KR20150073801A - Non-oriented electrical steel sheets and method for manufacturing the same - Google Patents

Abstract

A non-oriented electrical steel sheet is disclosed. The non-oriented electrical steel sheet according to one embodiment of the present invention is characterized by containing 0.005% or less of C, 2.2 to 4.5% or less of Si, 0.1% or less of Mn, 0.4 to 3% And Sb is 0.1 to 0.30%, and the balance is Fe and other inevitably added impurities.

Description

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a non-oriented electrical steel sheet,

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a non-oriented electrical steel sheet, and more particularly, to a non-oriented electrical steel sheet having excellent magnetic properties by controlling composition and aggregate structure and a method of manufacturing the same.

The nonoriented electric steel sheet is used as an iron core material in rotating devices such as motors, generators, and stationary devices such as small transformers, and plays an important role in determining the energy efficiency of electric devices.

The nonoriented electrical steel sheet is mainly used as an iron core material for rotating equipment, and magnetic properties are very important as an important part for converting electrical energy into mechanical energy. Iron loss and magnetic flux density are mainly mentioned as magnetic properties. Since iron loss is energy that disappears into heat during the energy conversion process, the lower the better, and the higher the magnetic flux density is the power source of the rotating body, the better the energy efficiency. In other words, the nonoriented electrical steel sheet should be magnetized well in a low magnetic field, so that it can obtain high power even if it is applied with low electricity. That is, the efficiency should be high. For this purpose, the non-oriented electrical steel sheet should have low iron loss and high magnetic flux density. Iron loss appears as heat when a magnetic field is applied, and magnetic flux density indicates the degree of power and efficiency transmitted in a magnetic field applied, because magnetic flux density is low if a large magnetic field is applied but the power is small. If the magnetic flux density is high, magnetization is facilitated to reduce the copper line in the iron core region. The small amount of copper means that copper loss, which is a major loss in the motor, is small. Losses in motors include copper loss, iron loss and mechanical loss, among which the ratio of copper loss is high. Unoriented electrical steel sheets are generally graded by the amount of silicon, since Si has a high resistivity and lowers eddle loss during iron losses. Al is another element that increases vortex loss, but it has a disadvantage that it is expensive. There is a limitation in the addition of such an element that increases the resistivity, because it has the disadvantage of making it difficult to roll when added in excess. Also, when the Si content is increased, the iron loss is improved but the magnetic flux loss is lowered. When the cold rolling is considered, the addition amount is not more than 4%. At the same time, the mold life is reduced when the mold is punched by the customer.

In addition, Al and Mn are also used as main elements for increasing the electrical resistivity, and thus can be used for reducing iron loss due to vortexing. However, addition of saturation also reduces saturation flux density.

Examples of prior arts in which crystal grain segregation elements are added to improve iron loss include those disclosed in Japanese Patent Application Laid-Open No. 59 (1984) -100217, Japanese Laid-Open Patent Application No. 62 (1987) -180014, Japanese Patent Publication No. 4-71989, 10 (1998) -212556, and Japanese Patent Application Laid-Open No. 16 (2004) -292829. However, in these prior art documents, changes in texture due to the addition of Sn, Sb, etc. are not taken into consideration, and when the content of Al is higher than 0.4%, the problem of deterioration of adhesiveness due to grain boundary segregation elements can not be considered.

Therefore, in order to obtain a non-oriented electrical steel sheet having a low iron loss and a high magnetic flux density, an alloy element which increases the resistivity is added, but the impurity element is controlled so as to improve the characteristics of the material, There is a need for a method of reducing the magnetic flux density and increasing the bearing favorable to the magnetic flux density.

An object of the present invention is to provide a non-oriented electrical steel sheet having a low iron loss and excellent magnetic properties by controlling the alloying elements of steel, texture, annealing conditions and the like, and a manufacturing method thereof.

The non-oriented electrical steel sheet according to one embodiment of the present invention is characterized by containing 0.005% or less of C, 2.2 to 4.5% or less of Si, 0.1% or less of Mn, 0.4 to 3% And Sb is 0.1 to 0.30%, and the balance includes Fe and other inevitably added impurities.

