KR101980289B1 - Non-oriented electrical steel sheet method for manufacturing the same - Google Patents

Abstract

According to an embodiment of the present invention, a non-oriented electric steel sheet comprises: 0.01 wt% or less of C (excluding 0 wt%); 1.5-4.5 wt% of Si; 0.03-3 wt% of Mn; 0.01-0.12 wt% of P; 0.006 wt% or less of S (excluding 0 wt%); 6 wt% or less of AI (excluding 0 wt%); 0.005 wt% or less of N (excluding 0 wt%); 0.0002-0.003 wt% of Be; and the remainder consisting of Fe and other unavoidable impurities.

Description

BACKGROUND OF THE INVENTION 1. Field of the Invention [0001] The present invention relates to a non-oriented electrical steel sheet,

A non-oriented electrical steel sheet and a non-oriented electrical steel sheet. And more particularly, to a method for producing a non-oriented electrical steel sheet and a non-oriented electrical steel sheet having excellent magnetic properties by adding an appropriate amount of Be.

Recently, the use of high efficiency motors has been greatly increased due to strengthened regulation of motor efficiency. In order to improve the efficiency of such a motor, it is necessary to lower the iron loss or lower the copper hand, and various methods are used for this purpose. In particular, both of these methods can significantly affect the magnetic properties of the non-oriented electrical steel sheet, which is a core material. As a result, manufacturers of motors are turning to the use of non-oriented electrical steel sheets with low iron loss in the use of conventional non-oriented electrical steel sheets having high iron loss.

On the other hand, in order to reduce copper loss, the design flux density is lowered or the excitation current in the design flux is lowered. In order to use the latter method, it is necessary to make the flux density of the non-oriented electrical steel sheet.

Especially, in case of high magnetic flux density material, it is advantageous to improve the torque, so that a motor having frequent n / off can output a large output in a short time.

In order to obtain a non-oriented electrical steel sheet having a high magnetic flux density, various alloy compositions have been proposed. Beryllium (Be) is an element distributed in various trace amounts on the earth. As an example of the addition of Be, a technique of adding Be in an amount of 0.2 wt% or more is known. However, when a large amount of Be is added in this manner, there is a problem in that Be is precipitated in grain boundaries and magnetic properties are largely deteriorated.

A non-oriented electrical steel sheet and a non-oriented electrical steel sheet. And more particularly, to a method for producing a non-oriented electrical steel sheet and a non-oriented electrical steel sheet having excellent magnetic properties by adding an appropriate amount of Be.

The non-oriented electrical steel sheet according to one embodiment of the present invention may contain 0.01% or less of C (excluding 0%), 1.5 to 4.5% of Si, 0.03 to 3% of Mn, 0.01 to 0.12% of P, , S: not more than 0.006% (excluding 0%), Al: not more than 6% (excluding 0%), N: not more than 0.005% (excluding 0%) and Be: The remainder includes Fe and other unavoidable impurities.

Sb: 0.001 to 0.1% by weight, and Sn: 0.001 to 0.1% by weight.

0.0005 to 0.005% by weight of Ca, and 0.0005 to 0.003% by weight of Mg.

And the average grain size may be 50 to 200 mu m.

The ratio B50L / B50D of the rolling direction magnetic flux density B50L to the magnetic flux density B50D in the direction of the rolling direction and the direction of the 45 占 angle may be 1.07 or less.

A method of manufacturing a non-oriented electrical steel sheet according to an embodiment of the present invention includes: C: 0.01% or less (excluding 0%); Si: 1.5 to 4.5%; Mn: 0.03 to 3% (Excluding 0%), N: 0.005% or less (excluding 0%), and Be: 0.0002 to 0.003% (inclusive) And the remainder comprising Fe and unavoidable impurities; Heating the slab; Hot rolling the slab to produce a hot rolled sheet; A step of cold-rolling the hot-rolled sheet to produce a cold-rolled sheet, and a step of finally annealing the cold-rolled sheet.

After the step of producing the hot-rolled sheet, the step of annealing the hot-rolled sheet may be further included.

The step of producing the cold rolled sheet may include one cold rolling step or may include two or more cold rolling steps with intermediate annealing in between.

The non-oriented electrical steel sheet produced according to one embodiment of the present invention improves the texture by adding P, and further by adding Be as a new trace additive element.

