Title of invention: non-oriented electrical steel sheet Technical field [0001] The present invention relates to non-oriented electrical steel sheets. This application has priority based on Japanese Patent Application No. 2019-206709 filed in Japan on November 15, 2019, and Japanese Patent Application No. 2019-20683 filed in Japan on November 15, 2019. Insist and use its contents here. Background technology [0002] Non-oriented electrical steel sheets are used, for example, for iron cores of motors, and for grain-oriented electrical steel sheets, averages in all directions parallel to the plate surface (hereinafter, "overall circumference average within the plate surface (omnidirectional average)). ”), Which requires excellent magnetic properties, such as low iron loss and high magnetic flux density. Although various techniques have been proposed so far, it is difficult to obtain sufficient magnetic characteristics in all directions in the plate surface. For example, even if sufficient magnetic characteristics can be obtained in a specific direction within the plate surface, sufficient magnetic characteristics may not be obtained in other directions. [0003] For example, Patent Document 3 discloses a technique for developing {100} crystal grains by utilizing phase transformation for the purpose of improving magnetic properties. However, in this method, it is necessary to increase the plate thickness after hot rolling to about 4 mm as in the example of Patent Document 3. This thickness makes it difficult to wind the hot-rolled steel sheet after hot-rolling, and there is a problem that winding in the pickling process and line operation become difficult. Prior art literature Patent documents [0004] Patent Document 1: Japanese Patent No. 4029430 Patent Document 2: Japanese Patent No. 6319465 Patent Document 3: JP-A-2017-193731 Outline of the invention Problems to be solved by the invention [0005] In view of the above-mentioned problems, an object of the present invention is to provide a non-oriented electrical steel sheet capable of obtaining excellent magnetic characteristics with an all-around average (omnidirectional average). Means to solve problems [0006] (1) The non-oriented electrical steel sheet according to one aspect of the present invention is By mass% C: 0.010% or less, Si: 1.50% to 4.00%, Sol. Al: 0.0001% to 1.0%, S: 0.010% or less, N: 0.010% or less, One or more selected from the group consisting of Mn, Ni, Co, Pt, Pb, Cu, Au: 2.50% to 5.00% in total, Sn: 0.000% to 0.400%, Sb: 0.000% to 0.400%, P: 0.000% to 0.400%, and One or more selected from the group consisting of Mg, Ca, Sr, Ba, Ce, La, Nd, Pr, Zn, Cd: A total of 0.0000% to 0.0100% is contained. Mn content (mass%) is [Mn], Ni content (mass%) is [Ni], Co content (mass%) is [Co], Pt content (mass%) is [Pt], Pb content The amount (mass%) is [Pb], the Cu content (mass%) is [Cu], the Au content (mass%) is [Au], the Si content (mass%) is [Si], sol. The Al content (% by mass) was changed to [sol. When [Al] is set, the following equation (1) is satisfied, and The balance has a chemical composition consisting of Fe and impurities, It has a metal structure with a recrystallization rate of 1% to 99% and a plate thickness of 0.50 mm or less. When the magnetic flux density B50 is measured after annealing at 800 ° C. for 2 hours, the magnetic flux density B50 in the 45 ° direction with respect to the rolling direction is 1.75 T or more. ([Mn] + [Ni] + [Co] + [Pt] + [Pb] + [Cu] + [Au])-([Si] + [sol.Al])> 0% ... (1) [0007] (2) In the non-oriented electrical steel sheet described in (1) above, After ablation at 800 ° C. for 2 hours, the value of the magnetic flux density B50 in the rolling direction is B50L, the value of the magnetic flux density B50 in the direction tilted 45 ° from the rolling direction is B50D1, and the value of the magnetic flux density B50 in the direction tilted 90 ° from the rolling direction. When the value of is B50C and the value of the magnetic flux density B50 in the direction inclined by 135 ° from the rolling direction is B50D2, the following equation (2) may be satisfied. (B50D1 + B50D2) / 2> (B50L + B50C) / 2 ... (2) (3) In the non-oriented electrical steel sheet described in (2) above, The following equation (3) may be satisfied. (B50D1 + B50D2) / 2> 1.1 x (B50L + B50C) / 2 ... (3) (4) In the non-oriented electrical steel sheet according to any one of (1) to (3) above, By mass% Sn: 0.020% to 0.400%, Sb: 0.020% to 0.400%, and P: 0.020% to 0.400% It may contain one or more species selected from the group consisting of. (5) In the non-oriented electrical steel sheet according to any one of (1) to (4) above, One or more selected from the group consisting of Mg, Ca, Sr, Ba, Ce, La, Nd, Pr, Zn, Cd in% by mass: Containing 0.0005% to 0.0100% in total. May be good. (6) In the non-oriented electrical steel sheet according to any one of (1) to (5) above, In the metal structure, the recrystallization rate may be 