steel sheet is cold-rolled in a conventional manner after pickling.
  • the pickled hot-rolled steel sheet can be cold-rolled and cold-rolled in one stage.
  • the cold rolling rate in the case of single-stage cold rolling may be 70% to 96%
  • the thickness of the cold-rolled steel sheet is 0.1 mm or more, specifically 0.1 to 0.5 mm, preferably 0.1 to 0.35 mm.
  • the austenite ( ⁇ ) phase does not exist in the range of 1000° C. to 1250° C.
  • the ferrite ( ⁇ ) single phase or ferrite ( ⁇ ) and MnS precipitates are mixed with the ferrite ( ⁇ ) + MnS precipitate temperature and final annealing under a reducing gas atmosphere of 1 atm.
  • the temperature increase rate to the final annealing temperature may be 25 °C / h to 14400 °C / h
  • the final annealing time may be performed at the temperature for 8 to 48 hours.
  • the cold-rolled steel sheet does not have an austenite ( ⁇ ) phase, and a single phase of ferrite ( ⁇ ) or ferrite ( ⁇ ) and MnS precipitates
  • An electrical steel sheet composed of (001) crystal grains can be easily manufactured by final annealing for a long time in a reducing gas atmosphere of 1 atm and a temperature of mixed ferrite ( ⁇ ) + MnS precipitates.
  • the non-oriented electrical steel sheet composed of ⁇ 111 ⁇ uvw> texture applied to the current motor iron core changes the measurement angle from 0° to 45° with respect to the rolling direction and changes the magnetic properties depending on the direction. It shows a difference of about ⁇ 5% compared to the average value, so the measured value shows a difference of up to 10%. Therefore, due to this difference, strictly speaking, the average value of the electrical steel sheet should be indicated using a ring type test piece, but in general, a rectangular steel sheet test piece and a DC magnetometer are used to measure the rolling direction and perpendicular to the rolling direction. Two magnetic properties in one direction are shown as representative values of the electrical steel sheet.
  • the magnetic properties of the electrical steel sheet composed of (001)[010] texture increased from 0° to 45° from the rolling direction, and the deviation angle between the rolling direction and the measurement direction increased. Accordingly, the magnetic flux density changes abruptly from the maximum value to the minimum value, and the iron loss changes from the minimum value to the maximum value.
  • the deviation angle increased from 45° to 90° the magnetic flux density rapidly increased from the minimum value to the maximum value, and the iron loss increased from the maximum value to the maximum value. decreases to the minimum value.
  • the magnetic properties of the present invention composed of (001) texture are measured by the non-oriented electrical steel sheet magnetism in the direction parallel to the rolling direction and the direction perpendicular to the rolling direction. value cannot be represented. Therefore, in order to accurately represent the magnetic properties of the present invention composed of (001) crystal grains, the average value of the magnetic properties was measured using a ring type test piece as in the following example.
  • a ring-type steel sheet having an inner diameter of 15 mm and an outer diameter of 30 mm is cut from the final annealed steel sheet, and the iron loss and magnetic flux density are measured after stress relief annealing in an argon (Ar) atmosphere at 800° C. for 1 hour.
  • the results are shown in Table 3 below shown in As can be seen from one embodiment, the electrical steel sheet mostly composed of (001) grains shows the same average magnetic properties regardless of changes in process parameters if the components and thickness are the same.
  • the product of the present invention composed of a texture is finally shipped to the customer after insulating film treatment.
  • the insulating film may be treated with an organic, inorganic and organic/inorganic composite film, and may be subjected to a tension coating treatment to further reduce iron loss.
  • a customer can use an electrical steel sheet composed of (001) texture after manufacturing a motor iron core, stress relief annealing at 800°C for 1 to 2 hours, and discharge after furnace cooling to 400°C.
  • the slabs of the composition A to E of Table 1 (wt%, balance is Fe) were heated to 1150° C. and hot-rolled to a thickness of 2.5 mm.
  • the hot-rolled steel sheet was annealed at 1050° C. for 2 minutes, and after pickling, one-stage cold rolling was performed to a thickness of 0.10 mm, 0.15 mm, or 0.35 mm.
  • the final annealing of the cold-rolled steel sheet was carried out according to the conditions of Table 2 below under a hydrogen (H 2 ) gas atmosphere of 1 atm.
  • a slab of the composition D in Table 1 (wt%, balance is Fe) was heated to 1150° C. and hot-rolled to a thickness of 2.5 mm.
  • the hot-rolled steel sheet was annealed at 1050° C. for 2 minutes, and after pickling, it was cold-rolled in one step to a thickness of 0.10 mm or 0.35 mm.
  • the final annealing of the cold-rolled steel sheet was carried out according to the conditions of Table 2 below under a hydrogen (H 2 ) gas atmosphere of 1 atm.
