KR102013820B1 - Non-oriented electrical steel sheet method for manufacturing the same - Google Patents

Abstract

Non-oriented electrical steel sheet according to an embodiment of the present invention by weight%, C: 0.01% or less (excluding 0%), Si: 2.46 to 4.5% by weight, Al: 6% by weight or less (excluding 0%) ), Mn: 0.03 to 3% by weight, P: 0.01 to 0.08% by weight, S: 0.001 to 0.01% by weight, N: 0.005% by weight or less (excluding 0%), and Sr: 0.0001 to 0.005% by weight , Balance includes Fe and other unavoidable impurities.

Description

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

It relates to a non-oriented electrical steel sheet and a method for producing a non-oriented electrical steel sheet. Specifically, the present invention relates to a method for producing non-oriented electrical steel sheets and non-oriented electrical steel sheets having excellent magnetic properties by adding an appropriate amount of Sr to Si and Al-containing steels.

Recently, the use of high-efficiency motors has greatly increased due to the enhanced efficiency regulation of motors. In order to improve efficiency, such a motor needs to lower iron loss or copper loss, and various methods are used for this purpose. In particular, both of these methods can greatly affect the magnetism of the non-oriented electrical steel sheet core material. Accordingly, manufacturers of motors are turning from the use of non-oriented electrical steel sheets having high iron loss to the use of non-oriented electrical steel sheets having low iron loss.

On the other hand, in order to reduce copper loss, a method of lowering the design magnetic flux density or lowering an excitation current in the design magnetic flux is used. In order to use the latter method, it is necessary to increase the high magnetic flux density of the non-oriented electrical steel sheet.

In particular, the high magnetic flux density material has the advantage of improving torque, and in the case of frequent motors with high n-off, the large output can be produced at a quick time.

In order to obtain non-oriented electrical steel sheet having high magnetic flux density, various alloy compositions have been proposed. Strontium (Sr) is an element distributed in various trace amounts on Earth. As an example of the addition of Sr, a technique is known in which a solidified structure of a cast steel is produced in a uniform equiaxed crystal by adding Sr to molten steel in a continuous casting method of molten steel for non-oriented electrical steel sheet. However, this technique has a problem in that iron loss characteristics are greatly deteriorated because inevitably small amounts of Si and Al are added in order to improve workability and magnetic flux density characteristics such as rolling.

An object of the present invention is to provide a non-oriented electrical steel sheet and a non-oriented electrical steel sheet. Specifically, by adding an appropriate amount of Sr to the Si and Al high-containing steels, to provide a non-oriented electrical steel sheet and a non-oriented electrical steel sheet having excellent magnetic properties.

Non-oriented electrical steel sheet according to an embodiment of the present invention by weight%, C: 0.01% or less (excluding 0%), Si: 2.46 to 4.5% by weight, Al: 6% by weight or less (excluding 0%) ), Mn: 0.03 to 3% by weight, P: 0.01 to 0.08% by weight, S: 0.001 to 0.01% by weight, N: 0.005% by weight or less (excluding 0%), and Sr: 0.0001 to 0.005% by weight , Balance includes Fe and other unavoidable impurities.

Non-oriented electrical steel sheet according to an embodiment of the present invention satisfies the following equation 1.

[Equation 1]

[Si] + [Al] ≥ 2.6

(In Formula 1, [Si] and [Al] represent the content of Si and Al (% by weight), respectively.)

Non-oriented electrical steel sheet according to an embodiment of the present invention may satisfy the following equation 2.

[Equation 2]

0.8 ≤ [Sr] / ([Si] + [Al]) × 10000 ≤ 8

(In formula 2, [Sr], [Si] and [Al] represent the contents (wt%) of Sr, Si, and Al, respectively.)

It may further include at least one of Sb: 0.001 to 0.1% by weight and Sn: 0.001 to 0.1% by weight.

It may further comprise at least one of Ca: 0.0005 to 0.005% by weight and Mg: 0.0005 to 0.003% by weight.