As a result, it is possible to provide a non-oriented electrical steel sheet having excellent magnetic properties, particularly, anisotropy of magnetic flux density.

Further, the non-oriented electrical steel sheet according to one embodiment of the present invention can be effectively used for an efficiency motor, a motor having high output and high torque characteristics, and a core material for a generator.

The terms first, second and third, etc. are used to describe various portions, components, regions, layers and / or sections, but are not limited thereto. These terms are only used to distinguish any moiety, element, region, layer or section from another moiety, moiety, region, layer or section. Thus, a first portion, component, region, layer or section described below may be referred to as a second portion, component, region, layer or section without departing from the scope of the present invention.

The terminology used herein is for the purpose of describing particular embodiments only and is not intended to limit the invention. The singular forms as used herein include plural forms as long as the phrases do not expressly express the opposite meaning thereto. Means that a particular feature, region, integer, step, operation, element and / or component is specified and that the presence or absence of other features, regions, integers, steps, operations, elements, and / It does not exclude addition.

When referring to a portion as being "on" or "on" another portion, it may be directly on or over another portion, or may involve another portion therebetween. In contrast, when referring to a part being "directly above" another part, no other part is interposed therebetween.

Unless otherwise defined, all terms including technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. Commonly used predefined terms are further interpreted as having a meaning consistent with the relevant technical literature and the present disclosure, and are not to be construed as ideal or very formal meanings unless defined otherwise.

Unless otherwise stated,% means% by weight, and 1 ppm is 0.0001% by weight.

In an embodiment of the present invention, the term further includes an additional element, which means that an additional amount of the additional element is substituted for the remaining iron (Fe).

Hereinafter, embodiments of the present invention will be described in detail so that those skilled in the art can easily carry out the present invention. The present invention may, however, be embodied in many different forms and should not be construed as limited to the embodiments set forth herein.

In one embodiment of the present invention, the texture and magnetism are significantly improved by adding the composition P in the non-oriented electrical steel sheet to improve the texture and by adding Be as a new trace additive element.

The non-oriented electrical steel sheet according to one embodiment of the present invention may contain 0.01% or less of C (excluding 0%), 1.5 to 4.5% of Si, 0.03 to 3% of Mn, 0.01 to 0.12% of P, , S: not more than 0.006% (excluding 0%), Al: not more than 6% (excluding 0%), N: not more than 0.005% (excluding 0%) and Be: The remainder includes Fe and other unavoidable impurities.

First, the reason for limiting the components of the non-oriented electrical steel sheet will be described.

C: not more than 0.01% by weight

When carbon (C) is contained in a large amount even after the final annealing, self-aging is caused and the iron loss is greatly increased. Therefore, the upper limit is set to 0.01 wt%. More specifically, it is adjusted to 0.005% by weight or less. More specifically, it may contain 0.0001 to 0.005% by weight of C.

Si: 1.5 to 4.5 wt%

Silicon (Si) is an element effective for increasing the intrinsic resistance of steel and reducing iron loss, and is a ferrite stabilizing element. If Si is contained too much, the ferrite may be transformed into austenite even at high temperatures, resulting in dislocation of magnetism. On the contrary, if too much Si is contained, the saturation flux is greatly reduced, and the excitation effective current remarkably increases when the motor is driven after fabrication. Therefore, Si can be contained in the range of 1.5 to 4.5% by weight. More specifically, it may contain 2.0 to 3.5% by weight of Si.

Mn: 0.03 to 3 wt%

Manganese (Mn) serves to prevent brittleness during hot rolling. When Mn is contained too much, the above-mentioned role can not be properly performed. On the other hand, if Mn is included too much, the proportion of Fe in the steel is reduced and the saturation magnetic flux density is lowered. Therefore, Mn can be included in the range of 0.03 to 3% by weight. More specifically, Mn may be contained in an amount of 0.05 to 1.0% by weight.

P: 0.01 to 0.12 wt%

Phosphorus (P) is a major element in improving texture. By adding P, the texture can be improved and the magnetic flux density can be increased. When P is too small, the effect of improving the magnetic flux density can not be sufficiently obtained. On the other hand, if too much P is contained, the brittleness of the steel is maximized, and cold rolling may become difficult. Accordingly, P may be contained in an amount of 0.01 to 0.12% by weight. More specifically, it may contain 0.03 wt% to 0.1 wt% of P.

