KR100973406B1 - Method of forming rotated cube texture at metal sheets and electrical steel sheets manufactured by using the same - Google Patents

Method of forming rotated cube texture at metal sheets and electrical steel sheets manufactured by using the same Download PDF

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KR100973406B1
KR100973406B1 KR1020080004997A KR20080004997A KR100973406B1 KR 100973406 B1 KR100973406 B1 KR 100973406B1 KR 1020080004997 A KR1020080004997 A KR 1020080004997A KR 20080004997 A KR20080004997 A KR 20080004997A KR 100973406 B1 KR100973406 B1 KR 100973406B1
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heat treatment
texture
iron
electrical steel
plate
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KR1020080004997A
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Korean (ko)
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KR20090079055A (en
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성진경
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성진경
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    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216Modifying 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
    • C21D8/1233Cold rolling
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244Modifying 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
    • C21D8/1272Final recrystallisation annealing
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D2201/00Treatment for obtaining particular effects
    • C21D2201/05Grain orientation
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D9/00Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals

Abstract

The present invention is made of a {100} texture including the columnar columnar particles, and in processing a metal sheet composed of iron or an iron-based alloy, the metal sheet is cold-rolled at a rolling reduction of 10 to 50% {100} <011> having a {100} plane parallel to the metal plate surface and a <011> direction parallel to the rolling direction by performing a second heat treatment at a stable temperature after the rolling of the ferrite phase α Provided is a method for forming an aggregated structure for forming an aggregated structure.

Electrical steel, rolling reduction, texture, {100} <011>

Description

Method of forming rotated cube texture at metal sheets and electrical steel sheets manufactured by using the same

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.

In general, 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.

This phenomenon occurs because iron and iron-based soft magnetic alloys are magnetically anisotropic. In other words, 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 phenomenon of magnetic anisotropy in iron and iron-based alloys has been known since the 1930s. Goss proposed a method of controlling an atomic arrangement called a goth texture, which is characterized by the fact that the {110} plane of the particles constituting the plate is parallel to the plate surface and the <001> direction is rolled. Is parallel to the direction. That is, by developing a method of arranging particles having a {110} <001> orientation in a rolling direction, the technology has been developed for the last 70 years and is currently sold under the name of oriented electrical steel sheet.

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 ℃ or more, and there is a problem that the energy cost is very high because of the high temperature reheating temperature. In order to overcome this problem, 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.

Thus, since the process of manufacturing a grain-oriented electrical steel sheet requires a long time at a high temperature, the grain-oriented electrical steel sheet is very expensive and the manufacturing equipment is very complicated.

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 according to an aspect of the present invention is based on a metal plate made of {100} texture including the columnar columnar particles and composed of iron or an iron-based alloy. In order to form the {100} texture on the metal sheet, the metal sheet is cold rolled at a rolling reduction of 10 to 50%, and then the second heat treatment is performed under a temperature at which the ferrite phase (a) is stable. It must be done.

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 (γ) 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 (α) 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 | grains.

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.

Hereinafter, the present invention will be described in detail.

In the electrical steel sheet according to the present invention, 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.

In order to form the above-described {100} <011> texture on the metal sheet, 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.

Even if 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.

Hereinafter will be described a method according to an embodiment of the present invention for preparing a metal plate consisting of {100} texture including the columnar columnar particles.

In order to prepare a metal plate made of {100} texture including the columnar columnar particles, 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 (γ) refers to a state in which an atomic array structure of iron or iron alloy forms a face-centered cubic lattice. In addition, the ferrite phase (ferrite, α) refers to a state in which the atomic arrangement structure of iron or iron alloy forms a body-centered cubic lattice. In general, iron and iron alloys are stable at room temperature, but the ferrite phase is stable, but when the temperature increases, the ferrite phase and the austenite phase undergo a phase transformation process in which only the austenite phase is transformed into a stable region. 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.

In addition, 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. In the present invention, it is very important to block the contact between the metal to be heat treated and oxygen.

As 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 In order to treat the surface of the metal plate material, a method of controlling the amount of water present in the heat treatment atmosphere may be varied. In particular, 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.

In addition, 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.

In summary, 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. In particular, 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. Alternatively, 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.

According to the present invention, 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.

In addition, this change is substantially made in a very short time, the process of the present invention compared to the prior art of producing a grain-oriented electrical steel sheet, which took several hours to several tens of hours is a breakthrough in process efficiency.

By the above-described initial process, 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.

It is difficult to say that 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.

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.

In the present invention, the control of the reduction ratio is a very important variable for imparting directivity. In the present invention, 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.

If 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 α 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 α → γ phase transformation so as not to cause a change in the already formed {100} texture.

Specifically, 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.