The average grain size may be 50 to 200 μm.

The ratio (B50L / B50D) of the magnetic flux density B50L in the rolling direction to the magnetic flux density B50D in the rolling direction and the direction of the 45 ° angle may be 1.085 or less.

Method for producing a non-oriented electrical steel sheet according to an embodiment of the present invention by weight, C: 0.01% or less (excluding 0%), Si: 2.46 to 4.5% by weight, Al: 6% by weight or less (0% Mn: 0.03 to 3% by weight, P: 0.01 to 0.08% by weight, S: 0.001 to 0.01% by weight, N: 0.005% by weight or less (excluding 0%), and Sr: 0.005% by weight or less ( Producing a slab comprising Fe and unavoidable impurities; 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 final annealing the cold rolled sheet.

The slab may satisfy the following formula 1.

[Equation 1]

[Si] + [Al] ≥ 2.6

(In Formula 1, [Si] and [Al] represent the content of Si and Al (% by weight), respectively.)

After preparing the hot rolled sheet, the method may further include annealing the hot rolled sheet.

The manufacturing of the cold rolled sheet may include one cold rolling or two or more cold rolling between intermediate annealing.

In the non-oriented electrical steel sheet manufactured according to the embodiment of the present invention, in the Si, Al high-containing steel species, by adding P to improve the texture, and by adding a new trace additive element Sr, the texture is further improved. .

As a result, it is possible to provide a non-oriented electrical steel sheet excellent in magnetic properties, in particular magnetic density density.

In addition, the non-oriented electrical steel sheet according to an embodiment of the present invention can be usefully used for an efficiency motor, a motor of high power, high torque characteristics, a core material of a generator, and the like.

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 meaning of "comprising" embodies a particular characteristic, region, integer, step, operation, element and / or component, and the presence of other characteristics, region, integer, step, operation, element and / or component It does not exclude the addition.

When a portion is referred to as "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.

Unless 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 to have a meaning consistent with the related technical literature and the presently disclosed contents, and are not interpreted in an ideal or very formal sense unless defined.

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

In an embodiment of the present invention, the meaning of further including an additional element means to include iron (Fe), which is the balance 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.

In an embodiment of the present invention, in the non-oriented electrical steel sheet is Si, Al high-containing steel, by adding P to improve the texture, and by adding a new trace additive element Sr, the texture is further improved.

Non-oriented electrical steel sheet according to an embodiment of the present invention by weight%, C: 0.01% or less (excluding 0%), Si: 2.46 to 4.5% by weight, Al: 6% by weight or less (excluding 0%) ), Mn: 0.03 to 3% by weight, P: 0.01 to 0.08% by weight, S: 0.001 to 0.01% by weight, N: 0.005% by weight or less (excluding 0%), and Sr: 0.0001 to 0.005% by weight , Balance includes Fe and other unavoidable impurities.

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

C: 0.01 wt% or less

When a large amount of carbon (C) is contained even after the final annealing, the magnetic aging is caused and iron loss is greatly increased. Therefore, the upper limit is made 0.01% by weight. More specifically, it adjusts to 0.005 weight% or less. More specifically, it may include 0.0001 to 0.005% by weight of C.

Si: 2.46 to 4.5 wt%

Silicon (Si) is an element and an ferrite stabilizing element effective for increasing the specific resistance of steel and reducing iron loss. It is preferable to add a large amount of Si. However, when too much Si is included, the saturation magnetic flux is greatly reduced due to the development of the secondary phase, and the excitation effective current is significantly increased during driving after the motor is manufactured. Therefore, Si is included at 2.46 to 4.5% by weight. More specifically, it may include 2.46 to 3.5 wt% of Si.