S: not more than 0.006% by weight

Sulfur (S) forms a sulfide such as MnS, and the sulfide can inhibit grain growth. As a result, since the iron loss increases as S increases, the upper limit is set to 0.006 wt%. More specifically, 0.0001 to 0.005% by weight of S may be contained.

Al: 6 wt% or less

Aluminum (Al) is an element effective for increasing the intrinsic resistance of a steel and reducing iron loss, and is a ferrite stabilizing element. In addition, it is a useful element because it can prevent phase transformation to austenite at high temperature depending on the addition amount. However, if too much Al is contained, the saturation magnetic flux is greatly reduced, and the excitation effective current remarkably increases when the motor is driven after fabrication. Further, due to the development of the secondary phase, cold rolling may become difficult. Therefore, Al can be contained in an amount of 6% by weight or less. More specifically, Al may be contained in an amount of 3% by weight or less. And more specifically 0.001 to 2% by weight of Al.

N: 0.005 wt% or less

Nitrogen (N) is a harmful element that forms nitrides, inhibits grain growth, and increases iron loss. Therefore, the upper limit is set to 0.005 wt%. More specifically, N may be contained in an amount of 0.003% by weight or less. More specifically, N may be contained in an amount of 0.0001 to 0.003% by weight.

Be: 0.0002 to 0.003 wt%

Beryllium (Be) is an important element in one embodiment of the present invention. As described above, in the Si and P additionally added steels, the grain boundaries are bonded to Fe or bonded to C or the like to form precipitates such as carbides, thereby suppressing the segregation effect at the grain boundaries of P, and thereby the magnetic flux density Is known as a harmful element. However, in an embodiment of the present invention, by appropriately adding it, the amount of Be precipitates bonded to the Fe-Be precipitates or carbides is controlled, and the effect of improving the aggregate structure by segregation of P is strengthened, and the magnetic flux density, It is possible to improve the anisotropy of the surface. In one embodiment of the present invention, Be is contained in an amount of 0.0002 to 0.003% by weight. More specifically, it may contain 0.0003 to 0.002% by weight of Be. And more specifically 0.0003 to 0.001% by weight of Be.

The non-oriented electrical steel sheet according to one embodiment of the present invention may further contain at least one of Sb and Sn in the following ranges in addition to the above-described alloy components.

0.001 to 0.1% by weight of Sb, 0.001 to 0.1% by weight of Sn,

The antimony (Sb) is a grain boundary segregation element and has an effect of improving the magnetic flux density by controlling the aggregate structure due to crystal growth during annealing. However, it acts in a joint with P, so it is added in the range of 0.001 to 0.1 wt% .

Tin (Sn) has an effect of improving the magnetic flux density because the action during annealing in the Si and P high added steels is similar to that of Sb, and therefore it can be added in the range of 0.001 to 0.1 wt%. More specifically, it may further include at least one of 0.005 to 0.08% by weight of Sb and 0.005 to 0.08% by weight of Sn.

In one embodiment of the present invention, the non-oriented electrical steel sheet further comprises at least one of 0.001 to 0.1% by weight of Sb and 0.001 to 0.1% by weight of Sn in the above alloy component, meaning 0.001 to 0.1% by weight of Sb, , Further comprising 0.001 to 0.1% by weight of Sn, or 0.001 to 0.1% by weight of Sb and 0.001 to 0.1% by weight of Sn.

The non-oriented electrical steel sheet according to one embodiment of the present invention may further contain at least one of Ca and Mg in addition to the above-described alloy components.

Ca: 0.0005 to 0.005 wt%, Mg: 0.0005 to 0.003 wt%

Calcium (Ca) is an element that forms sulfides and oxides. When added in large amounts, calcium (Ca) binds with Ca and oxygen in the steel to form precipitates, thereby slowing the crystal growth rate. The addition amount thereof is limited to 0.005% by weight or less. At this time, Ca may be expected to have an effect of promoting grain growth by coarsening the sulfide when properly added, so the lower limit of Ca is set to 0.0005% by weight.

