WO2009091217A1 - Procédé de production de tôle magnétique non orientée - Google Patents

Procédé de production de tôle magnétique non orientée Download PDF

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Publication number
WO2009091217A1
WO2009091217A1 PCT/KR2009/000255 KR2009000255W WO2009091217A1 WO 2009091217 A1 WO2009091217 A1 WO 2009091217A1 KR 2009000255 W KR2009000255 W KR 2009000255W WO 2009091217 A1 WO2009091217 A1 WO 2009091217A1
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Prior art keywords
heat treatment
temperature
electrical steel
iron
plane
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PCT/KR2009/000255
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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
    • 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
    • C21D8/1244—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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • C21D9/561—Continuous furnaces for strip or wire with a controlled atmosphere or vacuum

Definitions

  • the present invention relates to a method for producing non-oriented electrical steel sheet, and more particularly, to a method for producing a non-oriented electrical steel sheet excellent in magnetic properties by having a high density ⁇ 100 ⁇ fiber texture.
  • soft magnetic materials of iron and iron-based alloys used in motors require two important magnetic properties.
  • the first is to have a low iron loss, the loss that occurs when the material is magnetized, and the second is to have a high magnetic flux density.
  • the atomic arrangement of the iron-based soft magnetic material must be maintained in a particular shape, and more specifically, the ⁇ 100 ⁇ plane of most of the particles constituting the plate must be arranged parallel to the plate plane, and the ⁇ 001> directions shall be evenly distributed in all directions of the plate. This is called ⁇ 100 ⁇ fiber texture or cube-on-face texture.
  • the reason why the ⁇ 100 ⁇ fiber texture improves the magnetic properties of the iron-based soft magnetic alloy is that the ⁇ 100 ⁇ plane does not have a ⁇ 111> direction, which is a magnetization difficulty direction, and two ⁇ 001> directions, which are easy magnetization directions. Because.
  • ⁇ 100 ⁇ cotton fiber aggregates have been formed by a method using surface energy (method using tertiary recrystallization) and direct casting.
  • the particles having the ⁇ 100 ⁇ plane formed on the surface grow and thus the atoms of the whole plate material.
  • the arrangement is identical to the atomic arrangement of the surface.
  • This method is not commercially viable as it requires a long heat treatment at a high temperature.
  • the ⁇ 100 ⁇ plane grows in the solidification direction, and as a result, the ⁇ 100 ⁇ fiber aggregate structure is formed by using the phenomenon in which the columnar crystal grains in which the ⁇ 100 ⁇ plane is parallel to the plate surface are formed. That's how. Plates produced using this method are not suitable for use as electrical steel sheets requiring uniform thickness and low surface roughness due to uneven thickness and rough surface.
  • the method for forming the ⁇ 100 ⁇ cotton fiber aggregate according to the prior art including the above-described method is inefficient in terms of process efficiency, and technically, various problems to be solved for commercial production are accumulated.
  • An object of the present invention is to provide a method for producing a non-oriented electrical steel sheet in which the atomic arrangement of most of the particles constituting the plate has a high density ⁇ 100 ⁇ fiber aggregate structure, the process efficiency is significantly improved.
  • Method for producing a non-oriented electrical steel sheet is a heat treatment step of heat-treating a metal plate made of iron or iron-based alloy under a stable temperature and a reducing gas atmosphere of the austenite phase ( ⁇ ), and the heat treated metal plate Phase transformation step of changing to the ferrite ( ⁇ ) phase.
  • the heat treatment is performed while reducing oxygen in at least one of the inner region and the surface region of the metal sheet or blocking the metal sheet from external oxygen to prevent surface oxidation of the metal sheet.
  • the heat treatment step may include adjusting the dew point of the reducing gas atmosphere before the heat treatment, thereby preventing the metal plate from being oxidized.
  • the reducing gas atmosphere include a hydrogen-containing gas atmosphere.
  • the heat treatment is performed in a section in which the dew point in the hydrogen-containing gas atmosphere is -20 ° C or lower.
  • the heat treatment is performed in a section where the dew point in the hydrogen-containing gas atmosphere is -45 °C or less.