Al: 6 wt% or less

Aluminum (Al) is an element effective in increasing the resistivity of steel and reducing iron loss and is a ferrite stabilizing element. In addition, depending on the amount added, austenite can prevent phase transformation even at high temperatures, and is a useful element. However, when Al is included too much, the saturation magnetic flux is greatly reduced, and the excitation effective current is significantly increased during driving after the motor is manufactured. Also, due to the development of the secondary phase, cold rolling can be difficult. Therefore, Al may be included in an amount of 6 wt% or less. More specifically, it may include 3 wt% or less of Al. More specifically, it may include 0.001 to 2% by weight of Al.

Si and Al are both ferrite stabilizing elements, and when added from pure iron, they are cast into a single ferrite single phase after solidification of the cast steel when the sum of the two components is 2.1% by weight or more. In one embodiment of the present invention, since austenite stabilizing elements are also included, such as C and Mn, 2.6 wt% or more is added to form a ferrite single phase. That is, the following formula 1 can be satisfied.

[Equation 1]

[Si] + [Al] ≥ 2.6

(In Formula 1, [Si] and [Al] represent the content of Si and Al (% by weight), respectively.)

As the steel is solidified and cast into a ferrite single phase, it becomes a thin cold rolled sheet from the slab without undergoing phase transformation and undergoes many deformations, thereby obtaining a strong deformation structure. Can be obtained. More specifically, the total amount of Si and Al may be 2.6 to 4.0 wt%. More specifically, the total amount of Si and Al may be 3.0 to 3.5% by weight.

Mn: 0.03 to 3 wt%

Manganese Mn plays a role of preventing brittleness during hot rolling. If it contains too little Mn, the above-mentioned role cannot be properly performed. On the contrary, when too much Mn is included, the proportion of Fe in the steel is reduced and the saturation magnetic flux density decreases. Therefore, Mn may be included in the range of 0.03 to 3% by weight. More specifically, Mn may be included in an amount of 0.05 wt% to 1.0 wt%.

P: 0.01 to 0.08 wt%

Phosphorus (P) is a major element for improving the texture of aggregates. By adding P, the texture can be improved and the magnetic flux density can be increased. When P is included too little, the effect of improving the magnetic flux density cannot be sufficiently obtained. Conversely, if too much P is included, the brittleness of the steel can be maximized, making cold rolling difficult. Therefore, P may be included in an amount of 0.01 to 0.08 wt%. More specifically, it may include 0.03% to 0.07% by weight of P.

S: 0.001 to 0.01 wt% or less

Sulfur (S) is an element that segregates the surface and the grain boundary and is an element which helps to improve the magnetic flux density and lower the anisotropy by influencing the development of the aggregate structure caused by the surface segregation during annealing when an appropriate amount is added. If too little sulfur is included, this effect cannot be obtained properly. If it contains too much sulfur, sulfides, such as MnS, are formed and particle growth can be inhibited by this sulfide. Eventually, iron loss can increase as S increases. Therefore, S may be included in 0.001 to 0.01% by weight. More specifically, it may include 0.001 to 0.005% by weight of S.

N: 0.005 wt% or less

Nitrogen (N) is a harmful element that forms nitrides, inhibits particle growth, and increases iron loss. Therefore, an upper limit is made into 0.005 weight%. More specifically, N may be 0.003% by weight or less. More specifically, N may be included in 0.0001 to 0.003% by weight.

Sr: 0.0001 to 0.005 wt%

Strontium (Sr) is an important element in one embodiment of the present invention. As described above, by delaying the performance of Si, Al high addition, and S and P addition steel, segregation of S and P on the surface of the steel sheet during the performance to be removed by scab or the like, and in steel C, N, Ti It is a harmful element which exists as a precipitate by combining with etc. and suppresses segregation effect of S and P in a post process, and thereby reduces the magnetic flux density of the steel plate after annealing. Therefore, the content of Sr is limited to 0.005% by weight or less. However, if too little Sr is added, a problem arises in that the surface quality is degraded by S and P segregating on the surface with excessive concentration during the playing process. Therefore, the content of Sr is limited to 0.0001% by weight or more. More specifically, it may comprise 0.0003 to 0.003% by weight.

In addition, in one embodiment of the present invention can satisfy the following formula 2.