Magnesium (Mg) is similar to Ca in the annealing in the Si and P highly-doped steels, and combines with S at high temperature to form MgS, thereby slowing the crystal growth rate, , The addition amount thereof is limited to 0.003% by weight or less. At this time, Mg may be expected to have an effect of promoting the grain growth by coarsening the sulfide when properly added, so that the lower limit is set to 0.0005 wt%.

Further, in the non-oriented electrical steel sheet of the present invention, the balance other than the above-mentioned components is Fe and inevitable impurities. However, if the effect of the present invention is not impaired, the inclusion of other elements is not excluded.

Ti, Nb, V, Mo, and Cu are used as the impurity element, and Ti, Nb, V, and Mo are required to be 0.005 wt% or less and 0.025 wt% or less, respectively.

The non-oriented electrical steel sheet according to an embodiment of the present invention may have an average crystal grain size of 50 to 200 탆. The magnetic properties of the non-oriented electrical steel sheet are superior in the above-mentioned range.

The non-oriented electrical steel sheet according to one embodiment of the present invention can obtain excellent magnetic flux density (B50) and iron loss (W15 / 50) by adding an appropriate amount of Be. Specifically, the magnetic flux density (B50) of the non-oriented electrical steel sheet may be 1.68 T or more and the iron loss (W15 / 50) may be 2.65 W / kg or less. More specifically, the magnetic flux density (B50) of the non-oriented electrical steel sheet may be 1.69 to 1.75 T and the iron loss (W15 / 50) may be 1.7 to 2.55 W / kg.

The magnetic flux density B50 is a magnetic flux density at a magnetic force of 5000 A / m measured by using a value measured in the longitudinal direction in the rolling direction and a value measured in the longitudinal direction measured in the direction perpendicular to the rolling direction in half. W15 / 50 means an iron loss when a magnetic flux density of 1.5 T is induced at a frequency of 50 Hz.

The non-oriented electrical steel sheet according to one embodiment of the present invention can improve anisotropy of magnetic flux density by adding an appropriate amount of Be. Specifically, the ratio (B50L / B50D) of the magnetic flux density in the rolling direction (B50L) to the magnetic flux density (B50D) in the direction of the angle of 45 degrees with the rolling direction can be 1.07 or less. When the anisotropy of the magnetic flux density is excellent, there is a merit that the vibration when the motor rotates is small. Particularly when the magnetic moment is less than 1.07, the difference in magnetoresistance between the iron cores generated by the anisotropy in the motor core decreases, There is an advantage that it can be prevented. More specifically, B50L / B50D may be 1.06 or less.

The non-oriented electrical steel sheet according to an embodiment of the present invention may have a thickness of 0.09 to 0.70 mm.

A method of manufacturing a non-oriented electrical steel sheet according to an embodiment of the present invention includes: C: 0.01% or less (excluding 0%); Si: 1.5 to 4.5%; Mn: 0.03 to 3% (Excluding 0%), N: 0.005% or less (excluding 0%), and Be: 0.0002 to 0.003% (inclusive) And the remainder comprising Fe and unavoidable impurities; Heating the slab; Hot rolling the slab to produce a hot rolled sheet; A step of cold-rolling the hot-rolled sheet to produce a cold-rolled sheet, and a step of finally annealing the cold-rolled sheet.

Each step will be described in detail below.

First, slabs are manufactured. The reason why the addition ratio of each composition in the slab is limited is the same as the reason for limiting the composition of the non-oriented electrical steel sheet described above, so repeated description is omitted. The composition of the slab is substantially the same as that of the non-oriented electrical steel sheet because the composition of the slab does not substantially change during the manufacturing process such as hot rolling, hot rolling annealing, cold rolling and final annealing, which will be described later.

Next, heat the slab. Specifically, the slab is charged into a heating furnace and heated to 1100 to 1250 占 폚. When heated at a temperature exceeding 1250 DEG C, the precipitate is redissolved and may be precipitated finely after hot rolling.

The heated slab is hot-rolled to 2 to 2.3 mm to produce a hot-rolled sheet. In the step of preparing the hot rolled sheet, the hot rolling temperature may be 800 to 1000 캜.

Next, the hot-rolled sheet is subjected to hot-rolled sheet annealing. The hot-rolled hot-rolled sheet can be subjected to hot-rolled sheet annealing at a temperature of 950 캜 to 1150 캜 for 10 seconds to 30 minutes. The hot-rolled sheet annealing is performed in order to increase the orientation favorable to magnetism as required, and may be omitted.