The non-oriented electrical steel sheet may satisfy F _{111} + F _{112}? 50%.

Where F _{111} is the volume fraction of crystal grains having an angle formed by the {111} plane with the rolled surface of not more than 15 ° F _{112} is the volume fraction of grains having an angle { Percentage fraction.)

The non-oriented electrical steel sheet can satisfy (F _{100} + F _{110} ) / (F _{111} + F _{112} ) 0.45.

Where F _{100} is the volume fraction of crystal grains having an angle of {100} with the rolled surface of not more than 15 ° F _{110} is the volume fraction of grains having an angle of {110} Percentage fraction.)

The non-oriented electrical steel sheet may satisfy B ₅₀ / Bs ≥ 0.85.

(Where B50 is the magnitude of the magnetic flux density (Tesla) induced when a magnetic field of 5000 A / m is added, and BS is the saturation flux density value).

The non-oriented electrical steel sheet can satisfy an average loss of 2.00 W / kg or less in a rolling direction and a direction perpendicular to the rolling direction when a magnetic flux density of 1.5 Tesla is induced at a frequency of 50 Hz.

The non-oriented electrical steel sheet further contains 0.015% or less of Cu (not including 0%), S: 0.003% or less (does not include 0%), and N: 0.005% or less can do.

A method for producing a non-oriented electrical steel sheet according to the present invention is a method for producing a non-oriented electrical steel sheet which comprises 0.005% or less of C, 2.2 to 4.5% or less of Si, 0.1% or less of Mn, 0.4 to 3% 0.1 to 0.30% of at least one of Sb and Fe, and the balance being Fe and other inevitably added impurities;

Reheating the slab to a temperature of 1050 to 1200 ° C, and rolling the slab to produce a hot-rolled steel sheet;

Rolling the hot-rolled steel sheet to produce a cold-rolled steel sheet; And

And finally annealing the cold-rolled steel sheet through a heating step and a cracking step.

The temperature raising step may raise the temperature to 700 ° C or higher at a temperature raising rate of 50 ° C / sec or higher. More preferably, the temperature can be raised to 800 ° C or higher at a heating rate of 80 ° C / sec or more.

The atmosphere in the heating step may be P _H2 / P _H2O ≤0.004. And more preferably P _H2 / P _H2O ≤ 0.0015.

(Where P _H2 is the partial pressure of hydrogen and P _H2O is the partial pressure of water vapor).

The hydrogen in the mixed gas may be at least 90 vol% in the heating step.

The atmosphere of the cracking step may be P _H2 / P _H2O ≤ 0.015. And more preferably P _H2 / P _H2O ≤ 0.008.

In the cracking step, hydrogen in the mixed gas may be 51 vol% or more.

The temperature in the cracking step may be 900 to 1150 ° C. More preferably 950 to 1070 < 0 > C.

The final annealing time may be 65 to 900 seconds.

Annealing the hot-rolled steel sheet at 900 to 1,150 占 폚; And air cooling at 750 DEG C or less after annealing the hot-rolled sheet.

The slab may further contain not more than 0.015% of Cu (not including 0%), S: not more than 0.003% (not including 0%) and N: not more than 0.005% (not including 0%) .

The electric steel sheet after completion of the final annealing can satisfy F _{111} + F _{112}? 50%.

The final annealed electric steel sheet can satisfy (F _{100} + F _{110} ) / (F _{111} + F _{112} ) 0.45.

The final annealed steel sheet may satisfy B ₅₀ / B _s ≥ 0.85.

The final annealed electric steel sheet can satisfy the rolling loss and the average loss in the rolling direction of 2.00 W / kg or less when a magnetic flux density of 1.5 Tesla is induced at a frequency of 50 Hz.

The non-oriented electrical steel sheet according to the present invention improves the aggregate structure by appropriately controlling the Al, Sn or Sb content among the alloying elements added to the steel and optimally managing the annealing conditions to prevent the segregation of Sn and Sb by segregation There is provided a non-oriented electrical steel sheet improved in magnetic properties by solving magnetic deterioration despite containing a large amount of Al.

Also, there is provided a non-oriented electrical steel sheet excellent in adhesion property by solving the problem that Sn, Sb and the like are segregated below the Al oxide layer despite containing a large amount of Al.

