KR101630427B1 - Non-oriented electrical steel sheet and method for manufacturing the same - Google Patents

Abstract

The present invention relates to a non-oriented electrical steel sheet and a method of manufacturing the same. The steel sheet comprises 1.0 to 3.6% of Si, 0.1 to 0.3% of Al, 0.02 to 0.05% of Mn, 0.02 to 0.2% 0.005% or less, S: 0.001% to 0.005%, and Ti: 0.005% or less by weight, the balance being Fe and other inevitably added impurities, and having a {100} A non-oriented electrical steel sheet whose volume fraction is 1.5 times or more the volume fraction of crystal grains parallel to the {110} plane with respect to the sheet surface, and a production method thereof.

Description

BACKGROUND OF THE INVENTION 1. Field of the Invention [0001] 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 a method of manufacturing the same, and more particularly, to a non-oriented electrical steel sheet having improved magnetic properties by effectively controlling the relationship between Mn and P components, .

In order to improve the iron loss among the magnetic properties of the non-oriented electrical steel sheet, a method of adding Si, Al, Mn or the like, which is an alloy element having a large resistivity, is generally used for increasing the electrical resistance. However, addition of an alloying element reduces the iron loss, but also decreases the magnetic flux density due to the decrease of the saturation magnetic flux density. In addition, if the amount of Si added increases, the workability is lowered, which makes cold rolling difficult and lowers the productivity. When Al, Mn, etc. are added too much, the rolling properties are lowered and the hardness is increased and the workability is lowered.

In order to improve the magnetic flux density while lowering iron loss, a method of adding a trace amount of alloying element is used to reduce the fraction of crystal grains parallel to the <111> axis in the direction perpendicular to the sheet, which is a harmful texture, And a technique for manufacturing a clean steel was used. However, all of these technologies cause a rise in manufacturing cost and difficulties in mass production, and therefore, there is a need for a technique that is excellent in magnetic improvement effect without significantly increasing manufacturing cost.

In order to solve these problems, there have been continuous efforts in Japanese Patent Unexamined Publication Nos. 55-158252, 62-180014, 59-100217, 2000-160306 and Korean Patent Laid-Open No. 1998-026183, , An increase in cost or a decrease in productivity.

Mn, together with Si and Al, is a major element that increases electrical resistivity. It also plays a role of reducing eddy loss by reducing vortex loss. However, Mn is a major cause of decreasing magnetism by forming fine inclusions in combination with S in steel. It is also a factor for lowering the magnetism.

In the nonoriented electric steel sheet, the iron loss is lowered when the crystal grain size is increased in the factors affecting the magnetism. However, if the texture is not easily developed at this time, the aggregate structure is more important because it increases iron loss and lowers the magnetic flux density. It is preferable that the {100} planes of the crystal grains are parallel to each other, and the {111} planes or {211} planes are preferably low in the texture of the set texture. The {100} plane of the texture is parallel to the {100} plane of the {100} plane. However, since the {100} plane is difficult to magnetize and is disadvantageous to magnetic properties, 100} parallel to the plane and the {110} plane parallel to the plane are also important.

In order to solve the above problems, the present invention is to provide a non-oriented electrical steel sheet having excellent magnetic properties and improved magnetic properties by efficiently arranging aggregate structures favorable to magnetism by utilizing the relationship between Mn and P components, and a manufacturing method thereof.

In one or more embodiments of the present invention, it is preferable that the steel sheet contains 1.0 to 3.6% of Si, 0.1 to 0.3% of Al, 0.02 to 0.05% of Mn, 0.02 to 0.2% of P, 0.005% or less of C, 0.005% or less, S: 0.001 to 0.005%, Ti: 0.005% or less, the balance being composed of Fe and other inevitably added impurities, and a volume fraction of crystal grains having {100} 110} plane is 1.5 times or more than the volume fraction of parallel crystal grains can be provided.