[Equation 2]

0.8 ≤ [Sr] / ([Si] + [Al]) × 10000 ≤ 8

(In formula 2, [Sr], [Si] and [Al] represent the contents (wt%) of Sr, Si, and Al, respectively.)

When the following formula 2 is satisfied, an electrical steel sheet with high magnetic flux density and low anisotropy can be obtained.

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

Sb: 0.001 to 0.1 wt%, Sn: 0.001 to 0.1 wt%

Antimony (Sb) is an intergranular segregation element, and has an effect of controlling the aggregate structure according to crystal growth during annealing to improve the magnetic flux density. However, since antimony (Sb) is co-acting with P, it can be added in the range of 0.001 to 0.1 wt%. Can be.

Tin (Sn) can be added in the range of 0.001 to 0.1% by weight since the action during annealing in the Si, Al, P high-added steels is similar to Sb, and has an effect of improving the magnetic flux density. More specifically, Sb: 0.005 to 0.08% by weight and Sn: 0.005 to 0.08% by weight may further include one or more.

In one embodiment of the present invention, the non-oriented electrical steel sheet further comprises at least one of Sb: 0.001 to 0.1% by weight and Sn: 0.001 to 0.1% by weight to the above-described alloy components, Sb: 0.001 to 0.1% by weight It further comprises, or further comprising: 0.001 to 0.1% by weight of Sn: 0.001 to 0.1% by weight of Sb and 0.00 to 0.1% by weight.

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, and when added in large amounts, it combines with Ca and oxygen in steel to form precipitates, thereby slowing down the crystal growth rate and thus controlling the texture control effect during annealing by P. Since it suppresses, the addition amount is restrict | limited to 0.005 weight% or less. At this time, Ca may be expected to have an effect of coarsening sulfides when appropriately added to promote grain growth, so the lower limit thereof is made 0.0005% by weight.

Magnesium (Mg) is similar to Ca in the action of annealing in high-added Si, Al, and P steels, so that it combines with S at high temperature to form MgS, thereby slowing down the crystal growth rate, thereby In order to suppress the effect of controlling the texture during annealing, the amount thereof is limited to 0.003% by weight or less. At this time, Mg may be expected to have an effect of coarsening sulfides when appropriately added to promote grain growth, so the lower limit thereof is made 0.0005% by weight.

In addition, in the non-oriented electrical steel sheet of this invention, remainder other than the above-mentioned component is Fe and an unavoidable impurity. However, as long as it is in the range which does not inhibit the effect of this invention, containing of another element is not excluded.

As impurity elements, there are Ti, Nb, V, Mo, Cu, and the like. Ti, Nb, V, and Mo need to be controlled at 0.005 wt% or less and Cu at 0.025 wt% or less, respectively.

Non-oriented electrical steel sheet according to an embodiment of the present invention may have an average grain size of 50 to 200㎛. In the aforementioned range, the magnetism of the non-oriented electrical steel sheet is more excellent.

In the non-oriented electrical steel sheet according to one embodiment of the present invention, by adding an appropriate amount of Sr, excellent magnetic flux density (B50) and iron loss (W15 / 50) can be obtained. Specifically, the magnetic flux density (B50) of the non-oriented electrical steel sheet is 1.68T or more, iron loss (W15 / 50) may be less than 2.85W / kg. More specifically, the magnetic flux density (B50) of the non-oriented electrical steel sheet is 1.69 to 1.75T, iron loss (W15 / 50) may be 1.7 to 2.55W / kg.

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

In the non-oriented electrical steel sheet according to one embodiment of the present invention, an anisotropy of magnetic flux density may be improved by adding an appropriate amount of Sr. Specifically, the ratio (B50L / B50D) of the magnetic flux density B50L in the rolling direction to the magnetic flux density B50D in the rolling direction and the direction of the 45 ° angle may be 1.085 or less. When the anisotropy of magnetic flux density is excellent, the rotational vibration of the motor is small when it is laminated and used as the iron core of the motor, and in particular, when it is 1.085 or less, the magnetic resistance in the laminated iron core of the motor is more constant and local along the direction. There is an advantage that the occurrence of phosphorus saturation is small. More specifically, B50L / B50D may be 1.07 or less.