When the cold rolling for directional formation and the second heat treatment for removing residual stress are completed, an electrical steel sheet having an aggregate structure according to the present invention may be manufactured. According to the present invention, 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). In addition, 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.

In addition, 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. Have

At least 25% or more of the electrical steel sheet has a {100} <011> texture.

Hereinafter, the present invention will be described in more detail with reference to specific examples. [Example]

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.

alloy Fe Si Mn Al C Ni S Fe-1.0% Si Bal 0.97 - 0.0016 0.0024 0.0041 0.0013

Cold rolled plate is applied to the {100} texture structure forming heat treatment (first heat treatment) according to 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 | plate material which the volume fraction of the particle | grains which have a face integrated 50% or more.

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. By the phase transformation of the heat-treated iron or iron-based alloy to the ferrite (α) phase, it is possible to form a predetermined texture on the plate. At this time, in order to form a {100} plane parallel to the metal sheet surface made of iron or iron-based alloy on the metal sheet, i) reduce oxygen in at least one of the inner region and the surface region of the metal sheet; The metal plate is heat-treated under a temperature at which the austenite phase is stable, while blocking the metal plate from external oxygen. By phase-transforming the heat treated metal sheet into a ferrite phase, particles having {100} <0vw> parallel to the sheet surface of the metal sheet can be formed at a high density. In addition, {100} <001> aggregates may be formed.

Analysis of the aggregates was done using the orientation distribution function (ODF) analysis. The pole figure was measured on {110}, {200}, and {211} planes in a circular plate specimen with a diameter of 3 cm, and then azimuth distribution analysis was performed. Orientation distribution analysis was expressed using the Orientation Density (f (g)) given in Euler space.

Example 1

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. In order to form a dense {100} plane having the columnar crystals on the sheet, 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. When the heat treatment furnace reached 900 ° C, the specimen at room temperature was pushed into the center of the furnace. In the alloy of Fe-1.0% Si composition, 900 ℃ 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 ℃ / hr to 1050 ℃. The Fe-1.0% Si alloy maintains a complete austenite phase above about 1000 ° C. Thus, 1050 ° C is the zone where the austenite phase is stable. After maintaining 15 minutes at 1050 ℃ again the specimen was cooled to a cooling rate of 400 ℃ / hr up to 900 ℃. When the temperature of the specimen reached 900 ℃ the specimen was removed to the room temperature chamber and cooled to reach the temperature of the specimen. In the specimen subjected to this heat treatment, 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.

Referring to FIG. 1, when cold rolling is carried out and cold rolling is performed with the reduction ratio of 20% or less, the strong {100} plane formed in the first heat treatment is maintained or slightly raised even after the residual stress removing heat treatment is performed. (Approximately 80% of the plate surface). In addition, when the reduction ratio was increased to 30% and residual stress relief heat treatment was performed, it was found that the {100} plane was reduced, so that at least 50% of the sheet surface had particles having the {100} plane. When rolling is performed at a rolling reduction of 35% or more and residual stress relief heat treatment is performed, {321}, {111}, and {310} planes are increased, and the {100} plane is reduced to less than 30% of the entire surface. The conclusion that can be derived from these results is that in order to obtain excellent texture even after the residual stress heat treatment, the reduction ratio of cold rolling should be 50% or less after the first heat treatment.

In the above analysis, 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. Although 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.

FIG. 2 is a graph showing azimuth density of a specimen subjected to heat treatment at 800 ° C. for 1 hour when the reduction ratio is 25% (φ 2 = 45 ° section).

Referring to FIG. 2, it can be seen that the {100} <011> texture is very well developed in the plate.

Figure 3 is a graph showing the change in the orientation density of the {100} texture in accordance with the reduction ratio (Φ = 0 °, φ 2 = 45 °).

Referring to FIG. 3, it can be seen that when the first heat treatment is performed, a high density {100} fiber aggregate can be formed on the plate. On the other hand, when cold rolling was performed, the reduction ratio was 15% or less, and even when the residual stress removal heat treatment was performed on the sheet, the <001> direction was well present in all directions. However, when the reduction ratio was 20% or more, it was shown that when the residual stress removal heat treatment was performed, {100} <011> particles were strongly formed in the rolling direction (Rotated Cube Texture). When the reduction ratio exceeds 50%, residual stress removal heat treatment causes the formation of planes other than the {100} planes, which weakens the overall strength of the {100} texture. Therefore, in order to form a strong {100} texture after the final residual stress removal heat treatment, the reduction ratio must be 50% or less.

[Example 2]

In this embodiment, 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 (first heat treatment) 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.

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 °).

Referring to FIG. 5, it can be seen that the thinner the thickness, the higher the volume fraction of the {100} fiber texture. That is, it can be seen that as the through-type particles increase, the {100} fiber texture increases. These results can be interpreted that the penetration particles play an important role in the formation of {100} fiber texture.

