WO2009091213A1 - Procédé de formation pour texture cubique orientée, et feuille d'acier électrique ainsi produite - Google Patents

Procédé de formation pour texture cubique orientée, et feuille d'acier électrique ainsi produite Download PDF

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Publication number
WO2009091213A1
WO2009091213A1 PCT/KR2009/000246 KR2009000246W WO2009091213A1 WO 2009091213 A1 WO2009091213 A1 WO 2009091213A1 KR 2009000246 W KR2009000246 W KR 2009000246W WO 2009091213 A1 WO2009091213 A1 WO 2009091213A1
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Prior art keywords
heat treatment
texture
iron
electrical steel
steel sheet
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PCT/KR2009/000246
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English (en)
Korean (ko)
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Jin Kyung Sung
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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
    • 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
    • C21D8/1233—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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/05—Grain orientation
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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

Definitions

  • the present invention relates to a method for forming a ⁇ 100 ⁇ ⁇ 011> texture on a metal sheet and an electrical steel sheet manufactured using the same in iron and iron-based alloys. More specifically, the ⁇ 100 ⁇ plane is parallel to the sheet surface and is ⁇
  • the present invention relates to a manufacturing method capable of manufacturing an electrical steel sheet having a high density of texture parallel to the rolling direction in a high efficiency and a simple process, and an electrical steel sheet manufactured using the same.
  • electrical steel sheets used in transformers and the like are required to exhibit excellent magnetic properties only in a specific direction.
  • the soft magnetic material of iron and iron-based alloys used in such transformers, etc. can be optimized by the atomic arrangement of the particles constituting the plate directional in a specific direction.
  • the ⁇ 001> direction is a magnetization direction that appears in iron and iron-based alloys. If the ⁇ 001> direction is aligned in a specific direction of the plate by controlling the atomic arrangement of the particles in the plate, the plate is very specific in the specific direction. It can be magnetized efficiently.
  • the manufacturing process of the grain-oriented electrical steel sheet currently produced in steel mills is a process using an inhibitor (MnS, AlN, etc.).
  • the grain-oriented electrical steel sheet using the inhibitor is very complicated and difficult to manufacture.
  • the first of these difficulties is that the temperature for reheating the slab before the hot rolling is too high. That is, the process has a problem that the oxidation is severely generated in the slab because the reheating temperature should be 1300 °C or more, and there is a problem that the energy cost is very high because of the high temperature reheating temperature.
  • a low temperature reheating method has been developed, and the above-mentioned problems have been largely solved.
  • a bigger problem, however, lies in the secondary recrystallization process of growing a so-called goth particle.
  • the secondary recrystallization process includes a heating condition of about 1200 ° C., and requires a heat treatment time of about 70 hours or more.
  • An object of the present invention is to overcome the problems and limitations of the prior art as described above, the ⁇ 100 ⁇ ⁇ 011> texture in which the high density ⁇ 100 ⁇ ⁇ 001> texture is rotated 45 ° with respect to the rolling direction It is to provide a method for forming an electrical steel sheet having a simple method in a significantly reduced time.
  • Another object of the present invention is to provide an electrical steel sheet having an orientation exhibiting excellent magnetic properties in the direction of ⁇ 45 ° with respect to the rolling direction by using the above method.
  • the method for forming the ⁇ 100 ⁇ ⁇ 011> texture is based on a metal plate made of ⁇ 100 ⁇ texture including the columnar columnar particles and composed of iron or an iron-based alloy.
  • the metal sheet In order to form the ⁇ 100 ⁇ texture on the metal sheet, the metal sheet should be cold rolled at a rolling reduction of 10 to 50%, and then subjected to a second heat treatment at a temperature at which the ferrite phase ⁇ is stable.
  • Metal plate made of ⁇ 100 ⁇ texture including the columnar columnar particles can be produced by various methods, according to the present invention i) a plate made of iron or iron-based alloy under a stable temperature of the austenite phase ( ⁇ ) A first heat treatment step of heat treatment while preventing oxidation of the surface of the plate; And ii) it can be prepared by the phase transformation step of changing the heat-treated metal plate into a ferrite ( ⁇ ) phase.