Next, the hot rolled sheet is pickled and cold rolled to a predetermined thickness. But it can be cold-rolled to a final thickness of 0.09 to 0.70 mm by applying a reduction ratio of 70 to 95%.

The step of producing the cold rolled sheet may include one cold rolling step or may include two or more cold rolling steps with intermediate annealing in between.

The cold-rolled sheet is subjected to final annealing so that the average grain diameter is 50 to 200 占 퐉. The final annealing temperature may be 750 to 1100 占 폚. If the final annealing temperature is too low, recrystallization may not occur sufficiently, and if the final annealing temperature is too high, rapid growth of crystal grains may occur and the magnetic flux density and high-frequency iron loss may be lowered. More specifically, final annealing can be performed at a temperature of 950 to 1050 캜. In the final annealing process, all the processed structures formed in the previous cold rolling stage can be recrystallized (i.e., 99% or more).

The atmosphere of the final annealing may be performed in a nitrogen atmosphere of 10 to 30% by volume of hydrogen and the remainder, and the annealing time may be 10 seconds to 1 minute.

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

Example

The molten steel obtained in the converter was degassed to obtain a slab having a composition of various components shown in the following Tables 1 and 2 and a remainder made of Fe and unavoidable impurities, followed by continuous casting. Thereafter, heating at 1150 DEG C for 1 hour was performed. Thereafter, hot rolling was carried out at a finish rolling temperature of 850 占 폚 and rolled on a coil at a temperature of 650 占 폚 to obtain a hot rolled sheet having a thickness of 2 mm. The hot-rolled sheet was subjected to hot-rolled sheet annealing in an atmosphere of nitrogen at 1020 캜 for 20 seconds or longer to be annealed, followed by cold rolling to obtain a cold-rolled sheet having the thicknesses listed in Table 2 below, And then subjected to finish annealing under the temperature conditions shown in Table 2 below in a nitrogen atmosphere.

SST specimens having a width of 60 mm and a length of 60 mm were cut from the thus obtained cold-rolled annealing sheet in the rolling direction (L direction) and the 45-degree direction (D direction) in the rolling direction, 50 and magnetic flux density B50, and the following (B50L / B50D) for the anisotropy measurement, respectively, and the results are summarized in Table 3.

Grade (weight%) C Si Mn P Al S N One 0.0026 3.13 0.129 0.026 0.12 0.0017 0.0038 2 0.0013 3.11 0.065 0.013 0.59 0.0024 0.0023 3 0.0027 3.13 0.136 0.027 0.22 0.0016 0.0017 4 0.0018 3.18 0.413 0.083 0.64 0.0039 0.0021 5 0.0007 3.2 0.478 0.096 0.91 0.0086 0.0025 6 0.0007 3.11 0.033 0.0067 0.23 0.0004 0.0033 7 0.0006 3.11 0.065 0.0057 0.89 0.0001 0.0009 8 0.0031 3.13 0.157 0.031 0.96 0.0029 0.0061 9 0.002 3.12 0.099 0.02 0.95 0.0017 0.0047 10 0.0031 3.2 0.029 0.098 0.75 0.0065 0.0047 11 0.0025 3.13 0.125 0.025 0.24 0.0016 0.0036 12 0.0075 3.2 0.5 0.1 0.57 0.0052 0.0026 13 0.0043 3.18 0.405 0.081 0.002 0.0033 0.0043 14 0.0042 3.14 0.211 0.042 0.0031 0.0035 0.0031 15 0.0032 3.17 0.336 0.067 0.0043 0.0024 0.0034 16 0.0022 3.12 3.21 0.022 0.13 0.0016 0.0039 17 0.014 3.14 0.199 0.04 0.92 0.003 0.0042 18 0.0032 3.13 0.16 0.032 0.45 0.0026 0.0023 19 0.0023 1.23 0.113 0.023 0.98 0.0014 0.0035 20 0.0015 1.43 0.073 0.015 0.63 0.0013 0.0049 21 0.0023 0.95 0.114 0.023 0.62 0.0022 0.0031 22 0.0025 3.12 0.123 0.025 0.08 0.0011 0.0045 23 0.0033 4.7 0.163 0.033 0.12 0.0015 0.0026 24 0.0012 3.11 0.061 0.012 0.15 0.0003 0.0013 25 0.0029 3.13 0.144 0.029 0.09 0.0012 0.0023 26 0.0043 3.17 0.34 0.068 0.42 0.0037 0.0007 27 0.0012 3.2 0.489 0.098 0.05 0.0053 0.003 28 0.0023 3.18 0.417 0.083 0.97 0.0048 0.0032 29 0.0043 3.14 0.213 0.043 0.62 0.0035 0.0029 30 0.0031 3.17 0.33 0.066 0.26 0.0025 0.0021 31 0.0023 3.17 0.343 0.069 0.15 0.0029 0.0023 32 0.0028 3.13 0.138 0.028 6.2 0.0023 0.0007 33 0.0017 3.12 0.085 0.017 0.7 0.0029 0.0049 34 0.0016 3.12 0.08 0.016 0.75 0.0008 0.0029 35 0.003 3.13 0.152 0.03 0.27 0.0019 0.0033 36 0.0001 3.1 0.0035 0.02 0.46 0.007 0.0038 37 0.0022 3.12 0.111 0.007 0.73 0.0006 0.0014 38 0.0033 3.13 0.046 0.033 0.28 0.002 0.0048 39 0.0015 3.17 0.328 0.066 0.03 0.0023 0.0025 40 0.0023 3.15 0.211 0.042 0.61 0.0015 0.0019