50% to 99%. (7) In the non-oriented electrical steel sheet according to any one of (1) to (6) above, In the metal structure, the recrystallization rate may be 80% to 99%. Effect of the invention [0008] According to the present invention, it is possible to provide a non-oriented electrical steel sheet capable of obtaining excellent magnetic characteristics with an all-around average (omnidirectional average). Embodiment for carrying out the invention [0009] The present inventors have conducted diligent studies to solve the above problems. As a result, it became clear that it is important to make the chemical composition, thickness and recrystallization rate appropriate. The production of such a non-directional electromagnetic steel plate is premised on the chemical composition of the α-γ transformation system, the crystal structure is refined by the transformation from austenite to ferrite during hot rolling, and cold rolling is performed under a predetermined pressure. It is important to make it easier to develop {100} crystal grains, which are normally difficult to develop, by controlling the temperature of intermediate annealing within a predetermined range to generate overhang recrystallization (hereinafter referred to as bulging). It also became clear that there was. [0010] The present inventors came up with the present invention as a result of further diligent studies based on such findings. [0011] Hereinafter, embodiments of the present invention will be described in detail. In the present specification, the numerical range represented by using "-" means a range including the numerical values ​​before and after "-" as the lower limit value and the upper limit value. Further, it is obvious that each element of the following embodiment can be combined with each other. [0012] First, the chemical composition of the non-oriented electrical steel sheet according to the embodiment of the present invention and the steel material used in the manufacturing method thereof will be described. In the following description, "%", which is a unit of the content of each element contained in non-oriented electrical steel sheets or steel materials, means "mass%" unless otherwise specified. Further, the chemical composition of the non-oriented electrical steel sheet shows the content when the base material excluding the film or the like is 100%. [0013] The non-oriented electrical steel sheet and steel material according to the present embodiment have a chemical composition capable of causing a ferrite-austenite transformation (hereinafter, α-γ transformation), and have a C: 0.010% or less and Si: 1.50% or more. 4.00%, sol. Al: 0.0001% to 1.0%, S: 0.010% or less, N: 0.010% or less, Mn, Ni, Co, Pt, Pb, Cu, Au One selected from the group Multiple types: 2.50% to 5.00% in total, Sn: 0.000% to 0.400%, Sb: 0.000% to 0.400%, P: 0.000% to 0.400% , And one or more selected from the group consisting of Mg, Ca, Sr, Ba, Ce, La, Nd, Pr, Zn, and Cd: a total of 0.0000% to 0.0100%, and the balance. Has a chemical composition consisting of Fe and impurities. [0014] The non-oriented electrical steel sheets and steel materials according to this embodiment are further described in Mn, Ni, Co, Pt, Pb, Cu, Au, Si and sol. The Al content satisfies a predetermined condition described later. Examples of impurities include those contained in raw materials such as ore and scrap, and those contained in the manufacturing process. [0015] (C: 0.010% or less) C increases iron loss and causes magnetic aging. Therefore, the lower the C content, the better. Such a phenomenon is remarkable when the C content exceeds 0.010%. Therefore, the C content is set to 0.010% or less. The reduction of the C content also contributes to the uniform improvement of the magnetic properties in all directions in the plate surface. Although the lower limit of the C content is not particularly limited, it is preferably 0.0005% or more in consideration of the cost of decarburization treatment at the time of refining. [0016] (Si: 1.50% to 4.00%) Si increases the electrical resistance, reduces the eddy current loss, reduces the iron loss, increases the yield ratio, and improves the punching workability to the iron core. If the Si content is less than 1.50%, these effects cannot be sufficiently obtained. Therefore, the Si content is 1.50% or more. On the other hand, if the Si content exceeds 4.00%, the magnetic flux density decreases, the punching workability decreases due to an excessive increase in hardness, and cold rolling becomes difficult. Therefore, the Si content is set to 4.00% or less. [0017] (Sol.Al: 0.0001% to 1.0%) Sol. Al increases electrical resistance, reduces eddy current loss, and reduces iron loss. sol. Al also contributes to the improvement of the relative magnitude of the magnetic flux density B50 with respect to the saturation magnetic flux density. sol. If the Al content is less than 0.0001%, these effects cannot be sufficiently