  • the heat treatment may be performed within 20 minutes, and depending on conditions, may be performed within only a few minutes.
  • 1 is a graph showing the change of the surface strength according to the heat treatment temperature change when the pure iron plate heat treatment in a gas atmosphere of hydrogen containing 1 atm.
  • Figure 2 is a photograph showing the cross-sectional microstructure change of the pure iron plate according to the heat treatment temperature change when the heat treatment under the same conditions as in FIG.
  • FIG. 3 is a graph showing the change of texture according to the dew point change of hydrogen gas when the pure iron sheet is heat-treated for 5 minutes under a hydrogen-containing gas atmosphere at 1 atmosphere and at a temperature of 930 ° C.
  • FIG. 4 is a graph showing the change in texture according to the heat treatment time when the heat treatment is performed under a hydrogen-containing gas atmosphere having a dew point of ⁇ 60 ° C. and a temperature of 930 ° C.
  • FIG. 4 is a graph showing the change in texture according to the heat treatment time when the heat treatment is performed under a hydrogen-containing gas atmosphere having a dew point of ⁇ 60 ° C. and a temperature of 930 ° C.
  • FIG. 5 is a graph showing the change of texture according to the heat treatment temperature change when silicon steel (Fe-1.0% Si) is heat treated in a hydrogen-containing gas atmosphere at 1 atm.
  • FIG. 6 is a graph showing the change of texture according to the dew point change of hydrogen gas when silicon steel (Fe-1.0% Si) is heat-treated for 5 minutes under a hydrogen atmosphere containing 1 atm and at a temperature of 1030 ° C.
  • FIG. 6 is a graph showing the change of texture according to the dew point change of hydrogen gas when silicon steel (Fe-1.0% Si) is heat-treated for 5 minutes under a hydrogen atmosphere containing 1 atm and at a temperature of 1030 ° C.
  • FIG. 7 is a graph showing a change in texture according to the atmosphere replacement temperature when the heat treatment atmosphere gas is replaced with an oxidizing gas atmosphere in a reducing atmosphere.
  • the non-oriented electrical steel sheet according to the present invention has a high density ⁇ 100 ⁇ fiber aggregate parallel to the sheet surface.
  • the metal plate made of iron or an iron-based alloy should be subjected to a heat treatment and phase transformation step according to the present invention.
  • the heat treatment temperature may vary slightly depending on the composition of the metal sheet, but in general, the heat treatment temperature should be made in a stable temperature range of the austenite (austenite, ⁇ ) phase in the metal sheet.
  • 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 heat treatment step should be performed while reducing the oxygen of at least one region of the inner region and the surface region of the metal sheet material or blocking the metal sheet material from external oxygen, thereby preventing the surface of the metal sheet material from being oxidized.
  • a method for removing oxygen a method of removing oxygen atoms contained in a metal plate, a method of arranging oxygen adsorbents such as titanium (Ti) in a heat treatment furnace, a method of removing oxygen through control of a gas atmosphere, and an inside of a heat treatment atmosphere
  • the method of controlling the amount of moisture, and the method of treating the surface of the metal plate to prevent oxygen contact may be various.
  • the heat treatment process is preferably carried out under a reducing gas atmosphere so that the surface of the metal sheet is not oxidized.
  • the time for performing the heat treatment is only a few minutes to several tens of minutes is sufficient. More specifically, the heat treatment may be performed within about 20 minutes.
  • the heat treatment according to the present invention can be carried out under a reducing gas atmosphere, specifically, under a hydrogen-containing gas atmosphere.
  • a reducing gas atmosphere specifically, under a hydrogen-containing gas atmosphere.
  • a hydrogen-containing gas atmosphere When the heat treatment is performed under the hydrogen-containing gas atmosphere, a high density ⁇ 100 ⁇ plane strength may be secured to the metal sheet even without a separate means for removing or blocking oxygen.
  • the heat treatment is performed under a hydrogen-containing gas atmosphere, when moisture is present in the reducing atmosphere gas, oxygen may exist on the metal surface to be heat-treated while forming an equilibrium between the moisture and hydrogen. Therefore, if the dew point is high and the moisture in the atmosphere gas increases, this is equivalent to the increase in the partial pressure of oxygen in the atmosphere gas.