Steel grade
(weight%) Be Sb Sn Ca Mg Plate thickness
(mm) Final annealing temperature
(° C) One 0.0038 - 0.01 - - 0.35 1000 2 0.002 - 0.01 - - 0.35 1000 3 0.0006 0.01 0.01 - - 0.35 980 4 0.0016 - 0.01 - - 0.35 1040 5 0.002 - 0.01 - - 0.35 1000 6 0.0021 - 0.01 - - 0.35 1000 7 0.0015 - 0.01 - - 0.35 1000 8 0.0021 - 0.01 - - 0.35 1000 9 0.0047 - 0.01 - - 0.35 1000 10 0.0002 - 0.01 - - 0.35 1000 11 0.0034 - 0.01 - - 0.35 1000 12 0.0002 0.005 - - - 0.35 1040 13 0.0007 - - - - 0.35 1000 14 0.0005 - 0.01 - - 0.35 980 15 0.0009 - 0.03 - - 0.35 1000 16 0.0013 - 0.03 - - 0.35 1000 17 0.0021 - 0.03 - - 0.35 1000 18 0.0003 - 0.03 - - 0.1 1000 19 0.0004 - 0.03 - - 0.35 1000 20 0.0006 - 0.03 - - 0.35 1000 21 0.0003 - 0.03 - - 0.35 1000 22 0.0009 0.05 0.03 - - 0.35 1000 23 0.0013 - 0.03 - - 0.35 1000 24 0.0048 - 0.03 - - 0.35 1000 25 0.0008 - 0.05 - - 0.65 1000 26 0.0009 - 0.05 - - 0.25 1000 27 0.0038 - - - - 0.35 1000 28 0.0047 - - - - 0.35 1000 29 0.0019 0.05 - - - 0.35 1000 30 0.0061 - - - - 0.35 1000 31 0.0054 - - - - 0.35 1000 32 0.0021 - - - - 0.35 1000 33 0.0005 - - 0.002 - 0.5 1000 34 0.0053 - - - - 0.35 1000 35 0.0014 - - 0.0006 - 0.35 1000 36 0.0043 - - - - 0.35 1000 37 0.0023 - - - - 0.35 1000 38 0.0019 - - - 0.002 0.35 1000 39 0.0025 - - - 0.0001 0.35 1000 40 0.0001 - - - - 0.35 1000