The Mn and P satisfy a composition formula of [Mn] <[P], wherein [Mn] and [P] are weight percent of Mn and P added respectively.

Further, Mn may be contained in an amount of 0.02 to 0.05% by weight, Sn + Sb may be contained in an amount of 0.01 to 0.2% by weight, and each of Cu, Ni and Cr may be contained in an amount of 0.05% Each may further contain 0.01% by weight or less.

The inclusions may be at least one selected from the group consisting of MnS, CuS, Cu ₂ S and (Mn, Cu) S, wherein the inclusions in the steel sheet have an average diameter of not less than 0.01 탆 and not more than 1 탆, .

In one or more embodiments of the present invention, it is preferable that 1.0 to 3.6% of Si, 0.1 to 0.3% of Al, 0.02 to 0.05% of Mn, 0.02 to 0.2% of P, 0.005% or less of C, 0.005% or less of N, 0.001 to 0.005% of S, 0.005% or less of Ti, and the balance of Fe and other inevitably added impurities, wherein Mn and P satisfy a composition formula of [Mn] < Reheating the steel slab to 1200 DEG C or less; Hot rolling the reheated slab; Annealing the hot-rolled hot-rolled sheet by hot rolling or omitting the hot-rolled sheet and cold rolling; And finally annealing the cold-rolled cold-rolled sheet at a temperature of 850 to 1100 占 폚. Here, [Mn] and [P] are weight percent of Mn and P added, respectively.

In this case, Sn + Sb may be further added in an amount of 0.01 to 0.2% by weight, Cu, Ni and Cr may each be contained in an amount of 0.05% by weight or less, Zr, Mo and V may be contained in an amount of 0.01% have.

Also, the annealing of the hot-rolled sheet is performed in a temperature range of 850 to 1150 ° C, and the hot rolling is performed at a final reduction ratio of 20% or less. The cold rolling is carried out twice during the primary cold rolling or intermediate annealing Or more.

According to the embodiment of the present invention, it is possible to control the addition amount of Mn and Al to suppress generation of fine inclusions, or to control the ratio of {100} / {110} Directional electric steel sheet excellent in magnetic properties can be produced.

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.

In one embodiment of the present invention, the addition amount of Mn is strictly controlled to 0.01 to 0.10% by weight, more preferably 0.02 to 0.05% by weight, in the component system to which Si, Al, Mn and P are added, In the range of 0.1 to 0.3% by weight to suppress the generation of inclusions such as fine AlN and to increase the distribution density of coarse inclusions to improve the magnetic properties.

For this, in one embodiment of the present invention, the non-oriented electrical steel sheet comprises 1.0 to 3.6% of Si, 0.1 to 0.3% of Al, 0.02 to 0.05% of Mn, 0.02 to 0.2% of P, 0.005 to 0.005% of C, By mass or less of Ti, 0.005% or less of N, 0.001 to 0.005% of S, and 0.005% or less of Ti, the balance being Fe and other inevitably added impurities, So that the volume fraction of the {110} plane with respect to the plate surface is 1.5 times or more the volume fraction of the crystal grains parallel to each other.

Mn and P satisfy the composition formula of [Mn] < [P]. Here, [Mn] and [P] mean the weight percent of Mn and P added, respectively, and are the same as the following.

According to an embodiment of the present invention, Sn and Sb may further be included in addition to the above composition, and Sn + Sb may be further added in an amount of 0.01 to 0.2% by weight. In the non-oriented electrical steel sheet, The average diameter of the inclusions of the first layer is 0.11 탆 or more.

In one embodiment of the present invention, at least 0.1% or more of Mn is added to the non-oriented electrical steel sheet because Mn increases with the addition of Al and Si to increase the specific resistance of the steel and reduce iron loss. However, Mn is combined with S in forming a precipitate of MnS, and an impurity element S is combined with Cu to form CuS or Cu ₂ S. In other words, S combines with Mn and Cu to form a sulfide, which is formed of MnS or CuS alone or a composite inclusion of (Mn, Cu) S.