Advantages and features of the present invention and methods of achieving them will become apparent with reference to the embodiments described in detail below.

However, it is to be understood that the present invention is not limited to the disclosed embodiments, but may be embodied in many different forms and should not be construed as limited to the embodiments set forth herein. It is intended that the disclosure of the present invention be limited only by the terms of the appended claims.

The non-oriented electrical steel sheet according to one embodiment of the present invention is characterized by containing 0.005% or less of C (not including 0%), 2.2-4.5% of Si, or 0.1% or less of Mn (by weight) 0.001 to 0.005% of S, 0.02 to 0.1% of Al, at least one of Sn and Sb of 0.1 to 0.3%, and the balance of Fe and other inevitably added impurities.

The non-oriented electrical steel sheet may satisfy F _{111} + F _{112}? 50%.

Where F _{111} is the volume fraction of crystal grains having an angle formed by the {111} plane with the rolled surface of not more than 15 ° F _{112} is the volume fraction of grains having an angle { Percentage fraction.)

Further, the non-oriented electrical steel sheet may be a non-oriented electrical steel sheet satisfying (F _{100} + F _{110} ) / (F _{111} + F _{112} ) 0.45.

Where F _{100} is the volume fraction of crystal grains having an angle of {100} with the rolled surface of not more than 15 ° F _{110} is the volume fraction of grains having an angle of {110} Percentage fraction.)

The non-oriented electrical steel sheet may be a non-oriented electrical steel sheet satisfying B ₅₀ / B _s ≥ 0.85. (Where B ₅₀ is the magnitude of the magnetic flux density (Tesla) when a magnetic field of 5000 A / m is added and B _S is the saturation magnetic flux density value).

The inevitably added impurities include S, N, and may be added in an amount of 0.003% or less (not including 0%) and 0.005% or less (excluding 0%) of S,

The thickness of the electrical steel sheet may be 0.10 to 0.34 mm.

The reason for limiting the content of the components in the present invention is as follows.

C causes magnetic aging to degrade the magnetic properties, and therefore it is preferable to control it to 0.005% or less. More preferably 0.003% by weight or less.

Si is an element that increases the resistivity and lowers eddy current loss during iron loss.

If the content of Si is excessive, plate breakage may occur. Therefore, it is preferable to add 4.5% or less in the present invention steel for one time rolling in cold rolling.

In the present invention, Si is added in an amount of 2.2% or more based on a composition in which no solid phase transformation is present in the entire temperature range.

As the addition amount of Mn increases, the saturation magnetic flux density decreases. Further, in the present invention, since Mn is an austenite forming element, it is preferable that it is not added in order to satisfy a range that does not cause a solid phase transformation.

However, in consideration of the amount that is inevitably added during the steelmaking process, it is preferable to be 0.1% or less.

Al is an element that increases the resistivity and lowers the eddy loss, but the texture changes as the Al content increases.

In the case of the non-oriented electrical steel sheet according to the prior art, Al nitride has an adverse effect on magnetism, and the coating adhesion is weakened by Al oxide distributed on the surface.

However, in the present invention, since the above problem is solved through control of the temperature rise step and the cracking step in the final annealing and the specific resistance is increased by Al, the content of Al is added in an amount of 0.4 to 3%.

Sn and Sb are segregated in grain boundaries to suppress diffusion of oxygen elements and the like from the surface of the steel during annealing and are distributed densely on the surface of the final product to inhibit oxidation and reduce {111} orientation and {112} . ≪ / RTI >

In the present invention, at least one of Sn and Sb is preferably added in an amount of 0.1 to 0.3%. When it is less than 0.1%, there is no effect of addition, and when it exceeds 0.3%, the cold rolling property deteriorates.

N is preferably not added because it forms fine and long AlN precipitates to suppress the growth of crystal grains. However, it is preferably 0.005% or less, more preferably 0.002% or less, in view of the amount inevitably added in the steelmaking process.

S is preferably not added because it forms fine precipitates MnS and CuS and inhibits crystal grain growth. However, it is preferably 0.003% or less, more preferably 0.001% or less, in view of the amount that is unavoidably added in the steelmaking process.

