KR102087182B1 - Non-oriented electrical steel sheet and method for manufacturing the same - Google Patents

Abstract

Non-oriented electrical steel sheet according to an embodiment of the present invention in weight%, Si: 2.6 to 3.6%, Al: 0.2 to 1.3%, Mn: 0.1 to 1.5%, C: 0.005% or less (excluding 0%) , N: 0.005% or less (excluding 0%), S: 0.005% or less (excluding 0%), Cr: 0.01 to 0.06%, P: 0.003 to 0.08%, Cu: 0.001 to 0.008% and the balance It contains Fe and unavoidable impurities, and the texture area fraction of an orientation within 15 degrees from {111} <uvw> is 10% or less.

Description

Non-oriented electrical steel sheet and manufacturing method thereof {NON-ORIENTED ELECTRICAL STEEL SHEET AND METHOD FOR MANUFACTURING THE SAME}

It relates to a non-oriented electrical steel sheet and a method of manufacturing the same. Specifically, Cu, P, Cr and other components are precisely controlled, and after primary cold rolling, a skin pass secondary cold rolling process is introduced to minimize the {111} <uvw> texture ratio, thereby ultimately improving magnetism. It relates to a non-oriented electrical steel sheet and a method of manufacturing the same.

Non-oriented electrical steel sheet is mainly used in a motor that converts electrical energy into mechanical energy, in order to exhibit high efficiency in the process requires the excellent magnetic properties of the non-oriented electrical steel sheet. In particular, recently, as eco-friendly technology has attracted attention, it is considered to be very important to increase the efficiency of the motor, which accounts for the majority of the total electric energy consumption, and for this purpose, the demand for non-oriented electrical steel sheets having excellent magnetic properties is also increasing.

The magnetic properties of non-oriented electrical steel are mainly evaluated by iron loss and magnetic flux density. Iron loss refers to energy loss occurring at a specific magnetic flux density and frequency, and magnetic flux density refers to the degree of magnetization obtained under a specific magnetic field. The lower the iron loss, the more energy-efficient motors can be manufactured under the same conditions. The higher the magnetic flux density, the smaller the motor or the lower the copper loss. Therefore, the non-oriented electrical steel sheet having low iron loss and high magnetic flux density can be produced. It is important.

The characteristics of the non-oriented electrical steel sheet to be considered also depend on the operating conditions of the motor. As a criterion for evaluating the properties of non-oriented electrical steel sheet used in motors, W15 / 50, which is the iron loss when 1.5T magnetic field is applied at a commercial frequency of 50Hz, is the most important. However, not all motors of various applications consider the W15 / 50 iron loss the most important, and may also evaluate iron loss at different frequencies or applied magnetic fields, depending on the main operating conditions. In particular, among the non-oriented electrical steel sheets used in large-scale generators and electric motor drive motors, magnetic properties are often important at low magnetic fields of 1.0T or less, so low magnetic field loss such as W10 / 50 or W10 / 400 By evaluating the properties of the non-oriented electrical steel sheet.

A commonly used method for increasing the magnetic properties of non-oriented electrical steel sheet is to add alloying elements such as Si. The addition of such alloying elements can increase the resistivity of the steel. As the resistivity increases, the eddy current loss decreases, thereby lowering the total iron loss. On the other hand, as the amount of Si is increased, the magnetic flux density is inferior and brittleness is increased, and if a certain amount or more is added, cold rolling is impossible and commercial production is impossible. In particular, the electrical steel sheet can be seen that the effect of reducing the iron loss as the thickness is reduced, the rolling properties due to brittleness is a fatal problem. In order to increase the specific resistance of steel, elements such as Al and Mn may be added to produce high quality non-oriented electrical steel sheets having excellent magnetic properties.

{111} <uvw> aggregates are known to be disadvantageous to magnetism, and attempts have been made to suppress their production. Among them, a method of limiting the Al content extremely low is known. However, when the Al content is too low, there is a disadvantage that it is inferior to high frequency magnetism due to low specific resistance, or can not be used in a motor requiring high speed rotation due to low yield strength.