The inclusion of the non-oriented electrical steel sheet generally has a diameter of about 0.05 탆, which inhibits grain growth and hinders the movement of the magnetic wall, thereby greatly affecting the magnetic properties. Therefore, the frequency of formation of coarse inclusions is increased to minimize magnetic deterioration There is a need. Al added as a resistivity element also forms a fine nitride and causes magnetism to become weak.

According to one embodiment of the present invention, not only the Mn and P are controlled so as to satisfy the composition formula of [Mn] < P, but also the average diameter of the inclusions is made coarse as well as the {100} plane, 111} plane as well as the {110} plane. In particular, the fraction of {100} plane / {110} plane was set to be 1.5 or more.

In the nonoriented electrical steel sheet, the texture of the {100} plane parallel to the plane of the sheet is {fraction {100}} / {110} plane The magnetic property can be greatly improved.

Hereinafter, the reason for limiting the numerical value of the component according to the embodiment of the present invention will be described.

Si: 1.0 to 3.6 wt%

Since the Si is a component that lowers the vortex loss during iron loss by increasing the specific resistance of the steel, it is difficult to obtain a low iron loss property when the Si content is less than 1.0%. When the Si content exceeds about 3.6%, the plate breakage occurs during cold rolling. In one embodiment of the invention, Si is limited to 1.0 to 3.6 wt%.

Mn: 0.02 to 0.05 wt%

Since the Mn has the effect of increasing the specific resistance and lowering the iron loss in addition to the Si and Al, the conventional non-oriented electrical steel sheet was attempted to improve the iron loss by adding at least 0.02% of Mn. However, as the Mn addition amount increased, the saturation magnetic flux density decreased Therefore, the magnetic flux density is decreased, and it is combined with S to form fine MnS inclusions, thereby suppressing crystal growth and interfering with the magnetic wall movement, thereby increasing hysteresis loss among steel losses. Therefore, in order to improve the magnetic flux density and prevent the increase of iron loss due to inclusions, it is preferable that the amount of Mn added is limited to 0.02 to 0.05% in one embodiment of the present invention.

Al: 0.1 to 0.3 wt%

The above Al is an inevitably added element for steel deoxidation in the steelmaking process, which is a major element for increasing the resistivity. Therefore, it is added in order to lower the iron loss, but also serves to decrease the saturation flux density. If Al is added in an amount of less than 0.1%, fine AlN is formed to inhibit crystal growth to reduce magnetism. When the Al content is more than 0.3%, magnetic flux density is decreased. Therefore, in one embodiment of the present invention The addition amount of Al is limited to 0.1 to 0.3%.

P: 0.02 to 0.2 wt%

The P decreases the iron loss by lowering the specific resistance and segregates in the grain boundaries to inhibit the formation of {111} texture which is harmful to the magnetism and forms {100} which is an advantageous aggregate structure. However, 0.2% by weight. Further, Mn is an element that inhibits ferrite formation, whereas P is an element that expands a ferrite phase. By containing a larger amount of P in order to satisfy the formula [Mn] < [P] It is possible to work on ferrite so that the desirable texture for magnetism can be improved. In particular, the amount of P added is limited as described above so that a characteristic of {100} / {110} as a ratio between {100} plane and {110} plane, which is advantageous for magnetism, is 1.5.

C: 0.005 wt% or less

 When C is added heavily, it enlarges the austenite region and increases the phase transformation period. It suppresses the grain growth of ferrite during annealing and increases the iron loss. It combines with Ti and forms carbide to dislocate magnetism. The iron loss is increased by magnetic aging at the time of use after use. Therefore, the content of C is limited to 0.005% or less in one embodiment of the present invention.