Cu reacts with the impurity elements added during the steelmaking process to form fine sulfides, carbides and nitrides, which adversely affect the magnetism, so that it is preferable to control the Cu content to 0.015% or less.

The remainder is composed of Fe and other inevitably added impurities.

The non-oriented electrical steel sheet according to the present invention is controlled so as to satisfy F _{111} + F _{112} 50%. Where F _{111} is the volume fraction of crystal grains having a {111} plane with the rolled surface of 15 ° or less, and F _{112} is a grain fraction having an angle formed by the {112} Volume fraction).

Generally, the best orientation for magnetism in the RD direction is the <100> orientation, followed by <110> and finally <111>.

Generally, when the Si content is increased, the decrease of the saturation magnetic flux value due to Si can be expressed as shown in the following Equation 1.

Mn [%] - 0.0604 [Al%] ---- (1) where the element content is% by weight.

In addition, the {111} <112> orientation is very strongly developed, and the magnetic flux density is much worse than the value obtained by decreasing the saturation magnetic flux density.

The non-oriented electrical steel sheet has an ideal magnetic property when <100> is uniformly arranged in the surface direction of the steel sheet, and when the <100> direction strongly develops in the plane direction, the magnetic property becomes very poor.

In addition, in the nonoriented electrical steel sheet with high Si contents without phase transformation, there are more than {111} orientations in consideration of the volume fraction of grains having an angle formed by the {112} plane with the rolled surface of less than 15 °.

Such orientation also causes a large number of bad orientations in magnetism in the direction of the rolling surface, so it is necessary to lower the fraction of these orientations.

Therefore, in the present invention, F _{111} + F _{112}? 50% can be satisfied by controlling the component system and controlling the final annealing. Where F _{111} is the volume fraction of crystal grains having a {111} plane with the rolled surface of 15 ° or less, and F _{112} is a grain fraction having an angle formed by the {112} Volume fraction).

Further, Sn and Sb were added in an amount of 0.1% or more, and (F _{100} + F _{110} ) / (F _{111} + F _{112} )? . Where F _{100} is the volume fraction of the crystal grains having an angle of {100} with the rolled surface of 15 ° or less, and F _{110} is the grain size of the grains having an angle of {110} Volume fraction).

(F _{100} + F _{110} ) / (F _{111} + F _{112} ) in a non-oriented electrical steel sheet containing about 3.2% of Si and 30 ppm or less of C, ) Is about 0.329. In the present invention, it has been found that this value can be increased to 0.45 or more as the content of Sn and Sb is 0.1% or more, and is increased to 1 or more according to annealing conditions. Accordingly, the non-oriented electrical steel sheet according to the present invention has excellent magnetic properties.

Further, in the present invention, B ₅₀ / B _s ≥ 0.85 can be satisfied by adjusting the component system and controlling the atmosphere during the final annealing. (Where B ₅₀ is the magnitude of the magnetic flux density (Tesla) when a magnetic field of 5000 A / m is added and B _S is the saturation magnetic flux density value).

It is necessary to divide the magnetic flux density by the saturation magnetic flux density value according to the Si content to evaluate the degree of aggregate formation favorable to magnetism by the process improvement.

In other words, even though the magnetic density can be obtained at low silicon content, the iron loss is very poor. Therefore, the degree of aggregate formation with high magnetic flux density and high magnetic flux density should be evaluated as B ₅₀ / Bs value.

The non-oriented electrical steel sheet according to the present invention has an excellent magnetic property at a value of B ₅₀ / B _s or more.

Hereinafter, a method of manufacturing the non-oriented electrical steel sheet according to the present invention will be described.

A method for producing a non-oriented electrical steel sheet according to the present invention is a method for producing a non-oriented electrical steel sheet which comprises 0.005% or less of C, 2.2 to 4.5% or less of Si, 0.1% or less of Mn, 0.4 to 3% 0.1 to 0.30% of at least one of Sb and Fe, and the balance being Fe and other inevitably added impurities; Reheating the slab to a temperature of 1050 to 1200 ° C, and rolling the slab to produce a hot-rolled steel sheet; Rolling the hot-rolled steel sheet to produce a cold-rolled steel sheet; And finally annealing the cold-rolled steel sheet through a heating step and a cracking step.