In the non-oriented electrical steel sheet according to one embodiment of the present invention, the plate thickness may be 0.09 to 0.70 mm.

Method for producing a non-oriented electrical steel sheet according to an embodiment of the present invention by weight% by weight, C: 0.01% or less (excluding 0%), Si: 2.46 to 4.5% by weight, Al: 6% by weight or less (Excluding 0%), Mn: 0.03 to 3% by weight, P: 0.01 to 0.08% by weight, S: 0.001 to 0.01% by weight, N: 0.005% by weight or less (excluding 0%), and Sr: 0.0001 to Producing a slab comprising 0.005% by weight, the balance comprising Fe and inevitable impurities; 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 final annealing the 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 in the manufacturing process of hot rolling, hot rolling annealing, cold rolling, final annealing, and the like, the composition of the slab and the composition of the non-oriented electrical steel sheet are substantially the same.

In a converter, a degassing apparatus, etc., the steel of the component composition suitable for this invention can be melted, and a slab can be manufactured by continuous casting, ingot-digestion rolling, etc.

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

The heated slabs are hot rolled to 2 to 2.3 mm to produce hot rolled plates. Hot finishing rolling temperature in the step of producing a hot rolled sheet may be 800 to 1000 ℃.

Next, the hot rolled sheet is annealed. The hot rolled hot rolled sheet may be annealed for 10 seconds to 30 minutes at a temperature of 950 ° C to 1150 ° C. Hot-rolled sheet annealing is carried out in order to increase the orientation favorable to the magnetic, if necessary, may be omitted.

Next, the hot rolled sheet is pickled and cold rolled to a predetermined sheet thickness. 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 cold rolled so that the final thickness is 0.09 to 0.70mm.

The manufacturing of the cold rolled sheet may include one cold rolling or two or more cold rolling between intermediate annealing.

The cold rolled sheet is subjected to final annealing so that the average grain size is 50 to 200 µm. The final annealing temperature may be from 750 to 1100 ° C. If the final annealing temperature is too low, recrystallization does not occur sufficiently. If the final annealing temperature is too high, rapid growth of crystal grains may occur, which may lower magnetic flux density and high frequency iron loss. More specifically, the final annealing may be performed at a temperature of 950 to 1050 ° C. In the final annealing process, all of the processed tissue formed during the cold rolling step (ie, 99% or more) can be recrystallized.

The atmosphere of the final annealing can be carried out in 10 to 30% by volume hydrogen and the balance nitrogen atmosphere, the annealing time can be 10 seconds to 1 minute.

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

Example

The molten steel blown in the converter was degassed to have a composition of various components shown in Tables 1 and 2, and the remainder was dissolved in a steel containing Fe and unavoidable impurities, followed by continuous casting to prepare slabs. Then, heating of 1150 degreeC * 1 hr was performed. Thereafter, hot rolling was performed at a finish rolling temperature of 850 ° C., and the coil was wound at a temperature of 650 ° C. to obtain a hot rolled sheet having a sheet thickness of 2 mm. Subsequently, the hot rolled sheet was annealed in a nitrogen atmosphere at 1020 ° C. for 20 seconds or more, followed by cold rolling to form a cold rolled sheet having a thickness shown in Table 2 below, containing 20% hydrogen. In the nitrogen atmosphere, final annealing was performed under the temperature conditions shown in Table 2 below.

From the annealing plate obtained in this way, the SST test piece of width 60mm x length 60mm is cut out from 45 degree | times direction (D direction) to rolling direction (L direction) and rolling direction, and iron loss W15 / 50 based on IEC 60404-3. And (B50L / B50D) below for measuring magnetic flux density B50 and anisotropy, respectively, and the results are summarized in Table 3.