In order to examine the effect of the penetrating particles on the {100} <011> texture, 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.

6 is a rotated cube that appears in a specimen subjected to the 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 1 hour at a temperature of 800 ° C. and a nitrogen atmosphere ( {100} <011>) A graph showing the volume fraction of the aggregates (tolerance: 15 °).

Referring to FIG. 6, in a thin specimen (100 and 200 μm in thickness) in which almost all particles have a through particle shape, {100} <011> texture is formed even at a small reduction ratio of about 10 to 20%. Strengthening phenomenon is found. However, in the relatively thick specimens (500 µm) with about 60% of the through-particles, the {100} <011> texture was not strengthened at the reduction rate of 15% or less, and the reduction ratio was 20-50%. In the phosphorus interval, {100} <011> aggregation was strengthened. However, when the reduction ratio exceeds 40%, the volume of the {100} <011> aggregate tissue was relatively decreased. Therefore, it was found that the strength of the {100} <011> texture was very strong in the thin specimens having a large number of relatively penetrating particles.

Taken together, 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>.

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 µm. Referring to FIG. 7, it is well understood that 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. When 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. That is, when the specimen is rolled, particles having {100} <0vw> inside the plate are rotated to {100} <011>, and when the residual stress removing heat treatment is performed in this state, particles having {100} <011> This phenomenon occurs because only polygonization occurs while the orientation is maintained. The phenomenon in which the {100} <011> texture is formed is a phenomenon that appears when the usual residual stress removal heat treatment conditions are satisfied. In other words, the heat treatment is preferably performed in the temperature range of 650 ~ 950 ℃ 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 α is stable. If the heat treatment is performed in an austenite single phase zone or an austenite ferrite abnormal zone, the {100} <011> texture disappears. On the other hand, since 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. However, if 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. 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 ℃ nitrogen atmosphere. Referring to FIG. 8, after cold rolling 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. However, in semi-penetrating particles or particles whose <001> direction is not perpendicular to the plate surface, 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.

According to 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.

Furthermore, 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.

As described above, the present invention has been described by way of a limited embodiment, but the present invention is not limited to the above embodiments, and those skilled in the art to which the present invention pertains may make various modifications and variations from this description. Do. Therefore, the scope of the present invention should not be limited to the above-described embodiments, but should be defined by the claims below and equivalents thereof.

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 °).

FIG. 2 is a graph showing azimuth density of a specimen subjected to heat treatment at 800 ° C. for 1 hour when the reduction ratio is 25% (φ 2 = 45 ° section).

Figure 3 is a graph showing the change in the orientation density of the {100} texture in accordance with the reduction ratio (Φ = 0 °, φ 2 = 45 °).

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.

5 is a graph showing the change in volume fraction of {100} fiber texture according to the thickness in the specimen subjected to the first heat treatment (tolerance error: 15 °).

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 °).

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 µm.

 FIG. 8 is a {100} texture forming heat treatment on a Fe-1.0% Si steel plate having a thickness of 550 µm, 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.

Claims (7)

 In treating the metal plate composed of the {100} texture including the columnar columnar particles and composed of iron or iron-based alloy, {100} plane parallel to the metal plate surface on the metal plate member by cold rolling the metal plate member at a reduction ratio of 20 to 40%, followed by a second heat treatment at a stable temperature. A method for forming a {100} <011> texture having a <011> direction parallel to the rolling direction. The method of claim 1, Metal plate material consisting of a {100} texture including the columnar columnar particles, i) a first heat treatment step of heat treating a plate made of iron or an iron-based alloy while preventing the oxidation of the surface of the plate under a stable temperature of the austenite phase; And ii) a phase transformation step of changing the heat-treated metal sheet into a ferrite (α) phase. The method of claim 2, The phase transformation step is formed by cooling the heat-treated metal sheet material from the austenite phase stabilization temperature of {100}. The method of claim 1, The second heat treatment is a manufacturing method of an electrical steel sheet, characterized in that made under 650 to 950 ℃. The method of claim 1, The second heat treatment is a method of manufacturing an electrical steel sheet, characterized in that made for 3 hours or less. An electrical steel sheet prepared by the method of claim 1, comprising an aggregate structure made of iron or an iron-based alloy sheet and having a {100} plane parallel to the sheet surface and a direction parallel to the rolling direction. The method of claim 6, The electrical steel sheet, At least some of the crystal grains having a {100} plane parallel to the plate surface are vertically formed to penetrate the plate, and have at least 25% rotated cubes ({100} <011>). An electrical steel sheet comprising an assembly).
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KR102283225B1 (en) 2021-05-03 2021-07-29 주식회사 썸백 (001) textured electrical steels and method for manufacturing the same

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