If the reheating temperature is higher than 1200 ° C at the reheating stage of the slab, the precipitates may be re-precipitated in the slab and may be finely precipitated. When the reheating temperature is lower than 1050 ° C, hot rolling is difficult.

Thus, the reheated slab is hot-rolled to produce a hot-rolled steel sheet.

The produced hot-rolled steel sheet can be annealed at 900 to 1,150 ° C for hot-rolled annealing, and after annealing the hot-rolled sheet, it can be cooled from 750 ° C or less.

In the present invention, since the content of Sn and Sb is high and the grain growth is suppressed, when the annealing temperature of the hot-rolled sheet is less than 900 ° C, excessive inclusions of Sn and Sb are contained in the low- It is preferable to control the annealing temperature of the hot rolled sheet in this way.

Thereafter, pickling, cold rolling and final annealing are performed to produce a non-oriented electrical steel sheet.

Here, cold rolling is preferably performed by one step of cold rolling. The cold rolled steel sheet to which cold rolling has been completed may be 0.10 to 0.34 mm.

The final annealing consists of a heating step and a cracking step.

It is preferable to raise the temperature to 700 캜 or higher at a temperature raising rate of 50 캜 / sec or higher in the temperature raising stage.

The atmosphere in the temperature rising step is preferably P _H2 / P _H2O ≤0.0040 (where P _H2 is the partial pressure of hydrogen and P _H2O is the partial pressure of water vapor), and the hydrogen in the mixed gas is preferably 90 vol% or more Do.

More preferably, the temperature is raised to 800 ° C or more at a heating rate of 80 ° C / sec or more, and P _H2 / P _H2O ≦ 0.0015 is more preferable, and hydrogen in the mixed gas is more preferably 90 vol% or more.

Sn and Sb are not only segregated in the grain boundaries but also elements that are well segregated on the surface or the interface.

The content of Al, Sn, and Sb is high in the component system of the present invention, so that Sn and Sb are segregated under the Al oxide layer of the electrical steel sheet, and the adhesion between the electrical steel sheet and the coating layer may be deteriorated.

Therefore, in the present invention, it has been found through various experiments that segregation occurs between Sn and Sb at about 650 to 800 ° C.

Thus, in order to improve the adhesion, the formation of the Al oxide layer on the surface of the steel sheet was prevented before the formation of the segregation layers of Sn and Sb, thereby solving the problem of adhesion.

Therefore, the problem that the adhesion is lowered when P _H2 / P _H2O ≤0.0040 and the hydrogen content in the mixed gas is 90 vol% or more is raised to 700 ° C or more at a heating rate of 50 ° C / sec or more in the temperature rising step. (Where P _H2 represents the partial pressure of hydrogen and P _H2O represents the partial pressure of water vapor)

More preferably, the temperature is raised to 800 ° C or higher at a temperature raising rate of 80 ° C / sec or more, and P _H2 / P _H2O ≤ 0.0015, and hydrogen in the mixed gas is 90 vol% or more.

It was also found that the {111} orientation decreased and the {110} and {100} orientations increased, and the magnetization was improved by maintaining the above conditions in the temperature rising step.

Also in the cracking step, it is preferable that P _H2 / P _H2O ≤ 0.0150, and the hydrogen in the mixed gas is preferably 51 vol% or more. More preferably, P _H2 / P _H2O ≤ 0.0080 and hydrogen in the mixed gas is more preferably 51 vol% or more.

By maintaining the above conditions in the cracking step, it was possible to obtain a non-oriented electrical steel sheet with minimized formation of oxides, prevention of surface peeling, and improved texture.

The temperature at the cracking step is preferably 900 to 1150 占 폚, and more preferably 950 to 1050 占 폚.

In the present invention, since the content of Sn and Sb is high and grain growth is suppressed, the final annealing is preferably carried out at a temperature of 900 ° C or higher, and more preferably at 950 ° C or higher.

In order to prevent abnormal crystal grain growth, it is preferable to perform final annealing at 1150 占 폚 or lower, more preferably at 1050 占 폚 or lower.