  • the present invention is not limited to the manufacturing method of the metal plate which consists of the ⁇ 100 ⁇ texture containing the said columnar columnar particle
  • the phase transformation step may be performed by cooling the heat treated metal plate from an austenite phase stabilization temperature.
  • the second heat treatment may be performed under an inert atmosphere and preferably a reducing atmosphere including hydrogen, but is not limited thereto.
  • the second heat treatment is performed under 650 to 950 ° C. In addition, the second heat treatment is performed for a time of 3 hours or less.
  • the electrical steel sheet according to another aspect of the present invention is manufactured by the above-described method, made of iron or iron-based alloy plate material and has a ⁇ 100 ⁇ plane parallel to the plate surface and a direction parallel to the rolling direction.
  • the electrical steel sheet is formed vertically so that at least some of the crystal grains having ⁇ 100 ⁇ parallel to the sheet surface penetrate the sheet, and have a rotated cube ( ⁇ 100) of at least 25%.
  • ⁇ ⁇ 011>) includes an organization.
  • 1 is a graph showing the change in volume fraction of ⁇ 100 ⁇ fiber texture according to the reduction ratio when cold-rolled specimens subjected to the first heat treatment after stress relief heat treatment (tolerance error: 15 °).
  • Figure 4 is a graph showing the volume fraction of the through-type particles according to the thickness of the specimen when the first heat treatment in the Fe-1.0% Si alloy specimen.
  • FIG. 6 shows a cube ( ⁇ 100) exhibited in a specimen subjected to a first heat treatment on a Fe-1.0% Si alloy specimen and subjected to cold rolling at a constant reduction ratio, followed by a second heat treatment for one hour at a temperature of 800 ° C. and a nitrogen atmosphere.
  • ⁇ ⁇ 011> A graph showing the volume fraction of the aggregates (tolerance: 15 °).
  • FIG. 8 is a ⁇ 100 ⁇ texture forming heat treatment on a Fe-1.0% Si steel plate having a thickness of 550 ⁇ m, followed by cold rolling at a reduction ratio of 25%, and then a stress relief heat treatment for 10 minutes at 800 ° C. in a nitrogen atmosphere. It is a photograph showing the cross-sectional microstructure of the specimen.
  • the ⁇ 100 ⁇ plane is parallel to the plate surface and the ⁇ 011> direction is parallel to the rolling direction.
  • the above-described aggregate structure having the atomic arrangement of ⁇ 100 ⁇ ⁇ 011> has a ⁇ 011> direction in the rolling direction, but has a ⁇ 001> direction in the left and right 45 ° directions of the rolling direction. Therefore, the electrical steel sheet having such characteristics can be used as an electrical steel sheet having excellent directionality using a direction that becomes 45 ° to the rolling direction as the magnetization direction.
  • the present invention provides a method that can produce an electrical steel sheet having the above-described ⁇ 100 ⁇ ⁇ 011> texture with a breakthrough efficiency.
  • the metal sheet should have a predetermined characteristic in advance.
  • the metal plate for applying the method of forming the ⁇ 100 ⁇ ⁇ 011> texture according to the present invention should be composed of the ⁇ 100 ⁇ texture including the columnar columnar particles.
  • the method of forming the ⁇ 100 ⁇ texture having the above characteristics on the metal sheet is different, the method of forming the ⁇ 100 ⁇ texture according to the present invention can be effectively applied to the metal sheet having the above characteristics. have.
  • the metal plate made of iron or an iron-based alloy is subjected to the first heat treatment and phase transformation step according to the present invention, thereby providing a high density ⁇ 100 ⁇ to produce a metal sheet having a texture.
  • the first heat treatment temperature may vary slightly depending on the composition of the metal sheet, but in general, the first heat treatment temperature should be made in a stable temperature range of the austenite phase in the metal sheet to be heat treated.
  • the austenite phase ( ⁇ ) refers to a state in which an atomic array structure of iron or iron alloy forms a face-centered cubic lattice.
  • the ferrite phase (ferrite, ⁇ ) refers to a state in which the atomic arrangement structure of iron or iron alloy forms a body-centered cubic lattice.
  • iron and iron alloys are stable in the ferrite phase at room temperature, but when the temperature increases, the phase transformation process in which the austenite phase is transformed into a stable region via the region where the ferrite phase and the austenite phase coexist. That is, the first heat treatment is performed in a temperature section corresponding to the austenitic phase region described above.
  • the temperature range corresponding to the stable region of the austenite phase is variable depending on the type and content of the component elements included in the metal sheet.