S: 0.001 to 0.005% by weight or less

S is an element which forms sulfides such as MnS, CuS and (Cu, Mn) S which are harmful to the magnetic properties, and therefore it is known that it is preferable to add S low. However, when it is added in an amount less than 0.001%, it is rather disadvantageous in formation of aggregate structure and magnetic property is lowered. Therefore, it is contained in an amount of 0.001% or more, and when it is added in an amount exceeding 0.005%, the magnetism is heated due to increase of fine sulfides. In one embodiment, the content of S is limited to 0.001 to 0.005%.

N: 0.005 wt% or less

N is an element which is detrimental to magnetism such as forming a nitride by binding with Al, Ti or the like to inhibit crystal growth, and therefore it is preferable to contain N in a small amount. In one embodiment of the present invention, N is limited to 0.005 wt% or less.

Ti: 0.005 wt% or less

Ti forms fine carbides and nitrides to inhibit crystal growth. As the amount of Ti is increased, the magnetization becomes poor due to the increase in the carbides and nitrides, resulting in the deterioration of the magnetism. Therefore, the Ti content is limited to 0.005% or less in one embodiment of the present invention.

Sn + Sb: 0.01 to 0.2 wt%

The Sn and Sb are added as a segregated element in the grain boundaries to suppress the diffusion of nitrogen through the grain boundaries and to suppress the {111} texture which is detrimental to the magnetism and to increase the {100} And Sb alone or in a total amount exceeding 0.2%, the content of Sn + Sb is limited to 0.01 to 0.2% because grain growth is suppressed and magnetic properties are deteriorated and the rolling property is deteriorated.

In addition to the above elements, Cu, Ni, and Cr, which are inevitably added in the steelmaking process, react with impurity elements to form fine sulfides, carbides, and nitrides, thereby detrimentally affecting the magnetic properties. Limit. Since Zr, Mo, V and the like are also strong carbonitride-forming elements, they are preferably not added as much as possible and are each contained at 0.01% by weight or less.

In addition to the above composition, the remainder is composed of Fe and other unavoidable impurities.

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

The non-oriented steel sheet steel slab prepared as described above is reheated to a temperature of 1200 DEG C or less and then hot rolled. When the reheating temperature is higher than 1200 ° C., the precipitates such as AlN and MnS present in the slab are reused after hot rolling to precipitate fine crystals to suppress grain growth and decrease magnetism, so that the reheating temperature is limited to below 1200 ° C. Finishing rolling in hot rolling is finished in ferrite phase and final rolling reduction is 20% or less for plate shape calibrating.

According to one embodiment of the present invention, rolling in the ferrite phase can add a large amount of ferrite-like expansion elements such as Si, Al, P, or less Mn and C, which are elements that suppress ferrite phase, The temperature of the finish rolling may be rolled to a ferrite phase temperature. In particular, when the Si content is 2 wt% or more, hot rolling on ferrite is possible without any control. As described above, when rolled on ferrite, a large number of {100} planes are formed in the texture, thereby improving the magnetic properties.

The hot-rolled sheet prepared as described above is rolled up at 700 ° C or less and cooled in air. The rolled hot-rolled sheet, if necessary, is subjected to hot-rolled sheet annealing, pickling, cold-rolling, and finally cold-rolled sheet annealing.

The hot-rolled sheet annealing is to anneal the hot-rolled sheet when necessary for improving the magnetic properties, and the hot-rolled sheet annealing temperature is 850 to 1150 ° C. If the annealing temperature of the hot-rolled sheet is lower than 850 ° C, the grain growth is insufficient. When the annealing temperature exceeds 1150 ° C, the crystal grains excessively grow and the surface defects of the plate become excessive. Lt; RTI ID = 0.0 &gt; 1150 C. &lt; / RTI &gt;

The hot rolled sheet picked up by a conventional method or the annealed hot rolled sheet is cold rolled.

The cold rolling is final rolled to a thickness of 0.10 mm to 0.70 mm, and if necessary, can be subjected to primary cold rolling and secondary cold rolling after intermediate annealing, and the final rolling reduction is in the range of 50 to 95%.