In the case of less than 65 seconds, since the content of Sn or Sb is high in the present invention, the crystal grain segregation is disturbed by grain boundary segregation and the size of the grain is reduced, The continuous annealing may become difficult. Also, if the annealing time is shortened, the economical efficiency is increased. Therefore, the annealing time is preferably 65 to 330 seconds from the viewpoint of improving the economical efficiency.

Hereinafter, a method of manufacturing a non-oriented electrical steel sheet according to the present invention will be described in detail with reference to examples. The following examples are illustrative of the present invention only and are not intended to limit the scope of the present invention.

[Example 1]

0.005% of S, 0.0012% of S, 0.0015% of N, 0.07% of Mn, 2.5% of Si, 1.1% of Al and the balance of Fe and other unavoidable impurities and Sn and Sb as shown in Table 1 Lt; RTI ID = 0.0 &gt; 1150 C. &lt; / RTI &gt;

Thereafter, hot rolled steel sheet was produced by hot rolling at 2.3 mm.

The hot-rolled steel sheet was annealed at 1,050 ° C for 80 seconds, annealed to 750 ° C, and air-cooled.

The pickled plate was then cold-rolled to 0.30 mm.

The cold-rolled steel sheet was finally annealed and the temperature was raised from room temperature to 800 ° C or higher under the same conditions as in Table 1.

In the cracking step, the conditions were maintained at 1025 DEG C for 185 seconds in an atmosphere of 60 vol.% Hydrogen and 40 vol.% Hydrogen and a dew point of -10 DEG C (where P _H2 / P _H20 value was 0.005).

The properties of the thus-prepared electrical steel sheets were measured and are shown in Table 1.

The magnetic measurements were measured in a rolling direction and in a direction perpendicular to the rolling direction using a 60 × 60 mm ² size single plate measuring instrument and expressed as an average value.

Sn% by weight Sb% Heating rate
℃ / s Consumption
[%] Oxidation degree P _H2 / P _H20 value Iron loss W15 / 50 Magnetic flux density
B50 B50 / Bs Adhesiveness Remarks 0.15 0 10 10 0.061 2.52 1.66 0.836 Bad Comparative Example 1 0.15 0 100 10 0.061 2.30 1.68 0.846 Bad Comparative Example 2 0.15 0 100 95 0.0005 1.81 1.75 0.866 Good Inventory 1 0 0.15 10 10 0.061 2.63 1.65 0.817 Bad Comparative Example 3 0 0.15 100 10 0.061 2.11 1.71 0.846 Bad Comparative Example 4 0 0.15 100 95 0.0005 1.88 1.74 0.861 Good Inventory 2

Here, the magnetic flux density B ₅₀ is the magnetic flux density measured at 5000 A / m, Bs is the saturation magnetic flux density, and the units are all Tesla.

_Iron loss W _15/50 is the average iron loss in the rolling direction and in the direction perpendicular to the rolling when the magnetic flux density of 1.5 Tesla is induced at a frequency of 50 Hz, and the unit is W / kg.

As can be seen from the above results, the inventive examples included in the scope of the present invention are superior to the comparative examples in magnetic properties and adhesion.

[Example 2]

Sn, and Sb as shown in Table 1 were mixed in a ratio of C: 0.00253%, S: 0.0014%, N: 0.0011%, Mn: 0.06%, Al: 1.05%, and other Fe and other unavoidable impurities, And reheated to 1150 캜.

Thereafter, hot rolled steel sheet was produced by hot rolling at 2.3 mm.

The hot-rolled steel sheet was annealed at 1,050 ° C for 80 seconds, annealed to 750 ° C, and air-cooled.

The pickled plate was then cold-rolled to 0.30 mm.

In the final annealing temperature raising step the gas mixture temperature increase the rate of temperature rise from room temperature to above 800 ℃ to 90 ℃ / s, and the hydrogen 95% by volume nitrogen 5 vol%, dew point -25 ℃ in the atmosphere (where P _H2 / P _H20 value Was 0.0008).

In the cracking step, the mixed gas was subjected to final annealing at 1025 ° C for 185 seconds at a dew point of -10 ° C (where P _H2 / P _H20 value was 0.005) at 60 vol% nitrogen and 40 vol% nitrogen.