  • the first heat treatment step should be performed while reducing oxygen in at least one region of the inner region and the surface region of the metal sheet or blocking the metal sheet from the external oxygen.
  • it is very important to block the contact between the metal to be heat treated and oxygen.
  • a method for removing oxygen a method of disposing an oxygen adsorbent such as titanium (Ti) in a heat treatment furnace, a method of removing oxygen atoms contained in a metal sheet, a method of removing oxygen through gas atmosphere control, and preventing oxygen contact
  • an oxygen adsorbent such as titanium (Ti)
  • a method of removing oxygen atoms contained in a metal sheet a method of removing oxygen through gas atmosphere control, and preventing oxygen contact
  • a method of controlling the amount of water present in the heat treatment atmosphere may be varied.
  • the heat treatment step is preferably carried out under a reducing gas atmosphere and a substantially vacuum atmosphere so that the surface of the metal sheet is not oxidized.
  • the time for performing the first heat treatment is sufficient for only a few minutes to several tens of minutes. More specifically, the heat treatment may be performed within about 20 minutes.
  • the first heat-treated metal sheet may be manufactured into an electrical steel sheet having a ⁇ 100 ⁇ texture by undergoing a phase transformation process from an austenite phase to a ferrite phase.
  • the particles whose ⁇ 100 ⁇ planes are parallel to the plate plane include at least a portion of columnar grain tissue that vertically penetrates through the metal plate.
  • the metal plate has a grain structure in which the ⁇ 100 ⁇ plane parallel to the plate plane is parallel to the plate plane through the heat treatment and phase transformation.
  • the strength of the ⁇ 100 ⁇ texture formed can be significantly increased compared to conventional commercially available electrical steel sheet. That is, the ⁇ 100 ⁇ texture is determined by heat treatment and phase transformation, and the orientation of the electrical steel sheet is not determined by the heat treatment and phase transformation.
  • the phase transformation may be achieved by cooling the heat treated metal sheet from the austenite phase stabilization temperature to the ferrite phase stabilization temperature.
  • the phase transformation may be performed by adding a change to the internal composition of the heat-treated metal sheet in the absence of temperature change.
  • a dense ⁇ 100 ⁇ texture is formed in a very short time. Specifically, a dense ⁇ 100 ⁇ texture may be formed within a maximum of 30 minutes.
  • Formation of the ⁇ 100 ⁇ texture means that particles having a ⁇ 100 ⁇ plane parallel to the surface of the plate are formed on the surface, and the particles formed on the surface are grown in the present invention. By successive deployment.
  • a metal plate material having a dense ⁇ 100 ⁇ texture and having at least some tissues penetrating the plate surface may be formed, and the present invention is completed on the premise of preparing the metal plate. Can be.
  • the metal sheet material up to this step has a specific orientation, and in order to arrange the generated ⁇ 100 ⁇ texture in the ⁇ 100 ⁇ ⁇ 011> orientation as intended in the present invention, the following process must be performed.
  • the metal plate having the ⁇ 100 ⁇ texture In order to change the metal plate having the ⁇ 100 ⁇ texture into a plate having the ⁇ 100 ⁇ ⁇ 011> orientation, the metal plate having the ⁇ 100 ⁇ texture must be cold rolled under a controlled rolling reduction rate.
  • the control of the reduction ratio is a very important variable for imparting directivity.
  • the cold rolling may be slightly different depending on the cold rolling apparatus and the method characteristics (roll size, surface roughness of the roll, one-time rolling rate, etc.) and the metal sheet composition or thickness, but 10 to 50 It should be made under% reduction rate.
  • the reduction ratio is less than 10%, the formation of ⁇ 100 ⁇ ⁇ 011> aggregates is weak, whereas if the reduction ratio exceeds 50%, the ⁇ 100 ⁇ ⁇ 011> aggregates disappear.
  • the cold rolled metal sheet is subjected to a second heat treatment under a temperature at which the ferrite ⁇ is stable for removing residual stress.
  • the second heat treatment for removing the residual stress should be performed at a temperature below the temperature of ⁇ ⁇ ⁇ phase transformation so as not to cause a change in the ⁇ 100 ⁇ texture formed.
  • the temperature of the second heat treatment is slightly different depending on the components of the metal sheet, but is generally made under 650 to 950 ° C, and is sufficient for approximately 3 hours or less.
  • an electrical steel sheet having an aggregate structure according to the present invention may be manufactured.
  • an electrical steel sheet having a ⁇ 100 ⁇ ⁇ 011> texture can be manufactured with excellent process efficiency within a significantly reduced time.
  • the electrical steel sheet manufactured as described above includes iron or an iron-based alloy, and preferably includes iron containing silicon (Si).