  • the dew point in the atmosphere gas should be controlled.
  • the heat treatment is performed under a hydrogen-containing gas atmosphere having a dew point of -20 ° C or lower.
  • the heat treatment is performed under a hydrogen-containing gas atmosphere having a dew point of -45 ° C or less. If the dew point is out of the dew point condition, the surface strength (surface index) of the ⁇ 100 ⁇ texture is sharply lowered.
  • the heat treated metal sheet is subjected to a phase transformation process from an austenite phase to a ferrite phase, thereby finally transforming into a metal sheet having a ⁇ 100 ⁇ fiber texture.
  • the particles having the ⁇ 100 ⁇ plane formed by the above-described method are columnar grains that vertically penetrate the metal sheet or columnar grains having an average particle size larger than half of the sheet thickness (semi-penetrating columnar grains). It will include at least a part.
  • the metal sheet has a grain structure characterized by ⁇ 100 ⁇ fiber aggregates parallel to the sheet surface through the heat treatment and phase transformation.
  • the strength of the ⁇ 100 ⁇ fiber aggregate formed can be significantly increased compared to conventional commercially available electrical steel sheet.
  • 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.
  • ⁇ 100 ⁇ ⁇ 0vw> orientation through particles having a high density of ⁇ 100 ⁇ ⁇ 0vw> orientation are formed in a very short time.
  • a dense ⁇ 100 ⁇ cotton fiber aggregate may be formed within a maximum of 30 minutes.
  • the formation of the ⁇ 100 ⁇ fiber aggregate structure means that particles having a ⁇ 100 ⁇ ⁇ 0vw> orientation parallel to the sheet surface are formed on the surface, and the particles formed on the surface grow inward. Changes are continuously developed by a single process.
  • 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.
  • N hkl multiplicity factor
  • I hkl X-ray intensity of the (hkl) plane.
  • I R, hkl X-ray intensity of the (hkl) plane of random specimens.
  • the P hkl means a roughly showing how many times the (hkl) plane exists in the target specimen compared to the (hkl) plane in the non-oriented random specimen.
  • the face index value is 20.33 when the ⁇ 100 ⁇ plane of all particles is parallel to the plate plane.
  • the present embodiment relates to an aggregate structure which appears when the pure iron sheet is heat treated in a hydrogen atmosphere.
  • the heat treatment of FIG. 1 was performed for 1 minute in a hydrogen gas atmosphere having a dew point temperature of -49 ° C.
  • the heat treatment was carried out as follows. First, the metal specimen was mounted in a sample boat at room temperature. When the heat treatment furnace reached 850 ° C. and the dew point of hydrogen gas reached the desired level, the specimen at room temperature was pushed into the center of the furnace. The specimen was held at 850 ° C. for 5 minutes to recrystallize on ferrite, and then heated to a desired temperature at a heating rate of 600 ° C./hr.
  • the specimen After the specimen reached the desired temperature and maintained for 1 minute, the specimen was cooled again at a cooling rate of 600 ° C./hr. When the temperature of the specimen reached 850 ° C., the specimen was removed into a chamber at room temperature, and the specimen was cooled to reach room temperature.
  • the ⁇ 111 ⁇ plane is formed relatively strongly when the ferrite phase is heat-treated in a stable temperature range (below 910 ° C.) after cold rolling of the pure iron sheet.
  • This phenomenon is a general phenomenon that is not significantly affected by the heat treatment atmosphere.
  • the pure iron was heat-treated in the temperature zone where the austenite phase was stable (above 910 ° C.)
  • the ⁇ 111 ⁇ plane was greatly weakened and the ⁇ 100 ⁇ plane was strongly formed at the same time.
  • the heat treatment was performed at 930 ° C., which is 20 ° C. higher than the phase transformation temperature, the ⁇ 100 ⁇ plane occupied about 90% or more of the entire surface.
  • Figure 2 is a photograph showing the cross-sectional microstructure change of the pure iron plate according to the heat treatment temperature change when the heat treatment under the same conditions as in FIG.