The final cold-rolled steel sheet is cold-rolled sheet annealed. In the step of annealing the cold rolled sheet, the temperature of the annealing of the cold rolled sheet during annealing is 850 to 1100 占 폚. If the annealing temperature of the cold rolled sheet is lower than 850 DEG C, the growth of the crystal grains is insufficient and the {111} texture, which is harmful to the magnetism, increases. When the temperature exceeds 1100 DEG C, the crystal grains grow excessively, The cracking temperature of the cold-rolled sheet in the embodiment of the present invention is 850 to 1100 ° C.

The annealed sheet is shipped to the customer after the insulating coating treatment. The insulating coating may be treated with an organic, inorganic and organic composite coating, or may be treated with other insulating coatings. The customer can use the steel sheet after processing.

Hereinafter, an embodiment of the present invention will be described in more detail.

[Example 1]

The slabs formed as shown in Table 1 below were heated at 1150 占 폚, hot-rolled to a thickness of 2.4 mm, and then rolled at 650 占 폚. The hot-rolled steel sheet cooled in air was annealed at 1050 ° C for 3 minutes, pickled, cold-rolled to a thickness of 0.35 mm, and subjected to final annealing at 1,050 ° C for 1 minute. For each specimen, the average diameter of the inclusions of not less than 0.01 탆 and not more than 1 탆 was examined, and the texture was examined using X-ray. The iron loss and magnetic flux density were measured using a magnetometer, Respectively.

In one embodiment of the present invention, as a method for analyzing the diameter, type, and distribution of inclusions, a carbon replica extracted from a specimen was observed by TEM and analyzed by EDS. The TEM observation was carried out to determine the inclusions having a diameter of 0.01 탆 or more in a randomly selected area without any bias, and the diameters and distributions of all inclusions appearing after photographing with at least 100 images were measured. The EDS spectrum ) Were used to analyze the types of inclusions.

In the embodiment of the present invention, in the analysis of the diameter and distribution of inclusions, inclusions having a diameter of 0.01 탆 or less have difficulty in observation and measurement, and have a small influence on the magnetism and have oxides of 1 탆 or more. However, Is not included in the analysis object of the present invention.

Steel grade C Si Mn P S Al N Ti Sn Sb A1 25 1.3 0.05 0.18 38 0.25 23 14 0.03 A2 26 2.0 0.05 0.15 32 0.26 21 13 0.05 A3 21 2.5 0.04 0.06 31 0.23 13 15 0.03 A4 22 3.0 0.07 0.05 42 0.006 16 16 0.04 A5 24 3.2 0.06 0.03 31 0.22 15 14 0.03 A6 21 3.5 0.25 0.07 33 0.21 14 15 0.03 A7 30 3.1 0.28 0.06 22 0.3 15 13 0.03 A8 24 2.8 0.02 0.05 20 0.12 15 13 A9 25 3.0 0.05 0.02 15 0.28 16 14 0.02 0.02 A10 29 3.3 0.07 0.02 28 0.2 15 16 0.03 A11 23 3.0 0.05 0.07 30 0.3 16 16 A12 21 3.2 0.05 0.04 26 0.25 17 15 0.07 0.01 A13 38 3.6 0.05 0.03 22 0.15 16 14 0.05 A14 21 3.5 0.06 0.07 55 0.41 14 14 A15 26 3.4 0.06 0.09 60 0.18 12 15 0.04

In Table 1, the unit of the component content is% by weight. However, the content of C, S, N, and Ti is in ppm.