The magnetic properties of the steel sheet were measured in a rolling direction and a direction perpendicular to the rolling direction using a 60 × 60 mm2 single-piece measuring instrument and expressed as an average value.

 The orientation parameters were calculated by cross sectional EBSD measurements. The data are shown in Table 2.

Si wt% Sn% by weight Sb% Iron loss W15 / 50 Magnetic flux density
B50 B50 / Bs (F {111} + F {112})
[%] (F {100} + F {110}) /
(F {111} + F {112}) value Adhesiveness Remarks 0.8 0.15 0 3.22 1.73 0.871 54 0.18 Good Comparative Example 5 2.6 0 0 2.12 1.66 0.836 75.1 0.29 Good Comparative Example 6 2.6 0.04 0 2.01 1.67 0.841 59.5 0.38 Good Comparative Example 7 2.6 0.14 0 1.72 1.75 0.882 41.5 1.19 Good Inventory 3 2.6 0.24 0 1.87 1.74 0.876 36.4 0.97 Good Honorable 4 2.6 0.41 0 2.33 1.70 0.856 31.5 0.57 Bad Comparative Example 8 2.6 0 0.035 2.11 1.68 0.846 61.5 0.36 Good Comparative Example 9 2.6 0 0.16nrftrnwhtfh distribution 1.76 1.74 0.876 29.7 0.55 Good Inventory 5 2.6 0 0.38 2.43 1.71 0.861 39.1 0.51 Bad Comparative Example 10
Rolling failure 2.6 0.12 0.11 1.93 1.74 0.876 37.3 0.86 Good Inventory 6 4.6 0.15 0 - - - - - - Comparative Example 11
Rolling failure

As can be seen from the above results, it can be seen that the {111} and {112} directions are reduced and the magnetic flux density is improved in the inventive example of the present invention.

While the present invention has been described in connection with certain exemplary embodiments, it will be understood by those skilled in the art that various changes and modifications may be made without departing from the spirit and scope of the invention as defined by the appended claims.

It is therefore to be understood that the above-described embodiments are illustrative in all aspects and not restrictive. The scope of the present invention is defined by the appended claims rather than the detailed description, and all changes or modifications derived from the meaning and scope of the claims and their equivalents should be interpreted as being included in the scope of the present invention .

Claims (25)