  • the heat treatment conditions were carried out at a heat treatment temperature of 930 °C and the heat treatment time was 5 minutes, the dew point was measured the dew point of the hydrogen gas passed through the heat treatment furnace.
  • the heat treatment furnace reached the desired heat treatment temperature and the dew point of hydrogen reached the desired value
  • the specimen at room temperature was pushed into the center of the furnace.
  • the specimen was held at 890 ° C. for 5 minutes to recrystallize on ferrite, and then the temperature of the specimen was controlled at a heating rate of 600 ° C./hr to 930 ° C.
  • the sample was then cooled again at a cooling rate of 600 ° C./hr after maintaining 5 minutes at 930 ° C.
  • the temperature of the specimen reached 850 ° C.
  • the specimen was removed into a chamber at room temperature, and the specimen was cooled to reach room temperature.
  • FIG. 3 is a graph showing the change of texture according to the dew point change of hydrogen gas when the pure iron sheet is heat-treated for 5 minutes under a 1 atmosphere of hydrogen-containing gas atmosphere and at a temperature of 930 ° C.
  • FIG. 3 is a graph showing the change of texture according to the dew point change of hydrogen gas when the pure iron sheet is heat-treated for 5 minutes under a 1 atmosphere of hydrogen-containing gas atmosphere and at a temperature of 930 ° C.
  • the strengthening of the ⁇ 100 ⁇ plane was found strongly in the dew point of hydrogen gas in the range of -55 to -20 ° C.
  • the ⁇ 100 ⁇ plane was weakened and the ⁇ 310 ⁇ plane was strengthened in a high purity hydrogen atmosphere having a very low moisture content.
  • the reason for this phenomenon is that in high-temperature, high-purity hydrogen, most of the oxygen, carbon, and other impurities present on the surface are removed, and hydrogen easily penetrates into iron, and these hydrogen atoms interfere with the movement of the grain boundary, thus causing the ⁇ 100 ⁇ plane to be removed. It is judged that the coarse grains having are hindered from growing. The reason for this reasoning lies in the change in the size of the particles that appear after the heat treatment.
  • the particle size of the inside of the plate was found to be 700 ⁇ m or more.
  • the average particle diameter of the plate was reduced to about 400 ⁇ m.
  • the inventors have found a way to integrate ⁇ 100 ⁇ planes at a high density while performing heat treatment in a hydrogen atmosphere with a low dew point (dew point ⁇ -58 ° C).
  • FIG. 4 is a graph showing texture changes with heat treatment time when heat treatment is performed under a hydrogen atmosphere having a dew point of ⁇ 60 ° C. and a temperature of 930 ° C.
  • FIG. 4 is a graph showing texture changes with heat treatment time when heat treatment is performed under a hydrogen atmosphere having a dew point of ⁇ 60 ° C. and a temperature of 930 ° C.
  • the iron plate was able to form a ⁇ 100 ⁇ plane with a high density when the heat treatment was performed for a short time, and the ⁇ 100 ⁇ plane was decreased as the heat treatment time was increased.
  • the reason why the high density ⁇ 100 ⁇ plane is formed in such a short time is that the surface of the metal plate is thin in oxygen to satisfy the ⁇ 100 ⁇ plane formation condition, and at the same time, the particles having the ⁇ 100 ⁇ plane of the surface grow rapidly. This is because there are not enough hydrogen atoms at the grain boundaries enough to.
  • the short heat treatment time reduces the process cost and at the same time extends the dew point temperature range in which the ⁇ 100 ⁇ fiber aggregate can be formed, which is very useful for producing iron-based alloy plates having high density ⁇ 100 ⁇ fiber aggregates. Can be.
  • the present embodiment relates to an aggregate structure that appears when heat treatment of silicon steel (Fe-1.0% Si) in a hydrogen atmosphere.
  • FIG. 5 is a graph showing the change of texture according to the heat treatment temperature change when the silicon steel (Fe-1.0% Si) is heat treated in a hydrogen atmosphere of 1 atm.
  • This heat treatment was carried out in a hydrogen gas atmosphere with a dew point temperature of -50 ° C.