Steel grade {100} / {110} [Mn] < [P] 0.01 to 1 탆
Inclusion
Average diameter (占 퐉) Iron loss
W15 / 50
Magnetic flux density
B50
Remarks A1 1.55 O 0.145 2.70 1.78 Honor A2 1.80 O 0.131 2.55 1.78 Honor A3 2.10 O 0.135 1.99 1.76 Honor A4 0.85 X 0.051 2.30 1.70 Comparative Example A5 0.90 X 0.081 2.21 1.66 Comparative Example A6 1.20 X 0.910 2.17 1.65 Comparative Example A7 1.35 X 0.920 2.09 1.67 Comparative Example A8 1.99 O 0.121 1.95 1.75 Honor A9 2.30 X 0.154 1.83 1.77 Honor A10 2.50 X 0.350 1.87 1.74 Comparative Example A11 2.90 O 0.140 1.70 1.76 Honor A12 3.20 X 0.151 1.75 1.76 Honor A13 2.10 X 0.162 1.80 1.76 Honor A14 0.35 O 0.093 2.01 1.66 Comparative Example A15 0.55 O 0.102 2.50 1.65 Comparative Example

1) _Iron loss (W _15/50 ) is the average loss (W / kg) in the rolling direction and the rolling direction perpendicular to the magnetic flux density of 1.5 Tesla at 50 Hz frequency.

2) The magnetic flux density (B ₅₀ ) is the magnitude of the flux density (Tesla) induced when a magnetic field of 5000 A / m is added.

As shown in Table 2, the specimens satisfying the condition that the ratio of the {100} plane / {110} plane parallel to the plate surface of the steel sheet according to the embodiment of the present invention is 1.5 or more are A1, A2, A3, A8 , A9, A10, A11, A12, A13. All of these specimens had an average diameter of the inclusions of 0.11 탆 or more, and as a result, it was possible to produce an electric steel sheet having a low iron loss and a high magnetic flux density.

In addition, the characteristics of A9 and A12, in which Sn alone was added and A1, A2, A3, A10 and A13, and Sn and Ab, in which both Sn and Sb were added, had very low iron loss and excellent magnetic flux density.

Among the specimens satisfying the condition that the ratio of the {100} plane / {110} plane parallel to the flat surface is 1.5 or more, the content of Mn is 0.05% or less and the conditions of [Mn] <[P] Was particularly excellent in iron loss and magnetic flux density was extremely high.

On the other hand, among the specimens satisfying the conditions of [Mn] <[P], A14 and A15 are specimens in which the S content does not satisfy the range of the invention and the ratio of the {100} plane / {110} And the average diameter of the inclusions is not more than 0.11 mu m, so that the magnetism was examined for heat.

 As a comparative example, A4, A5, A6, and A7 did not satisfy the condition that the ratio of the {100} plane / {110} plane parallel to the flat surface was 1.5 or more, and the magnetic flux density was examined for heat.

[Example 2]

0.003% of C, 0.0035% of C, 1.35% of Si, 0.02% of Mn, 0.12% of P, 0.003% of S, 0.25% of Al, 0.0015% of N, 0.0018% of Ti and the balance of Fe and other unavoidable impurities Was subjected to reheating to a temperature of 1180 占 폚, followed by finish rolling of hot rolling at the time of hot rolling as shown in Table 3 below to obtain a hot-rolled steel sheet having a thickness of 2.3 mm, winding at 650 占 폚 and cooling in air. The hot-rolled sheet was continuously annealed for 5 minutes, pickled, and cold-rolled to a thickness of 0.35 mm as shown in Table 3. The cold-rolled sheet annealed for 1 minute at 70% nitrogen and 30% hydrogen. For each specimen, the average diameter of the inclusions of not less than 0.01 탆 and not more than 1 탆 and the texture using X-ray were examined. The iron loss and the magnetic flux density were measured using a magnetometer, and the results are shown in Table 3 below.

division Finishing finish
Rolling temperature
(° C) Hot-rolled plate
Temperature (℃) Annealing temperature of cold rolled sheet
(° C) 0.01 to 1 탆
Inclusion
Average diameter (占 퐉) Iron loss
(W15 / 50)
(W / kg) Magnetic flux density
B50 {100} / {110} Inventory 1 850 900 880 0.131 2.65 1.79 1.87 Inventory 2 850 960 900 0.136 2.56 1.80 1.90 Inventory 3 850 980 970 0.127 2.45 1.78 2.15 Comparative Example 1 950 950 900 0.095 3.35 1.72 1.01 Comparative Example 2 950 950 950 0.010 3.05 1.73 1.15

In Table 3, Inventive Examples 1 to 3 show that the average diameter of the inclusions was 0.127 to 0.131 탆 and the ratio of the {100} plane / {110} plane parallel to the plate surface was 1.5 or more when the finishing rolling of the finish rolling was performed on the ferrite. , Iron loss was low, and magnetic flux density was high.