Steel grade
(weight%) C Si Al Mn P S N Sr One 0.0034 2.86 0.31 0.47 0.051 0.0031 0.0026 0.0009 2 0.0031 2.88 0.38 0.47 0.025 0.0027 0.0019 0.0003 3 0.0008 3.04 1.05 0.06 0.0067 0.0008 0.0035 0.011 4 0.0032 2.87 0.49 0.48 0.008 0.0004 0.0022 0.001 5 0.0025 2.92 0.57 0.08 0.02 0.0109 0.0023 0.0091 6 0.0031 2.87 1.11 0.42 0.025 0.0029 0.0033 0.009 7 0.0007 3.05 0.65 0.02 0.03 0.0015 0.0022 0.0039 8 0.0039 2.82 0.53 0.31 0.031 0.0039 0.002 0.0095 9 0.0016 2.98 0.4 0.06 0.036 0.0019 0.0043 0.0004 10 0.0034 2.72 0.0035 0.64 0.042 0.0051 0.0031 0.0005 11 0.0043 2.46 0.22 1.44 0.054 0.005 0.0032 0.0003 12 0.0035 2.22 3.98 0.1 0.098 0.0114 0.0025 0.0005 13 0.0051 2.24 0.54 1.61 0.13 0.003 0.0029 0.0053 14 0.0032 3.17 0.0043 0.336 0.067 0.0024 0.0034 0.0009 15 0.0022 3.12 0.13 3.21 0.022 0.0016 0.0039 0.0013 16 0.014 3.14 0.92 0.199 0.04 0.003 0.0042 0.0021 17 0.0032 3.13 0.45 0.16 0.032 0.0026 0.0023 0.0003 18 0.0023 1.23 0.98 0.113 0.023 0.0014 0.0035 0.0004 19 0.0015 1.43 0.63 0.073 0.015 0.0013 0.0049 0.0006 20 0.0023 0.95 0.62 0.114 0.023 0.0022 0.0031 0.0003 21 0.0025 3.12 0.08 0.123 0.025 0.0011 0.0045 0.0009 22 0.0033 4.7 0.12 0.163 0.033 0.0015 0.0026 0.0013 23 0.0012 3.11 0.15 0.061 0.012 0.0003 0.0013 0.0048 24 0.0029 3.13 0.09 0.144 0.029 0.0012 0.0023 0.0008 25 0.0043 3.17 0.42 0.34 0.068 0.0037 0.0007 0.0009 26 0.0012 3.2 0.05 0.489 0.098 0.0053 0.003 0.0038 27 0.0023 3.18 0.97 0.417 0.083 0.0048 0.0032 0.0047 28 0.0043 3.14 0.62 0.213 0.043 0.0035 0.0029 0.0019 29 0.0031 3.17 0.26 0.33 0.066 0.0025 0.0021 0.0061 30 0.0023 3.17 0.15 0.343 0.069 0.0029 0.0023 0.0054 31 0.0028 3.13 6.2 0.138 0.028 0.0023 0.0007 0.0021 32 0.0017 3.12 0.7 0.085 0.017 0.0029 0.0049 0.0005 33 0.0016 3.12 0.75 0.08 0.016 0.0008 0.0029 0.0053 34 0.003 3.13 0.27 0.152 0.03 0.0019 0.0033 0.0014 35 0.0001 3.1 0.46 0.0035 0.02 0.007 0.0038 0.0043 36 0.0022 3.12 0.73 0.111 0.007 0.0006 0.0014 0.0023 37 0.0033 3.13 0.28 0.046 0.033 0.002 0.0048 0.0019 38 0.0015 3.17 0.03 0.328 0.066 0.0023 0.0025 0.0025