Various methods for improving the texture of non-oriented electrical steel sheet are already widely known, but the effect thereof is limited or causes an increase in the process cost, which is often not practical. Therefore, there is a demand for non-oriented electrical steel sheet having a superior texture while minimizing the increase in process cost.

One embodiment of the present invention provides a non-oriented electrical steel sheet and a method of manufacturing the same. Specifically, Cu, P, Cr and other components are precisely controlled, and after primary cold rolling, a skin pass secondary cold rolling process is introduced to minimize the {111} <uvw> texture ratio, thereby ultimately improving magnetism. To provide a non-oriented electrical steel sheet and a method for manufacturing the same.

Non-oriented electrical steel sheet according to an embodiment of the present invention in weight%, Si: 2.6 to 3.6%, Al: 0.2 to 1.3%, Mn: 0.1 to 1.5%, C: 0.005% or less (excluding 0%) , N: 0.005% or less (excluding 0%), S: 0.005% or less (excluding 0%), Cr: 0.01 to 0.06%, P: 0.003 to 0.08%, Cu: 0.001 to 0.008% and the balance It contains Fe and unavoidable impurities, and the texture area fraction of an orientation within 15 degrees from {111} <uvw> is 10% or less.

Non-oriented electrical steel sheet according to an embodiment of the present invention may further include at least one of Ti: 0.003% by weight or less, Nb: 0.003% by weight or less, V: 0.003% by weight or less and Zr: 0.003% by weight or less. .

Non-oriented electrical steel sheet according to an embodiment of the present invention may have an average grain diameter of 70 to 150㎛.

Non-oriented electrical steel sheet according to an embodiment of the present invention may have a thickness of 0.1 to 0.65mm.

Method for producing a non-oriented electrical steel sheet according to an embodiment of the present invention by weight, Si: 2.6 to 3.6%, Al: 0.2 to 1.3%, Mn: 0.1 to 1.5%, C: 0.005% or less (0% N: 0.005% or less (excluding 0%), S: 0.005% or less (excluding 0%), Cr: 0.01 to 0.06%, P: 0.003 to 0.08%, Cu: 0.001 to 0.008% And the remainder producing a slab comprising Fe and inevitable impurities; Heating the slab; Hot rolling the slab to produce a hot rolled sheet; Primary cold rolling of the hot rolled sheet to prepare a primary cold rolled sheet; Intermediate annealing the primary cold rolled sheet at a temperature of 850 ° C. or lower; Preparing a secondary cold rolled sheet by second cold rolling the primary cold rolled sheet at a reduction ratio of 1 to 6%; And final annealing the secondary cold rolled sheet at 900 ° C. or higher.

Heating the slab may heat the slab to 1200 ° C. or less.

The manufacturing of the hot rolled sheet may have a finish rolling temperature of 800 ° C. or higher.

After the step of producing the hot rolled sheet, the hot rolled sheet annealing can be omitted, and the primary cold rolling can be started.

Non-oriented electrical steel sheet according to an embodiment of the present invention by controlling the optimum content range of Cr, P and Cu, and after the first cold rolling, by presenting the optimum conditions of the skin pass secondary cold rolling process, {111} < uvw> orientation can be extremely suppressed.

The non-oriented electrical steel sheet according to one embodiment of the present invention may provide the highest quality non-oriented electrical steel sheet by ultimately improving the low magnetic field.

This can contribute to improving the efficiency of motors and generators.

Terms such as first, second, and third are used to describe various parts, components, regions, layers, and / or sections, but are not limited to these. These terms are only used to distinguish one part, component, region, layer or section from another part, component, region, layer or section. Accordingly, the first portion, component, region, layer or section described below may be referred to as the second portion, component, region, layer or section without departing from the scope of the invention.

The terminology used herein is for reference only to specific embodiments and is not intended to limit the invention. As used herein, the singular forms “a,” “an,” and “the” include plural forms as well, unless the phrases clearly indicate the opposite. As used herein, the term "comprising" embodies a particular property, region, integer, step, operation, element, and / or component, and the presence of another property, region, integer, step, operation, element, and / or component, or It does not exclude the addition.