  • Example 1 steel grade cold rolled Way Final annealing conditions Electrical steel sheet thickness, mm Temperature (°C) hour Comparative Example 1 A 1st stage 1050 20 hours 0.15 Comparative Example 2 B 1st stage 1050 20 hours 0.15 Comparative Example 3 C 1st stage 1050 20 hours 0.15 Example 1 E 1st stage 1150 12 hours 0.10 Example 2 F 1st stage 1150 12 hours 0.10 Example 3 E 1st stage 1150 12 hours 0.15 Example 4 E 1st stage 1200 13 hours 0.10 Example 5 B 1st stage 1050 20 hours 0.10 Example 6 B 1st stage 1200 12 hours 0.35 Example 7 D 1st stage 1200 12 hours 0.50 Example 8 F 1st stage 1200 13 hours 0.10 Example 9 C 1st stage 1200 10 hours 0.15 Example 10 F 1st stage 1200 10 hours 0.15 Example 11 F 1st stage 1200 10 hours 0.35 Comparative Example 4 E 1st stage 1200 10 hours 0.35 Comparative Example 5 E 1st stage 1000 10 hours 0.10 Comparative Example 6 E 1st stage
  • Example 1 steel grade (001) grain area fraction, % iron loss, W 15/50 , Watts/kg magnetic flux density, B 50 , Tesla W 15/50 /thickness, Watts/kg/mm Average grain diameter, mm ⁇ Comparative Example 1 A 9 3.04 1.660 20.3 0.31 - Comparative Example 2 B 8 2.51 1.637 16.7 0.27 - Comparative Example 3 C 9 2.46 1.641 16.4 0.29 - Example 1 E 100 0.96 1.763 9.6 4.3 23.9
  • Example 2 F 97 0.74 1.772 7.4 0.85 20.6
  • Example 3 E 99 0.98 1.760 6.5 4.7 15.9
  • Example 4 E 98 0.92 1.763 9.2 0.61 23.2
  • Example 5 B 96 1.11 1.790 11.1 1.1 18.4
  • Example 6 B 90 1.66 1.800 4.7 12 12.6
  • Example 8 F 99 0.75 1.725 7.5 4.67 22.3
  • Example 9 C C 93 1.19 1.761
  • the steel grades B to F cold-rolled in one stage at an appropriate final annealing temperature exhibited a (001) area fraction of 70% or more and had excellent magnetic properties, and the magnetic properties obtained from the steel grades to which a large amount of Mn was added.
  • the iron loss was significantly lower than the magnetic characteristic obtained in Korean Patent Laid-Open No. 10-1842417.
  • the iron loss (W 15/50 ) to the steel plate thickness (mm) ratio showed a range of 3.2 to 11.1 Watts/kg/mm.
  • the angle ( ⁇ ) between the [100] crystal direction in the (001) texture and the rolling direction was in the range of 8.1 ⁇ ⁇ ⁇ ⁇ 23.2 ⁇ .
  • Example 5 using steel grade B having the same composition as Comparative Example 2, the decomposition of MnS precipitates was rapidly accelerated despite final annealing under the same conditions as performing one-stage cold rolling to a thickness of 0.10 mm (001)
  • the aspect ratio was as high as 96%
  • Example 6 the MnS precipitate was sufficiently decomposed by final annealing at a high temperature of 1200° C. of a cold-rolled steel sheet cold-rolled in one step to a thickness of 0.35 mm, resulting in a (001) aspect ratio of 90% , and thus, Examples 5 and 6 showed low iron loss and high magnetic flux density characteristics, unlike Comparative Example 2.
  • Example 9 using the C steel of the same composition as in Comparative Example 3, as the cold-rolled steel sheet was final annealed at a high temperature of 1200 ° C. As a result, it showed low iron loss and high magnetic flux density characteristics.
  • Comparative Example 4 using steel grade E of the same composition as Example 1, an electrical steel sheet was manufactured by one-stage cold rolling to 0.35 mm, so the surface fraction was extremely low, and thus the magnetic properties were poor.
  • Comparative Examples 5 and 6 using steel grade E of the same composition also exhibited poor magnetic properties due to an extremely low (001) area fraction.
  • This poor magnetic property is because, in the case of a low final annealing temperature, the MnS decomposition reaction by hydrogen in the hydrogen atmosphere is insignificant, and as a result, the MnS precipitates present inside the steel sheet extremely inhibited the growth of (001) grains, and In this case, it is difficult to completely decompose the MnS precipitates during the limited final annealing time because the MnS decomposition reaction time by hydrogen in the hydrogen atmosphere increases rapidly. It is presumed to be because
  • FIG. 5 shows the ⁇ 001 ⁇ 130> texture as an orientation distribution function (ODF) for the electrical steel sheet of Example 5, which was finally annealed after one-stage cold rolling.
  • ODF orientation distribution function
  • FIG. 6 is a view showing the azimuth distribution function with respect to FIG. 5 in the form of an etch fit.
  • the angle ( ⁇ ) between the [100] direction, which is the axis of easy magnetization, and the rolling direction is 18.4°.
  • the angle ( ⁇ ) observed in the one-stage rolled steel sheet shows various values depending on the steel sheet thickness.

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Abstract

Une feuille d'acier électrique selon la présente invention comprend, en % en poids, Si : de 2,0% à 4,0%, Mn : de 0,5 % (exclus) à 2,0 % (inclus), S : 0,01 % ou moins (à l'exclusion de 0 %), C : 0,01% ou moins (à l'exclusion de 0 %), N : 0,01 % ou moins (à l'exclusion de 0 %), et le reste étant du Fe et d'autres impuretés inévitables, la feuille d'acier électrique étant composée de (001) grains cristallins, satisfait à 6° ≤ θ ≤ 25°, qui est un angle (θ) entre la direction cristalline [100] dans la texture (001) indiquant la résistance de surface maximale et la direction de laminage, et a une épaisseur de 0,1 ㎜ ou plus par laminage à froid à une étape.
PCT/KR2021/013581 2021-05-03 2021-10-05 Feuille d'acier électrique à texture (001) et son procédé de fabrication WO2022234901A1 (fr)

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