Steel grade
(weight%) Sb Sn Ca Mg Equation 1 Equation 2 Plate thickness (mm) Final annealing temperature (℃) One 0.01 0.01 - - 3.17 2.84 0.35 980 2 0.05 0.03 - - 3.26 0.92 0.35 1000 3 - 0.01 - - 4.09 26.89 0.35 1000 4 - 0.01 - - 3.36 2.98 0.35 1000 5 - 0.01 - - 3.49 26.07 0.35 1000 6 - 0.01 - - 3.98 22.61 0.35 1000 7 - 0.01 - - 3.7 10.54 0.35 1000 8 - 0.01 - - 3.35 28.36 0.35 1000 9 - 0.01 - - 3.38 1.18 0.35 1000 10 - 0.01 - - 2.7235 1.84 0.35 980 11 - 0.01 - - 2.68 1.12 0.35 1040 12 - 0.01 - - 6.2 0.81 0.35 1000 13 - 0.01 - - 2.78 19.06 0.35 1000 14 - 0.03 - - 3.1743 2.84 0.35 1000 15 - 0.03 - - 3.25 4 0.35 1000 16 - 0.03 - - 4.06 5.17 0.35 1000 17 - 0.03 - - 3.58 0.84 0.1 1000 18 - 0.03 - - 2.21 1.81 0.35 1000 19 - 0.03 - - 2.06 2.91 0.35 1000 20 - 0.03 - - 1.57 1.91 0.35 1000 21 0.05 0.03 - - 3.2 2.81 0.35 1000 22 - 0.03 - - 4.82 2.7 0.35 1000 23 - 0.03 - - 3.26 14.72 0.35 1000 24 - 0.05 - - 3.22 2.48 0.65 1000 25 - 0.05 - - 3.59 2.51 0.25 1000 26 - - - - 3.25 11.69 0.35 1000 27 - - - - 4.15 11.33 0.35 1000 28 0.05 - - - 3.76 5.05 0.35 1000 29 - - - - 3.43 17.78 0.35 1000 30 - - - - 3.32 16.27 0.35 1000 31 - - - - 9.33 2.25 0.35 1000 32 - - 0.002 - 3.82 1.31 0.5 1000 33 - - - - 3.87 13.7 0.35 1000 34 - - 0.0006 - 3.4 4.12 0.35 1000 35 - - - - 3.56 12.08 0.35 1000 36 - - - - 3.85 5.97 0.35 1000 37 - - - 0.002 3.41 5.57 0.35 1000 38 - - - 0.0001 3.2 7.81 0.35 1000

Steel grade (% by weight) W15 / 50 (W / kg) B50 (T) B50L / B50D Remarks One 2.34 1.68 1.083 Inventive Example 2 1.829 1.692 1.046 Inventive Example 3 2.34 1.631 1.076 Comparative example 4 2.15 1.654 1.091 Comparative example 5 3.15 1.663 1.095 Comparative example 6 2.732 1.655 1.079 Comparative example 7 2.12 1.643 1.072 Comparative example 8 2.746 1.661 1.096 Comparative example 9 2.515 1.702 1.085 Inventive Example 10 2.85 1.683 1.057 Inventive Example 11 2.73 1.694 1.061 Inventive Example 12 3.41 1.669 1.075 Comparative example 13 2.34 1.668 1.091 Comparative example 14 2.396 1.713 1.065 Inventive Example 15 1.88 1.631 1.013 Comparative example 16 2.673 1.64 1.092 Comparative example 17 1.685 1.684 1.045 Inventive Example 18 2.526 1.665 1.098 Comparative example 19 2.548 1.659 1.073 Comparative example 20 2.543 1.674 1.072 Comparative example 21 2.507 1.7 1.008 Inventive Example 22 1.873 1.636 1.012 Comparative example 23 2.536 1.626 1.015 Comparative example 24 4.12 1.705 1.035 Inventive Example 25 1.873 1.683 1.042 Inventive Example 26 1.693 1.669 1.005 Comparative example 27 2.729 1.662 1.097 Comparative example 28 2.366 1.693 1.062 Inventive Example 29 2.719 1.653 1.026 Comparative example 30 2.721 1.654 1.015 Comparative example 31 1.975 1.634 1.023 Comparative example 32 2.743 1.702 1.07 Inventive Example 33 2.726 1.628 1.075 Comparative example 34 2.021 1.695 1.027 Inventive Example 35 2.735 1.62 1.046 Comparative example 36 2.483 1.631 1.073 Comparative example 37 2.314 1.701 1.028 Inventive Example 38 1.782 1.691 1.003 Inventive Example

As can be seen in Tables 1 to 3, the invention examples satisfying all of the alloy composition of one embodiment of the present invention can be confirmed that the iron loss, magnetic flux density is excellent, and also excellent anisotropy.