When a portion is referred to as being "on" or "on" another portion, it may be directly on or on the other portion or may be accompanied by another portion therebetween. In contrast, when a part is mentioned as "directly above" another part, no other part is intervened in between.

Although not defined otherwise, all terms including technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art. Commonly defined terms used are additionally interpreted as having a meaning consistent with the related technical literature and the presently disclosed contents, and are not interpreted as ideal or very formal meaning unless defined.

In addition, unless otherwise indicated,% means weight% and 1 ppm is 0.0001 weight%.

In the embodiment of the present invention, the meaning of further including an additional element means to include a residual amount of iron (Fe) by an additional amount of the additional element.

Hereinafter, embodiments of the present invention will be described in detail so that those skilled in the art can easily practice. As those skilled in the art would realize, the described embodiments may be modified in various different ways, all without departing from the spirit or scope of the present invention.

Non-oriented electrical steel sheet according to an embodiment of the present invention in weight%, Si: 2.6 to 3.6%, Al: 0.2 to 1.3%, Mn: 0.1 to 1.5%, C: 0.005% or less (excluding 0%) , N: 0.005% or less (excluding 0%), S: 0.005% or less (excluding 0%), Cr: 0.01 to 0.06%, P: 0.003 to 0.08%, Cu: 0.001 to 0.008% and the balance Fe and unavoidable impurities.

First, the reason for component limitation of a non-oriented electrical steel sheet is demonstrated.

Si: 2.6 to 3.6 wt%

Silicon (Si) serves to lower the iron loss by increasing the specific resistance of the material, and if too little is added, the iron loss improvement effect may be insufficient. On the contrary, when too much is added, the brittleness of the material may increase, leading to a sharp decrease in rolling productivity. Therefore, Si can be added in the above-mentioned range. More specifically, Si may include 2.7 to 3.5% by weight.

Al: 0.2-1.3 wt%

Aluminum (Al) serves to lower the iron loss by increasing the specific resistance of the material, and if too little is added to the nitride finely formed it may lower the magnetism. On the contrary, when too much is added, the nitride is excessively deteriorated and the magnetism is deteriorated, and in all processes such as steelmaking and continuous casting, problems can be caused and the productivity can be greatly reduced. Therefore, Al can be added in the above-mentioned range. More specifically, it may include 0.3 to 1.2% by weight of Al.

Mn: 0.1-1.5 wt%

Manganese (Mn) serves to improve the iron loss and form sulfides by increasing the resistivity of the material, and when too little is added, sulfides may be minutely precipitated to lower the magnetism. On the contrary, when too much MnS is precipitated excessively, the magnetic flux density may be reduced by encouraging the formation of {111} aggregates, which are disadvantageous to magnetism. Therefore, Mn can be added in the above-mentioned range. More specifically, Mn may be included in an amount of 0.2 wt% to 1.4 wt%.

C: 0.005 wt% or less

Since carbon (C) causes magnetic aging and combines with other impurity elements to form carbides to lower the magnetic properties, the carbon (C) is preferably limited to 0.005% by weight or less, more specifically 0.004% by weight or less.

N: 0.005 wt% or less

Nitrogen (N) not only forms fine and long AlN precipitates in the base material, but also combines with other impurities to form fine nitrides, inhibits grain growth and worsens iron loss, so more specifically, 0.005% by weight or less. It is good to restrict to the following.

S: 0.005 wt% or less

Sulfur (S) forms a fine sulfide inside the base material to suppress grain growth and worsen iron loss, so it is preferable to be lower, and preferably 0.005% by weight or less and more preferably 0.003% by weight or less.

Cr: 0.01 to 0.06 wt%

Chromium (Cr) serves to form coarse carbides by combining with C inside the base material at a temperature of about 700 ° C. or less. If too little is added, the carbide coarsening effect may be insufficient. If too much is added, the number of carbides during annealing may increase excessively, which may worsen the magnetism. Therefore, Cr may be included in the above range. More specifically, it may include 0.015 to 0.057% by weight of Cr.