On the other hand, Comparative Examples 1 and 2 were rolled in a state where the ferrite phase and the austenite phase were mixed while finishing rolling the finishing rolling, and the average diameters of the inclusions were 0.095 탆 and 0.10 탆, respectively. } Surface ratio of 1.01 and 1.16, respectively, it was found that both the iron loss and the magnetic flux density were not satisfied.

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 (11)

(% By mass), N: not more than 0.005% (0%), C: not more than 0.005%, N: not more than 0.005% 0.001 to 0.005% of S, and 0.005% or less of Ti (excluding 0%), the balance being Fe and other inevitably added impurities,
The volume fraction of crystal grains having {100} planes parallel to the plate surface is 1.5 times or more than the volume fraction of crystal grains having {110} planes parallel to the plate surface,
The average diameter of the inclusions of not less than 0.01 탆 and not more than 1 탆 in the steel sheet is not less than 0.11 탆,
Wherein the inclusions are at least one selected from MnS, CuS, Cu ₂ S and (Mn, Cu) S. The method according to claim 1,
Further comprising 0.01 to 0.2% by weight of Sn + Sb. The method according to claim 1,
Wherein the Mn and P satisfy a composition formula of [Mn] < [P].
(Where [Mn] and [P] are weight percentages of Mn and P added, respectively) The method according to claim 1,
And 0.05% by weight or less (excluding 0%) of Cu, Ni and Cr, and 0.01% by weight or less (excluding 0%) of Zr, Mo and V, respectively. (% By mass), N: not more than 0.005% (0%), C: not more than 0.005%, N: not more than 0.005% , Reheating a steel slab containing S: 0.001 to 0.005%, S: 0.005% or less (excluding 0%) and the balance consisting of Fe and other inevitably added impurities to a temperature of 1200 ° C or less;
Hot rolling the reheated slab;
Annealing the hot-rolled hot-rolled sheet by hot rolling or omitting the hot-rolled sheet and cold rolling; And
And finally annealing the cold-rolled cold-rolled sheet at a temperature of 850 to 1100 ° C,
In the hot rolling, finishing rolling in finish rolling finishes on ferrite,
The volume fraction of crystal grains having {100} planes parallel to the plate surface is 1.5 times or more than the volume fraction of crystal grains having {110} planes parallel to the plate surface,
An average diameter of inclusions of not less than 0.01 탆 and not more than 1 탆 in the produced non-oriented electrical steel sheet is 0.11 탆 or more,
Wherein the inclusions are at least one selected from MnS, CuS, Cu ₂ S and (Mn, Cu) S. 6. The method of claim 5,
Wherein the slab further comprises 0.01 to 0.2% by weight of Sn + Sb. 6. The method of claim 5,
Wherein the slab satisfies a composition formula of [Mn] < [P].
(Where [Mn] and [P] are weight percentages of Mn and P added, respectively) 6. The method of claim 5,
Wherein the slab further contains 0.05% by weight or less (excluding 0%) of Cu, Ni and Cr, and 0.01% by weight or less (excluding 0%) of Zr, Mo and V, respectively. 6. The method of claim 5,
Wherein the hot-rolled sheet annealing is performed in a temperature range of 850 to 1150 ° C. 6. The method of claim 5,
Wherein the hot rolling is performed at a final reduction ratio of 20% or less. 6. The method of claim 5,
Wherein said cold rolling is cold rolling at least two times with primary cold rolling or intermediate annealing being interposed therebetween.