On the other hand, the comparative example does not satisfy the alloy component presented in one embodiment of the present invention can be confirmed that the magnetic flux density is poor, and furthermore, the anisotropy and iron loss is also poor. In particular, steel grades 3, 5, 6, 8, 13, 29, 30, and 33, which do not contain an appropriate amount of Sr, have poor magnetic flux density, and furthermore, poor anisotropy and iron loss. Steel grades 18, 19, and 20, which did not adequately contain the total amount of Si and Al, were also confirmed to have poor magnetic and anisotropy.

The present invention is not limited to the above embodiments, but may be manufactured in various forms, and a person skilled in the art to which the present invention pertains has another specific form without changing 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 (9)

By weight, C: 0.01% or less (excluding 0%), Si: 2.46 to 4.5% by weight, Al: 6% by weight or less (excluding 0%), Mn: 0.03 to 3% by weight, P: 0.01 To 0.08% by weight, S: 0.001 to 0.01% by weight, N: 0.005% by weight or less (excluding 0%), and Sr: 0.0001 to 0.005% by weight, the balance including Fe and other unavoidable impurities, Non-oriented electrical steel sheet that satisfies Equation 1.
[Equation 1]
[Si] + [Al] ≥ 2.6
(In Formula 1, [Si] and [Al] represent the content of Si and Al (% by weight), respectively.) The method of claim 1,
Non-oriented electrical steel sheet satisfying the following formula 2.
[Equation 2]
0.8 ≤ [Sr] / ([Si] + [Al]) × 10000 ≤ 8
(In formula 2, [Sr], [Si] and [Al] represent the contents (wt%) of Sr, Si, and Al, respectively.) The method of claim 1,
The non-oriented electrical steel sheet further comprising at least one of Sb: 0.001 to 0.1% by weight and Sn: 0.001 to 0.1% by weight. The method of claim 1,
Non-oriented electrical steel sheet further comprising at least one of Ca: 0.0005 to 0.005% by weight and Mg: 0.0005 to 0.003% by weight. The method of claim 1,
Non-oriented electrical steel sheet having an average grain size of 50 to 200㎛. The method of claim 1,
The non-oriented electrical steel sheet whose ratio (B50L / B50D) of the magnetic flux density (B50L) of a rolling direction to the magnetic flux density (B50D) of a rolling direction and the direction of a 45 degree angle is 1.085 or less. By weight, C: 0.01% or less (excluding 0%), Si: 2.46 to 4.5% by weight, Al: 6% by weight or less (excluding 0%), Mn: 0.03 to 3% by weight, P: 0.01 To 0.08% by weight, S: 0.001 to 0.01% by weight, N: 0.005% by weight or less (excluding 0%), and Sr: 0.0001 to 0.005% by weight, and the balance includes Fe and unavoidable impurities. Manufacturing a slab satisfying 1;
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
Method for producing a non-oriented electrical steel sheet comprising the final annealing the cold rolled sheet.
[Equation 1]
[Si] + [Al] ≥ 2.6
(In Formula 1, [Si] and [Al] represent the content of Si and Al (% by weight), respectively.) The method of claim 7, wherein
After manufacturing the hot rolled sheet, the method of manufacturing a non-oriented electrical steel sheet further comprising the step of annealing the hot rolled sheet. The method of claim 7, wherein
The method of manufacturing a cold rolled sheet may include one step of cold rolling or two or more cold rolling with intermediate annealing.