P: 0.001 to 0.1 wt%

Phosphorus (P) is segregated on the surface or grain boundary of the base material to lower the surface energy and grain boundary energy to delay precipitate suppression and {111} <uvw> recrystallization and to develop a magnetically favorable texture. If the amount of P added is too small, the effect may be significantly reduced. If the amount of P added is too high, the segregation amount may increase brittleness and degrade the surface quality, making production difficult. Therefore, P can be added in the above-mentioned range. More specifically, it may include 0.003 to 0.07% by weight of P.

Cu: 0.001 to 0.008 wt%

If too little copper (Cu) is included in the base material to form a sulfide of a fine size may be worse grain growth. If too much Cu is included, complex sulfide may be produced together with Mn, Se, and the like to worsen iron loss. Therefore, Cu may be included in the above-described range. More specifically, it may include 0.003 to 0.0075 wt% of Cu.

Non-oriented electrical steel sheet according to an embodiment of the present invention may further include at least one of Ti: 0.003% by weight or less, Nb: 0.003% by weight or less, V: 0.003% by weight or less and Zr: 0.003% by weight or less. .

Ti: 0.003 wt% or less, Nb: 0.003 wt% or less, V: 0.003 wt% or less and Zr: 0.003 wt% or less

Niobium (Nb), titanium (Ti), vanadium (V), and zirconium (Zr) are elements that have a strong tendency to form precipitates in the steel, and deteriorate iron loss by forming fine carbides or nitrides in the base metal to suppress grain growth. Therefore, Nb, Ti, V, Zr may be further included in the aforementioned range, respectively. More specifically, at least one of Ti: 0.003 wt% or less, Nb: 0.003 wt% or less, V: 0.003 wt% or less, and Zr: 0.003 wt% or less.

The remaining component of the present invention is iron (Fe). However, in the usual manufacturing process, since impurities which are not intended from the raw materials or the surrounding environment may be inevitably mixed, this cannot be excluded.

In the non-oriented electrical steel sheet according to one embodiment of the present invention, the texture area fraction of an orientation within 15 ° from {111} <uvw> may be 10% or less. In {111} <uvw>, uvw means an arbitrary number, and means a direction in which the normal direction (ND direction) of the plate surface is parallel to <111>, and the rolling direction (RD direction) is parallel to <uvw>. That is, it means the case where the <111> axis of a crystal grain exists in the range within 15 degrees from the normal axis (ND direction) of the plate surface of a steel plate. At this time, the total area may be a TD plane.

In one embodiment of the present invention, magnetic control can be improved by controlling the aggregated area fraction of the orientation within 15 ° from {111} <uvw> to 10% or less. More specifically, the texture area fraction of an orientation within 15 ° from {111} <uvw> may be included in an amount of 8.8% or less. More specifically, the texture area fraction of the orientation within 15 ° from {111} <uvw> may be included as 6.5 to 8.8%.

Non-oriented electrical steel sheet according to an embodiment of the present invention may have an average grain size of 70 to 150㎛. In the aforementioned range, the magnetism of the non-oriented electrical steel sheet is more excellent.

Non-oriented electrical steel sheet according to an embodiment of the present invention may have a thickness of 0.1 to 0.65mm.

Non-oriented electrical steel sheet according to an embodiment of the present invention, as described above, the magnetic properties are improved. Specifically, the magnetic flux density B50 induced in the 5000 A / m magnetic field is 1.68T or more. Based on the thickness of 0.35mm, the iron loss W15 / 50 when the magnetic flux density of 1.5T is induced at a frequency of 50 Hz may be 2.2 W / kg or less. More specifically, the magnetic flux density B50 may be 1.69 to 1.75T, and the iron loss W15 / 50 may be 1.8 to 2.1 W / kg.

As such, since the non-oriented electrical steel sheet according to the embodiment of the present invention has excellent magnetic properties, it may contribute to improving the efficiency of the motor and the generator.

Method for producing a non-oriented electrical steel sheet according to an embodiment of the present invention comprises the steps of manufacturing a slab; Heating the slab; Hot rolling the slab to produce a hot rolled sheet; Primary cold rolling of the hot rolled sheet to prepare a primary cold rolled sheet; Intermediate annealing the primary cold rolled sheet; Preparing a secondary cold rolled sheet by second cold rolling the primary cold rolled sheet at a reduction ratio of 1 to 6%; And finally annealing the secondary cold rolled sheet.