  • the electrical steel sheet may include various metal elements for improving physical properties and processing efficiency of the electrical steel sheet.
  • the electrical steel sheet according to the present invention is composed of an aggregated structure (rotated cube texture) having a ⁇ 100 ⁇ plane parallel to the plate surface and a direction parallel to the rolling direction.
  • the manufactured electrical steel sheet contains at least a portion of ⁇ 100 ⁇ columnar particles whose grain structure vertically penetrates the sheet, and most of the formed particles have a structure having large particles having a particle size of 0.2 to 3 mm.
  • At least 25% or more of the electrical steel sheet has a ⁇ 100 ⁇ ⁇ 011> texture.
  • Table 1 shows the chemical composition of the specimen used in the present invention.
  • the specimen has a plate shape and the plate is cast into an ingot through a vacuum induction melting process, and the ingot is hot rolled to prepare a hot rolled sheet having a thickness of 2 mm, and then cold rolled into a cold rolled sheet having various thicknesses. Was prepared.
  • the trace amounts of the components listed in Table 1 are not the elements added intentionally, and the content thereof is the content of the impurity level existing in the original alloy, which will have little effect on the technical spirit of the present invention.
  • the microstructure is characterized in that most of the particles have a columnar structure and the texture of the texture is ⁇ 100 ⁇ It becomes the board
  • the ⁇ 100 ⁇ texture formation heat treatment is as described above, but to explain again, first, the metal plate of the iron and iron-based alloy should be heat treated under a stable temperature of the austenite phase.
  • the phase transformation of the heat-treated iron or iron-based alloy to the ferrite ( ⁇ ) phase it is possible to form a predetermined texture on the plate.
  • the metal plate is heat-treated under a temperature at which the austenite phase is stable, while blocking the metal plate from external oxygen.
  • particles having ⁇ 100 ⁇ ⁇ 0vw> parallel to the sheet surface of the metal sheet can be formed at a high density.
  • ⁇ 100 ⁇ ⁇ 001> aggregates may be formed.
  • ODF orientation distribution function
  • This embodiment is to present a cold reduction rate for forming the ⁇ 100 ⁇ texture in the rolling direction when cold rolling is performed after the heat treatment (first heat treatment) for forming the ⁇ 100 ⁇ plane.
  • the specimen used in this experiment was a sheet of Fe-1.0% Si composition with an initial thickness of 0.5 mm.
  • heat treatment was performed under the following conditions.
  • Heat treatment to form the ⁇ 100 ⁇ plane was carried out under a hydrogen atmosphere of 4.1x10 -1 torr.
  • the heat treatment furnace reached 900 ° C
  • the specimen at room temperature was pushed into the center of the furnace.
  • 900 °C is a temperature zone where the ferrite is stable
  • the specimen was kept on ferrite for 10 minutes to completely recrystallize and then heated the specimen at a heating rate of 400 °C / hr to 1050 °C.
  • the Fe-1.0% Si alloy maintains a complete austenite phase above about 1000 ° C.
  • 1050 ° C is the zone where the austenite phase is stable.
  • the specimen was cooled to a cooling rate of 400 °C / hr up to 900 °C.
  • the temperature of the specimen reached 900 °C the specimen was removed to the room temperature chamber and cooled to reach the temperature of the specimen.
  • most of the particles were columnar tablets and the volume fraction of the ⁇ 100 ⁇ fiber texture was about 80%.
  • Rolling was carried out at various reduction ratios on the specimens on which high density ⁇ 100 ⁇ fiber aggregates were formed. The rolled plate was subjected to heat treatment for 1 hour under an argon + 30% hydrogen mixed gas atmosphere and a temperature of 800 ° C. to remove residual stress.
  • 1 is a graph showing the volume fraction change of ⁇ 100 ⁇ fiber texture according to the reduction ratio when the residual stress removal heat treatment is performed after cold rolling the specimen subjected to the first heat treatment.
  • the iron and iron-based alloy sheet composed of ⁇ 100 ⁇ texture including penetrating columnar particles showed that ⁇ 100 ⁇ plane was formed on the sheet even when cold rolling and residual stress heat treatment of less than 50% were performed.
  • the data are shown, it is not known whether the sheet has a directivity. Since the present invention is a technique for a material used for oriented electrical steel sheet, the most preferable texture is to arrange the ⁇ 001> direction in a specific direction. Therefore, the analysis of the orientation distribution function analyzed the formation of direction according to the reduction ratio. Specimens subjected to azimuth distribution analysis are the same specimens used for surface strength analysis according to the reduction ratio.
  • the ⁇ 100 ⁇ ⁇ 011> texture formed after the residual stress removal heat treatment is performed, and looks at the effect of the characteristics of the microstructure on the formation of the ⁇ 100 ⁇ ⁇ 011> texture.