Steel grade W15 / 50
(W / kg) B50
(T) B50L / B50D Remarks One 2.528 1.633 1.012 Comparative Example 2 2.337 1.702 1.059 Honor 3 2.505 1.691 1.022 Honor 4 2.184 1.683 1.064 Honor 5 2.665 1.668 1.091 Comparative Example 6 2.525 1.623 1.023 Comparative Example 7 2.639 1.623 1.089 Comparative Example 8 2.746 1.636 1.096 Comparative Example 9 2.742 1.63 1.095 Comparative Example 10 2.503 1.669 1.075 Comparative Example 11 2.525 1.633 1.024 Comparative Example 12 2.632 1.692 1.057 Honor 13 1.941 1.712 1.059 Honor 14 2.504 1.709 1.061 Honor 15 2.396 1.713 1.065 Honor 16 1.88 1.631 1.013 Comparative Example 17 2.673 1.64 1.092 Comparative Example 18 1.685 1.684 1.045 Honor 19 2.526 1.665 1.098 Comparative Example 20 2.548 1.659 1.063 Comparative Example 21 2.543 1.674 1.062 Comparative Example 22 2.507 1.7 1.008 Honor 23 1.873 1.636 1.012 Comparative Example 24 2.536 1.626 1.015 Comparative Example 25 4.12 1.705 1.035 Honor 26 1.873 1.683 1.042 Honor 27 1.693 1.669 1.005 Comparative Example 28 2.729 1.662 1.097 Comparative Example 29 2.366 1.693 1.062 Honor 30 2.719 1.653 1.026 Comparative Example 31 2.721 1.654 1.015 Comparative Example 32 1.975 1.634 1.023 Comparative Example 33 2.743 1.702 1.07 Honor 34 2.726 1.628 1.075 Comparative Example 35 2.021 1.695 1.027 Honor 36 2.735 1.62 1.046 Comparative Example 37 2.483 1.631 1.073 Comparative Example 38 2.314 1.701 1.028 Honor 39 1.782 1.691 1.003 Honor 40 1.982 1.674 1.043 Comparative Example

As can be seen from Tables 1 to 3, it can be confirmed that the inventive example in which an appropriate amount of Be is added has excellent iron loss and magnetic flux density and is also excellent in anisotropy.

On the other hand, the comparative example, which does not satisfy the alloy components proposed in the embodiment of the present invention, shows that the magnetic flux density is poor, and further, anisotropy and iron loss are poor. In particular, it can be seen that the magnetic flux density is poor and the anisotropy and iron loss are also poor in the steel types 1, 9, 11, 24, 27, 28, 30, 31, 34, 36 and 40 which do not contain the proper amount of Be.

It will be understood by those skilled in the art that various changes in form and details may be made therein without departing from the spirit and scope of the present invention as defined by the following claims. As will be understood by those skilled in the art. It is therefore to be understood that the above-described embodiments are illustrative in all aspects and not restrictive.

Claims (8)

C: not more than 0.01% (excluding 0%), Si: 1.5 to 4.5%, Mn: 0.03 to 3%, P: 0.01 to 0.12%, S: 0.006% , Al: not more than 6% (excluding 0%), N: not more than 0.005% (excluding 0%) and Be: 0.0002 to 0.003%, the remainder being Fe and other unavoidable impurities Steel plate. The method according to claim 1,
0.001 to 0.1% by weight of Sb and 0.001 to 0.1% by weight of Sn. The method according to claim 1,
0.0005 to 0.005% by weight of Ca, and 0.0005 to 0.003% by weight of Mg. The method according to claim 1,
The non-oriented electrical steel sheet having an average grain size of 50 to 200 占 퐉. The method according to claim 1,
Wherein the ratio (B50L / B50D) of the magnetic flux density in the rolling direction (B50L) to the magnetic flux density (B50D) in the direction of the rolling direction and the direction of the angle of 45 DEG is 1.07 or less. C: not more than 0.01% (excluding 0%), Si: 1.5 to 4.5%, Mn: 0.03 to 3%, P: 0.01 to 0.12%, S: 0.006% , Al: not more than 6% (excluding 0%), N: not more than 0.005% (excluding 0%) and Be: 0.0002 to 0.003%, the balance being Fe and unavoidable impurities step;
Heating the slab;
Hot rolling the slab to produce a hot rolled sheet;
Cold rolling the hot rolled sheet to produce a cold rolled sheet; and
And finally annealing the cold rolled steel sheet. The method according to claim 6,
Further comprising a step of annealing the hot rolled steel sheet after the step of producing the hot rolled steel sheet. The method according to claim 6,
Wherein the step of producing the cold-rolled sheet comprises a step of cold-rolling once or a step of cold-rolling at least two times with intermediate annealing in between.