  • the heat treatment was carried out as follows. First, the metal specimen was mounted in a sample boat at room temperature. When the heat treatment furnace reached 950 ° C. and the dew point of the hydrogen gas reached the desired level, the specimen at room temperature was pushed into the center of the furnace. The specimen was held at 950 ° C. for 5 minutes to recrystallize on ferrite and then the temperature of the specimen was adjusted at a heating rate of 600 ° C./hr to the desired temperature. After the specimen reached the desired temperature and held for 5 minutes, the specimen was cooled again at a cooling rate of 600 ° C./hr. When 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.
  • the ⁇ 111 ⁇ plane is formed relatively strongly when the ferrite phase is heat-treated in a stable temperature range (less than 970 ° C.) after cold rolling of silicon steel (Fe-1.0% Si).
  • This phenomenon is a general phenomenon that is not significantly affected by the heat treatment atmosphere.
  • Fe-1.0% Si was heat-treated in the temperature zone where the austenite phase was stable (more than 1000 ° C.)
  • the ⁇ 111 ⁇ plane was greatly weakened and the ⁇ 100 ⁇ plane was strongly formed at the same time.
  • FIG. 6 is a graph showing the change of texture according to the dew point change of hydrogen gas when silicon steel (Fe-1.0% Si) is heat-treated for 5 minutes under a hydrogen atmosphere containing 1 atm and at a temperature of 1030 ° C.
  • FIG. 6 is a graph showing the change of texture according to the dew point change of hydrogen gas when silicon steel (Fe-1.0% Si) is heat-treated for 5 minutes under a hydrogen atmosphere containing 1 atm and at a temperature of 1030 ° C.
  • the strengthening of the ⁇ 100 ⁇ plane was found to be strongly in the dew point of hydrogen below -50 °C.
  • the dew point was -50 ° C or higher, the ⁇ 100 ⁇ plane decreased while the ⁇ 111 ⁇ plane increased. This phenomenon occurs because of the oxidation of silicon generated in the hydrogen atmosphere.
  • the dew point of hydrogen which is a heat treatment gas, is higher than -50 ° C, it becomes a condition under which silicon in silicon steel (Fe-1.0% Si) can be oxidized at a given heat treatment temperature.
  • this dew point is closely related to the silicon content and the heat treatment temperature inside the silicon steel. In the case of silicon steel with a silicon content of less than 2.0%, the commonly applicable dew point is about -45 ° C or less.
  • the regulation of the dew point may be further relaxed.
  • the most important factor in the method of forming the ⁇ 100 ⁇ plane using phase transformation in iron and iron-based alloys is oxygen, which must be completely removed from oxygen in the heat treatment atmosphere, the iron-based alloy sheet, and the heat treatment system.
  • oxygen which must be completely removed from oxygen in the heat treatment atmosphere, the iron-based alloy sheet, and the heat treatment system.
  • an element having a high bonding force with oxygen such as silicon
  • the element having a high bonding force with oxygen also bonds with a small amount of oxygen present in the atmosphere.
  • the oxide film is formed on the surface of the iron alloy sheet, the inherent surface properties of the iron and iron-based alloys are lost.
  • high density ⁇ 100 ⁇ plane formation in iron and iron-based alloys is hindered.
  • the specimen used in this experiment was a sheet of Fe-1.0% Si composition with a thickness of 0.375 mm.
  • the heat treatment furnace reached 950 ° C
  • the specimen at room temperature was pushed into the center of the furnace.
  • 950 ° C is a temperature zone where the ferrite is stable, and the specimen is kept in ferrite for 5 minutes to completely recrystallize and then heated the specimen at a heating rate of 600 ° C / hr to 1010 ° C.
  • the Fe-1.0% Si alloy maintains a complete austenite phase above about 1000 ° C.
  • 1010 ° C is the zone where the austenite phase is stable.
  • the specimen was cooled again to a cooling rate of 600 ° C / hr to 900 ° C.
  • 900 °C the specimen was removed to the room temperature chamber and cooled to reach the temperature of the specimen.
  • the heat treatment gas was changed during the heat treatment to observe which phase the oxide film formed prevented the formation of the ⁇ 100 ⁇ plane.