  • Figure 4 is a graph showing the volume fraction of the through-type particles according to the thickness of the specimen when the first heat treatment in the Fe-1.0% Si alloy specimen.
  • Heat treatment for forming the ⁇ 100 ⁇ plane was performed in the same manner as in Example 1. Referring to Figure 4, it was shown that the thickness change of the metal plate has a close relationship with the through-type particles. In other words, as the thickness of the plate becomes thinner, most of the particles have through-type particles, and as the thickness increases, the semi-penetrating particles increase.
  • FIG 5 is a graph showing a change in the volume fraction of the ⁇ 100 ⁇ fiber texture according to the thickness change in the specimen subjected to the first heat treatment (tolerance error: 15 °).
  • the ⁇ 100 ⁇ ⁇ 011> texture was formed using specimens having different volume fractions. That is, when the first heat treatment is performed on Fe-1.0% Si alloy plates having different thicknesses, the volume fraction of the through particles increases as the thickness decreases.
  • the specimen was subjected to cold rolling, and subjected to residual stress relief heat treatment for 1 hour in an atmosphere of nitrogen at 800 ° C., thereby measuring the volume fraction of the ⁇ 100 ⁇ texture shown therein.
  • the result is that if the silicon steel has penetrating particles and the ⁇ 001> direction of the particles is perpendicular to the sheet surface ( ⁇ 100 ⁇ ⁇ 0vw>), the sheet is appropriately rolled and heat treated to achieve ⁇ 100 ⁇ ⁇ 011> is very easy to form.
  • the reason for this phenomenon is that, when rolling the plate material characterized by the through-type particles in which the ⁇ 001> direction is perpendicular to the plate surface, the through-type particles in which the ⁇ 001> direction is perpendicular to the plate surface have a direction of ⁇ 100. ⁇ Because it rotates to ⁇ 011>.
  • FIG. 7 is a ⁇ 110 ⁇ pole figure measured on a specimen subjected to cold rolling at a reduction ratio of 25% after a heat treatment of ⁇ 100 ⁇ texture formation on a Fe-1.0% Si steel sheet having a thickness of 550 ⁇ m.
  • particles having a ⁇ 100 ⁇ fiber texture formed during the ⁇ 100 ⁇ texture formation heat treatment rotated to particles having a ⁇ 100 ⁇ ⁇ 011> orientation upon further cold rolling. Is showing.
  • the residual stress removal heat treatment is performed on the specimen, it is determined that the residual stress is removed while maintaining the ⁇ 100 ⁇ ⁇ 011> texture formed during cold rolling.
  • the heat treatment is preferably performed in the temperature range of 650 ⁇ 950 °C and the heat treatment time is completed within 3 hours. In selecting the heat treatment temperature, care should be taken in the temperature zone where the ferrite ⁇ is stable.
  • the heat treatment is performed in an austenite single phase zone or an austenite ferrite abnormal zone, the ⁇ 100 ⁇ ⁇ 011> texture disappears.
  • the heat treatment time is sufficient to remove the residual stress, heat treatment conditions within 3 hours are sufficient. More preferably it is economically more advantageous to carry out the heat treatment within about 15 minutes.
  • the ratio of through-hole particles is low and there are many particles whose ⁇ 100 ⁇ planes are not parallel to the plate plane, these particles are selectively recrystallized easily from these particles when subjected to stress relief heat treatment after cold rolling. As it occurs, it grows at the expense of particles with a ⁇ 100 ⁇ ⁇ 011> orientation formed around it.
  • FIG. 8 is a photograph showing the cross-sectional microstructure of the specimen subjected to the stress relief heat treatment for 10 minutes in the specimen used in the experiment of Figure 7 at 800 °C nitrogen atmosphere.
  • a plate having a rolling-type particle having a ⁇ 001> direction perpendicular to the sheet surface with a rolling reduction rate of 25% even though the heat-treating is performed at 800 ° C., many of the through-particles remain as it is. Demonstrates maintaining shape.
  • a general recrystallization phenomenon occurs in which new particles nucleate and grow. These new particles grow at the expense of particles with the ⁇ 100 ⁇ ⁇ 011> texture formed during cold rolling. When this phenomenon occurs, the ⁇ 100 ⁇ ⁇ 011> aggregate is weakened.
  • the method for producing a grain-oriented electrical steel sheet according to the present invention it is possible to simply form a high density ⁇ 100 ⁇ ⁇ 011> texture parallel to the rolling direction in a short time, and thus in a direction of ⁇ 45 ° to the rolling direction. It is easy to obtain an electrical steel sheet having excellent magnetic properties.
  • the method for forming the ⁇ 100 ⁇ ⁇ 011> aggregated tissue presented in the present invention is perfectly reproducible and is very easy for mass production.
  • the method is not only applied locally to a plate of a specific composition, but can be applied universally, and its utilization is very high.