Hereinafter, each step will be described in detail.

First make a slab. The reason for limiting the addition ratio of each composition in the slab is the same as the reason for limiting the composition of the non-oriented electrical steel sheet described above, and thus repeated description is omitted. Since the composition of the slab is not substantially changed during the manufacturing process of hot rolling, hot rolling annealing, primary cold rolling, intermediate annealing, and secondary cold rolling final annealing, the composition of the slab and the composition of the non-oriented electrical steel sheet Substantially the same.

First, the slab is heated. Specifically, the slab is charged into a heating furnace and heated to 1200 ° C or less. The precipitate may be redissolved when heated at a temperature exceeding 1200 ° C. to be finely precipitated after hot rolling. More specifically, it may be heated to 1100 to 1200 ℃.

The heated slabs are hot rolled to 2 to 2.3 mm to produce hot rolled plates. The finishing rolling temperature in the manufacturing of the hot rolled sheet may be 800 ℃ or more. Specifically, it may be 800 to 1000 ° C.

After preparing the hot rolled sheet, the method may further include pickling the hot rolled sheet. The primary cold rolling can be started within 10 seconds after the step of producing the hot rolled sheet, before or after pickling, without annealing the hot rolled sheet. In one embodiment of the present invention, the cold rolling rate of the primary cold rolling is relatively low, so that the hot rolled sheet annealing can be omitted.

Next, the hot rolled sheet is first cold rolled to produce a primary cold rolled sheet. Although it may be applied differently depending on the thickness of the hot rolled sheet, by applying a reduction ratio of 70 to 95% can be primary cold rolling so that the final thickness is 0.2 to 0.65mm.

Next, the primary cold rolled sheet is subjected to annealing at a temperature of 850 ° C. or lower. Intermediate annealing is carried out to recrystallize the deformed structure of the primary cold rolled plate. If the temperature is too high, the Υ-fiber develops strongly in the texture, and the orientation of the bearing within 15 ° from {111} <uvw> after the final annealing. A large amount of tissue is formed. More specifically, the intermediate annealing temperature may be 700 to 840 ° C. The intermediate annealing time may be 100 to 150 seconds.

Next, the secondary cold rolled intermediate cold-rolled primary cold plate at a reduction ratio of 1 to 6% to prepare a secondary cold rolled sheet. By adding a secondary cold rolling process in one embodiment of the present invention, it is possible to suppress the texture of the orientation within 15 ° from {111} <uvw>. If the reduction ratio is too small, the above effects may not be sufficient. If the reduction ratio is too large, a large amount of agglomerates having an orientation within 15 degrees from {111} <uvw> are formed. More specifically, the reduction ratio of the secondary cold rolling may be 1.5 to 5.5%.

Next, the secondary cold rolled sheet is finally annealed at 900 ° C or higher. By the final annealing as such, the average grain size can be 70 to 150 mu m. If the final annealing temperature is too low, recrystallization does not occur sufficiently, and a large amount of agglomerates in azimuth within 15 ° from {111} <uvw> are formed. Specifically, the final annealing temperature may be 910 to 1050 ℃. In the final annealing process, all of the processed tissue formed in the first and second cold rolling stages (ie, 99% or more) can be recrystallized. The final annealing time may be 50 to 150 seconds.

Hereinafter, preferred examples and comparative examples of the present invention are described. However, the following examples are only preferred embodiments of the present invention, and the present invention is not limited to the following examples.

Example

By weight, it was prepared as shown in Table 1, to prepare a slab containing the remaining Fe and unavoidable impurities. The slab was heated to 1150 ° C. and hot rolled to a finishing temperature of 880 ° C. to prepare a hot rolled plate having a plate thickness of 2.0 mm. The hot rolled hot rolled plate was subjected to pickling and primary cold rolling without the hot rolled sheet annealing. After the intermediate annealing for 120 seconds at a temperature summarized in Table 2, and the second cold rolling at a reduction ratio summarized in Table 2 to make a thickness of 0.35mm. Then, the final annealing for 90 seconds at the temperature summarized in Table 2 below.