  • the reducing atmosphere was a hydrogen atmosphere of 4.1 ⁇ 10 ⁇ 1 torr and the dew point of this gas was ⁇ 55.1 ° C.
  • the heat treatment is performed using the reducing atmosphere, the area occupied by the ⁇ 100 ⁇ fiber aggregate in the entire plate surface becomes 60% or more.
  • argon having 99.999% purity of 2.1 ⁇ 10 ⁇ 1 torr was used as an oxidizing atmosphere. Pure argon gas atmosphere is inert atmosphere, but the oxidation occurs weakly on the metal surface when heat treatment is performed in argon gas atmosphere of 99.999% purity.
  • This phenomenon occurs because of oxygen present as impurities in the argon gas. Therefore, this atmosphere was used as an oxidizing atmosphere.
  • the heat treatment atmosphere plays a very important role in forming the high density ⁇ 100 ⁇ plane. Therefore, in the initial stage of the heat treatment, a reducing atmosphere was used, and then, in a section in which a specific phase was stable, the oxidizing atmosphere gas was replaced, and the change in strength of the ⁇ 100 ⁇ plane at this time was observed. Analysis of these results can confirm which phase oxidation inhibits the ⁇ 100 ⁇ plane formation.
  • FIG. 7 is a graph showing a change in texture according to a temperature at which a heat treatment atmosphere gas is replaced with the oxidative atmosphere in the reducing atmosphere.
  • the formation of the oxide film at a given heat treatment temperature is determined by the activity of the oxidizing element present in the iron-based alloy and the partial pressure of oxygen present in the heat treatment atmosphere.
  • the amount of water contained in the hydrogen determines the oxygen partial pressure.
  • the phase transformation temperature changes according to the silicon content. As the silicon increases, the phase transformation temperature (heat treatment temperature) increases.
  • the oxygen partial pressure required for oxidation also changes according to the heat treatment temperature. As the heat treatment temperature increases, the oxygen partial pressure required for the oxidation increases.
  • the iron and iron-based alloy plate having a high density ⁇ 100 ⁇ fiber texture can be simply formed at a low temperature in a short time. Therefore, a highly efficient non-oriented electrical steel sheet can be manufactured using a very simple process, and the ⁇ 100 ⁇ ⁇ 0vw> forming method is completely 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.
  • non-oriented electrical steel sheet having excellent magnetic properties as well as ⁇ 100 ⁇ ⁇ 0vw> atoms in a short time at low temperature You can complete the array.
  • the non-oriented electrical steel sheet production method and the non-oriented electrical steel sheet described above may provide a very innovative technology to the electrical steel sheet industry, the ripple effect of the present invention is expected to be infinite.

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Abstract

La présente invention concerne un procédé de production de tôle magnétique non orientée, qui comprend : une étape de traitement thermique permettant de traiter thermiquement un matériau métallique en tôle fabriqué à partir de fer ou d'un alliage à base de fer à une température à laquelle la phase austénitique (g) est stable et sous une atmosphère gazeuse réduite, en empêchant l'oxydation de surface de ce matériau métallique en tôle et, une étape de transformation de phase destinée à transformer le métal en tôle traité thermiquement vers la phase ferritique (a). Par le réglage du point de rosée dans l'atmosphère gazeuse réduite, on peut produire une tôle magnétique non orientée avec une résistance à la flexion et à la torsion plane (100) nettement supérieure.
PCT/KR2009/000255 2008-01-16 2009-01-16 Procédé de production de tôle magnétique non orientée WO2009091217A1 (fr)

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KR10-2008-0004999 2008-01-16
KR1020080004999A KR20090079057A (ko) 2008-01-16 2008-01-16 무방향성 전기강판의 제조방법

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WO2016003245A1 (fr) * 2014-07-04 2016-01-07 한양대학교에리카산학협력단 Procédé de formage de tôle d'acier, équipement de formage et produit formé
KR102371572B1 (ko) * 2021-06-24 2022-03-07 서울대학교산학협력단 확산을 이용한 큐브 온 페이스 텍스쳐 제조방법 및 이를 통해 제조된 전기강판

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