At least one of Sn and Sb is 0.1 to 0.30% by weight, and the balance is at least one selected from the group consisting of C: 0.005% or less, Si: 2.2-4.5% or less, Mn: 0.1% Fe and other inevitably added impurities. The method according to claim 1,
Wherein the non-oriented electrical steel sheet has F _{111} + F _{112}? 50%
Of the non-oriented electrical steel sheet.
Where F _{111} is the volume fraction of crystal grains having an angle formed by the {111} plane with the rolled surface of not more than 15 ° F _{112} is the volume fraction of grains having an angle { Percentage fraction.) 3. The method of claim 2,
The non-directional electrical steel sheet has (F _{100} + F _{110} ) / (F _{111} + F _{112}
Of the non-oriented electrical steel sheet.
Where F _{100} is the volume fraction of crystal grains having an angle of {100} with the rolled surface of not more than 15 ° F _{110} is the volume fraction of grains having an angle of {110} Percentage fraction.) The method of claim 3,
The non-oriented electrical steel sheet
B ₅₀ / B _s ≥ 0.85.
(Where B ₅₀ is the magnitude of the magnetic flux density (Tesla) when a magnetic field of 5000 A / m is added and B _S is the saturation magnetic flux density value). 5. The method of claim 4,
Wherein the non-oriented electrical steel sheet satisfies an average loss of 2.00 W / kg or less in a rolling direction and a direction perpendicular to a rolling direction when a magnetic flux density of 1.5 Tesla is induced at a frequency of 50 Hz. 6. The method according to any one of claims 1 to 5,
The non-oriented electrical steel sheet further contains 0.015% or less of Cu (not including 0%), S: 0.003% or less (does not include 0%), and N: 0.005% or less Non-oriented electrical steel sheet. At least one of Sn and Sb is 0.1 to 0.30% by weight, and the balance is at least one selected from the group consisting of C: 0.005% or less, Si: 2.2-4.5% or less, Mn: 0.1% Providing a slab comprising Fe and other inevitably added impurities;
Reheating the slab to a temperature of 1050 to 1200 ° C, and rolling the slab to produce a hot-rolled steel sheet;
Rolling the hot-rolled steel sheet to produce a cold-rolled steel sheet; And
And finally annealing the cold-rolled steel sheet through a heating step and a cracking step. 8. The method of claim 7,
In the heating step,
Wherein the temperature is raised to 700 占 폚 or more at a heating rate of 50 占 폚 / sec or more. 9. The method of claim 8,
The atmosphere of the temperature-
P _H2 / P _H2O ≤ 0.004.
(Where P _H2 is the partial pressure of hydrogen and P _H2O is the partial pressure of water vapor). 10. The method of claim 9,
Wherein the hydrogen in the mixed gas in the heating step is 90 vol% or more. 8. The method of claim 7,
In the heating step,
Wherein the temperature is raised to 800 占 폚 or more at a heating rate of 80 占 폚 / sec or more. 12. The method of claim 11,
The atmosphere of the temperature-
P _H2 / P _{H2O & lt;} / = 0.0015.
(Where P _H2 is the partial pressure of hydrogen and P _H2O is the partial pressure of water vapor). 13. The method of claim 12,
Wherein the hydrogen in the mixed gas in the heating step is 90 vol% or more. 14. The method of claim 13,
The atmosphere of the cracking step is,
P _H2 / P _H2O ≤ 0.015.
(Where P _H2 is the partial pressure of hydrogen and P _H2O is the partial pressure of water vapor). 15. The method of claim 14,
Wherein the hydrogen in the mixed gas in the cracking step is 51 vol% or more. 16. The method of claim 15,
The atmosphere of the cracking step is,
P _H2 / P _H2O ≤ 0.008.
(Where P _H2 is the partial pressure of hydrogen and P _H2O is the partial pressure of water vapor). 17. The method of claim 16,
And the temperature in the cracking step is 900 to 1150 占 폚. The method of manufacturing a non-oriented electrical steel sheet according to claim 17, wherein the temperature in the cracking step is 950 to 1070 캜. The method of manufacturing a non-oriented electrical steel sheet according to claim 18, wherein the final annealing time is 65 to 900 seconds. 20. The method of claim 19,
Annealing the hot-rolled steel sheet at 900 to 1,150 占 폚;
Cooling at a temperature of 750 ° C or less after annealing the hot-rolled steel sheet;
Further comprising the steps of: 21. The method according to any one of claims 7 to 20,
Wherein the slab further comprises a non-directional (not more than 0.015%) alloy, further comprising not more than 0.015% of Cu (not including 0%), S: not more than 0.003% (not including 0% A method of manufacturing an electrical steel sheet. 21. The method according to any one of claims 7 to 20,
Wherein the electric steel sheet after completion of the final annealing satisfies F _{111} + F _{112}? 50%.
Where F _{111} is the volume fraction of crystal grains having an angle formed by the {111} plane with the rolled surface of not more than 15 ° F _{112} is the volume fraction of grains having an angle { Percentage fraction.) 23. The method of claim 22,
Wherein the final annealed electric steel sheet satisfies (F _{100} + F _{110} ) / (F _{111} + F _{112} ) 0.45.
Where F _{100} is the volume fraction of crystal grains having an angle of {100} plane with the rolled surface of not more than 15 ° F _{110} is the volume of grain at an angle of {110} Percentage fraction.) 24. The method of claim 23,
Wherein the electric steel sheet after completion of the final annealing satisfies B ₅₀ / B _s ? 0.85.
(Where B ₅₀ is the magnitude of the magnetic flux density (Tesla) when a magnetic field of 5000 A / m is added and B _S is the saturation magnetic flux density value). 25. The method of claim 24,
Wherein the electric steel sheet after completion of the final annealing satisfies a rolling direction when an magnetic flux density of 1.5 Tesla is induced at a frequency of 50 Hz and an average loss in a direction perpendicular to the rolling direction of 2.00 W / kg or less.