The {111} <uvw> area fraction, average grain diameter, and magnetic properties of each specimen are shown in Table 2 below.

The {111} <uvw> fraction was measured by EBSD as the area containing 3000 or more crystal grains in the TD section of the specimen, and was expressed by extracting the fraction of the point where the ND plane had the {111} plane within an error angle of 15 °.

The grain size was calculated by (measurement area / number of grains) ^ 0.5 by photographing an area including 1500 or more grains in the TD cross section of the specimen under an optical microscope.

The magnetic properties such as magnetic flux density and iron loss were averaged by cutting the specimens of width 60mm × length 60mm × number of sheets for each specimen and measuring them in the rolling direction and the vertical direction by single sheet tester. At this time, W15 / 50 is an iron loss when a magnetic flux density of 1.5T is induced at a frequency of 50 Hz, and B50 is a magnetic flux density induced in a magnetic field of 5000 A / m.

Psalm Number Si (%) Al (%) Mn (%) C (ppm) N (ppm) S (ppm) Cr (ppm) P (ppm) Cu (ppm) A1 2.7 1.2 0.2 27 16 11 80 45 51 A2 2.7 1.2 0.2 30 18 10 170 60 50 A3 2.7 1.2 0.2 29 16 9 390 45 44 A4 2.7 1.2 0.2 24 17 8 560 65 50 A5 2.7 1.2 0.2 29 15 14 780 75 47 B1 3.5 0.6 0.6 31 17 16 510 150 73 B2 3.5 0.6 0.6 27 16 17 480 880 72 B3 3.5 0.6 0.6 35 18 15 520 200 72 B4 3.5 0.6 0.6 32 18 17 510 240 69 B5 3.5 0.6 0.6 27 15 16 500 250 71 C1 3.1 0.8 0.4 25 17 13 340 690 63 C2 3.1 0.8 0.4 26 16 16 310 720 121 C3 3.1 0.8 0.4 28 16 14 300 23 68 C4 3.1 0.8 0.4 25 15 14 350 600 61 C5 3.1 0.8 0.4 27 21 15 320 680 64 D1 3.1 0.3 1.3 30 19 17 430 430 46 D2 3.1 0.3 1.3 29 19 16 450 400 50 D3 3.1 0.3 1.3 29 17 18 430 400 51 D4 3.1 0.3 1.3 32 17 18 440 450 50 D5 3.1 0.3 1.3 30 14 15 430 430 48 E1 3.4 0.05 1.1 26 16 13 420 400 65

Psalm Number middle
Annealed
Temperature
(℃) final
Annealed
Temperature
(℃) 2nd cold rolling reduction rate
(%) {111} <uvw>
Fraction
(area%) Average grain size
(μm) B50
(T) W15 / 50
(W / kg) Remarks A1 780 1000 5.5 18.7 91 1.64 2.4 Comparative example A2 780 1000 5.5 8.3 94 1.69 2.02 Inventive Example A3 780 1000 5.5 7.6 93 1.69 2.01 Inventive Example A4 780 1000 5.5 7.9 95 1.69 2.01 Inventive Example A5 780 1000 5.5 12.1 63 1.66 2.33 Comparative example B1 750 1040 3 6.8 117 1.69 1.94 Inventive Example B2 750 1000 3 11.6 54 1.66 2.39 Comparative example B3 750 960 3 7.3 87 1.69 1.99 Inventive Example B4 750 920 3 8.8 79 1.69 2.04 Inventive Example B5 750 880 3 11.8 58 1.66 2.38 Comparative example C1 745 1030 1.5 8.3 120 1.69 1.95 Inventive Example C2 775 1030 1.5 13.2 123 1.65 2.24 Comparative example C3 805 1030 1.5 19.4 137 1.64 2.21 Comparative example C4 835 1030 1.5 8.7 121 1.69 1.94 Inventive Example C5 865 1030 1.5 13.7 121 1.65 2.23 Comparative example D1 760 970 0.5 16.8 88 1.65 2.28 Comparative example D2 760 970 1.5 7.3 91 1.69 2.01 Inventive Example D3 760 970 3 7.4 92 1.69 2 Inventive Example D4 760 970 5.5 6.9 86 1.69 1.99 Inventive Example D5 760 970 7 24.1 87 1.64 2.3 Comparative example E1 760 970 3 11.1 91 1.67 2.17 Comparative example