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Abstract

La présente invention concerne un procédé de formation {100} d'une texture utilisé dans le traitement d'un matériau métallique en feuille possédant {100} une texture qui comprend des grains cristallins columnaires pénétrants et qui est constituée de fer ou d'un alliage à base de fer. Selon l'invention, le matériau métallique en feuille est laminé à froid à un rapport de réduction compris entre 10 et 50% et, puis, il est soumis à un traitement thermique secondaire à une certaine température, à laquelle la phase ferritique (a) est stable de sorte qu'une {100} texture ayant un {100} plan parallèle au plan du matériau métallique en feuille et une orientation parallèle à la direction du laminage est formée dans le matériau métallique en feuille.
PCT/KR2009/000246 2008-01-16 2009-01-16 Procédé de formation pour texture cubique orientée, et feuille d'acier électrique ainsi produite WO2009091213A1 (fr)

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KR1020080004997A KR100973406B1 (ko) 2008-01-16 2008-01-16 로테이티드 큐브 집합조직의 형성방법 및 이를 이용하여제조된 전기강판
KR10-2008-0004997 2008-01-16

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JP6844127B2 (ja) * 2016-06-16 2021-03-17 日本製鉄株式会社 鉄心、再冷延鋼板、鉄心用積層体、再冷延鋼板の製造方法、鉄心用積層体の製造方法、及び鉄心の製造方法
KR102283217B1 (ko) 2020-12-16 2021-07-29 주식회사 썸백 100 집합조직으로 구성된 전기강판 및 그의 제조방법
KR102283225B1 (ko) 2021-05-03 2021-07-29 주식회사 썸백 (001) 집합조직으로 구성된 전기강판 및 그의 제조방법
KR102283222B1 (ko) 2021-05-03 2021-07-29 주식회사 썸백 (001) 집합조직으로 구성된 전기강판 및 그의 제조방법
KR102376026B1 (ko) 2021-07-21 2022-03-23 주식회사 썸백 (001) 집합조직으로 구성된 전기강판 및 그의 제조방법
KR102417226B1 (ko) 2022-02-14 2022-07-06 주식회사 썸백 (001) 집합조직으로 구성된 전기강판 및 그의 제조방법

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JPH05279740A (ja) * 1992-03-31 1993-10-26 Nippon Steel Corp 磁気特性が極めて優れた高珪素無方向性電磁鋼板の製造方法
JPH06306467A (ja) * 1993-04-22 1994-11-01 Nippon Steel Corp 磁気特性が極めて優れた無方向性電磁鋼板の製造方法
US5913987A (en) * 1996-12-13 1999-06-22 Pohang Iron & Steel Co., Ltd. Finish treatment method and silicon steel sheet manufactured by direct casting method
KR20060055602A (ko) * 2004-11-18 2006-05-24 현대자동차주식회사 알루미늄-마그네슘-실리콘 합금 판재의 헤밍 이방성 저감방법

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KR100797895B1 (ko) 2006-12-22 2008-01-24 성진경 표면 (100) 면 형성 방법, 이를 이용한 무방향성 전기강판의 제조 방법 및 이를 이용하여 제조된 무방향성 전기강판

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Publication number Priority date Publication date Assignee Title
JPH05279740A (ja) * 1992-03-31 1993-10-26 Nippon Steel Corp 磁気特性が極めて優れた高珪素無方向性電磁鋼板の製造方法
JPH06306467A (ja) * 1993-04-22 1994-11-01 Nippon Steel Corp 磁気特性が極めて優れた無方向性電磁鋼板の製造方法
US5913987A (en) * 1996-12-13 1999-06-22 Pohang Iron & Steel Co., Ltd. Finish treatment method and silicon steel sheet manufactured by direct casting method
KR20060055602A (ko) * 2004-11-18 2006-05-24 현대자동차주식회사 알루미늄-마그네슘-실리콘 합금 판재의 헤밍 이방성 저감방법

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