As shown in Table 1 and Table 2, since A2, A3, A4, B1, B3, B4, C1, C4, D2, D3, and D4, both the component content and the manufacturing method satisfy the scope of the present invention, {111} < uvw> fraction was less than 10% and magnetic properties were also excellent.

On the other hand, A1, A5, B2, C2, and C3 have a content of Cr, P, and Cu outside the scope of the present invention, so that the {111} <uvw> fraction exceeds 10% or the crystal grains do not grow sufficiently, resulting in inferior magnetic properties. appear. In addition, out of the ranges of B5, C5, D1, D5, intermediate annealing temperature, secondary cold rolling, and final annealing temperature, the {111} <uvw> fraction exceeds 10% or the crystal grains do not grow sufficiently, resulting in poor magnetic properties. Inferior. E1, the Al content is out of the scope of the present invention, the {111} <uvw> fraction exceeded 10%, the less Al contained inferior magnetic properties.

The present invention is not limited to the above embodiments, but may be manufactured in various forms, and a person of ordinary skill in the art to which the present invention pertains does not change the technical spirit or essential features of the present invention. It will be appreciated that the present invention may be practiced as. Therefore, it should be understood that the embodiments described above are exemplary in all respects and not restrictive.

Claims (8)

By weight, Si: 2.6-3.6%, Al: 0.2-1.3%, Mn: 0.1-1.5%, C: 0.005% or less (excluding 0%), N: 0.005% or less (excluding 0%) , S: 0.005% or less (excluding 0%), Cr: 0.01 to 0.06%, P: 0.003 to 0.08%, Cu: 0.001 to 0.008% and the balance includes Fe and inevitable impurities,
Non-oriented electrical steel sheet having a texture area fraction of an orientation within 15 ° from {111} <uvw> of 10% or less. The method of claim 1,
Non-oriented electrical steel sheet further comprising at least one of Ti: 0.003% by weight or less, Nb: 0.003% by weight or less, V: 0.003% by weight or less and Zr: 0.003% by weight or less. The method of claim 1,
Non-oriented electrical steel sheet having an average grain diameter of 70 to 150㎛. The method of claim 1,
Non-oriented electrical steel sheet having a thickness of 0.1 to 0.65 mm. By weight, Si: 2.6-3.6%, Al: 0.2-1.3%, Mn: 0.1-1.5%, C: 0.005% or less (excluding 0%), N: 0.005% or less (excluding 0%) S: 0.005% or less (excluding 0%), Cr: 0.01 to 0.06%, P: 0.003 to 0.08%, Cu: 0.001 to 0.008% and the balance to produce a slab containing Fe and unavoidable impurities;
Heating the slab;
Hot rolling the slab to produce a hot rolled sheet;
Manufacturing the first cold rolled plate by cold rolling the hot rolled plate;
Annealing the primary cold rolled sheet at a temperature of 850 ° C. or lower;
Preparing a secondary cold rolled sheet by second cold rolling the primary cold rolled sheet at a reduction ratio of 1 to 6%; And
Method for producing a non-oriented electrical steel sheet comprising the step of final annealing the secondary cold rolled sheet to 900 ℃ or more. The method of claim 5,
Heating the slab is a method of manufacturing a non-oriented electrical steel sheet for heating the slab to 1200 ℃ or less. The method of claim 5,
The manufacturing of the hot rolled sheet is a method of manufacturing a non-oriented electrical steel sheet having a finish rolling temperature of 800 ℃ or more. The method of claim 5,
After the step of manufacturing the hot rolled sheet, the method of manufacturing a non-oriented electrical steel sheet to skip the hot rolled sheet annealing, to start the first cold rolling.