obtained. Al also has a desulfurization promoting effect in steelmaking. Therefore, sol. The Al content is 0.0001% or more. On the other hand, sol. When the Al content exceeds 1.0%, the magnetic flux density is lowered, the yield ratio is lowered, and the punching workability is lowered. Therefore, sol. The Al content is 1.0% or less. [0018] Here, the magnetic flux density B50 is the magnetic flux density in a magnetic field of 5000 A / m. [0019] (S: 0.010% or less) S is not an essential element and is contained as an impurity in steel, for example. S inhibits recrystallization and grain growth during annealing due to the precipitation of fine MnS. Therefore, the lower the S content, the better. The increase in iron loss and the decrease in magnetic flux density due to the inhibition of recrystallization and grain growth are remarkable when the S content exceeds 0.010%. Therefore, the S content is set to 0.010% or less. Although the lower limit of the S content is not particularly limited, it is preferably 0.0003% or more in consideration of the cost of desulfurization treatment at the time of refining. [0020] (N: 0.010% or less) Similar to C, N deteriorates the magnetic characteristics, so the lower the N content, the better. Therefore, the N content is 0.010% or less. Although the lower limit of the N content is not particularly limited, it is preferably 0.0010% or more in consideration of the cost of denitrification treatment at the time of refining. [0021] (One or more selected from the group consisting of Mn, Ni, Co, Pt, Pb, Cu, Au: 2.50% to 5.00% in total) Since Mn, Ni, Co, Pt, Pb, Cu, and Au are elements necessary for causing α-γ transformation, at least one or more of these elements are contained in a total of 2.50% or more. Need to be included. Further, the content of these elements is more preferably more than 2.50% in total for at least one or a plurality of these elements from the viewpoint of increasing the electric resistance and reducing the iron loss. On the other hand, if the total content of these elements exceeds 5.00%, the cost becomes high and the magnetic flux density may decrease. Therefore, at least one of these elements should be 5.00% or less in total. [0022] Further, the non-oriented electrical steel sheet and the steel material according to the present embodiment further satisfy the following conditions as conditions under which α-γ transformation can occur. That is, the Mn content (mass%) is [Mn], the Ni content (mass%) is [Ni], the Co content (mass%) is [Co], and the Pt content (mass%) is [Pt]. Pb content (mass%) is [Pb], Cu content (mass%) is [Cu], Au content (mass%) is [Au], Si content (mass) %) Is [Si], sol. The Al content (% by mass) was changed to [sol. Al], it is assumed that the following equation (1) is satisfied in terms of mass%. [0023] ([Mn] + [Ni] + [Co] + [Pt] + [Pb] + [Cu] + [Au])-([Si] + [sol.Al])> 0% ... (1) [0024] If the above equation (1) is not satisfied, the α-γ transformation does not occur, so the magnetic flux density becomes low. [0025] (Sn: 0.000% to 0.400%, Sb: 0.000% to 0.400%, P: 0.000% to 0.400%) Sn and Sb improve the texture after cold rolling and recrystallization, and improve the magnetic flux density. Therefore, these elements may be contained as needed, but if they are contained in an excessive amount, the steel is embrittled. Therefore, both the Sn content and the Sb content are set to 0.400% or less. Further, P may be contained in order to secure the hardness of the steel sheet after recrystallization, but if it is contained in an excessive amount, it causes embrittlement of the steel. Therefore, the P content is set to 0.400% or less. [0026] When imparting further effects such as magnetic properties, from 0.020% to 0.400% Sn, 0.020% to 0.400% Sb, and 0.020% to 0.400% P. It is preferable to contain one or more kinds selected from the group. [0027] (One or more selected from the group consisting of Mg, Ca, Sr, Ba, Ce, La, Nd, Pr, Zn, and Cd: 0.0000% to 0.0100% in total) Mg, Ca, Sr, Ba, Ce, La, Nd, Pr, Zn and Cd react with S in the molten steel to form sulfides, acid sulfides or both precipitates during casting of the molten steel. Hereinafter, Mg, Ca, Sr, Ba, Ce, La, Nd, Pr, Zn and Cd may be collectively referred to as "coarse precipitate-forming element". The particle size of the precipitate of the coarse precipitate-forming element is about 1 μm to 2 μm, which is much larger than the particle size of fine precipitates such as MnS, TiN, and AlN (about 100 nm). Therefore, these fine precipitates adhere to the precipitates of the coarse precipitate-forming element, and it becomes difficult to inhibit the recrystallization and the growth of crystal grains in annealing such as intermediate annealing. In order to sufficiently obtain these effects, the total amount of coarse precipitate-forming elements is preferably 0.0005% or more. However, if the total amount of these elements exceeds 0.0100%, the total amount of sulfide, acid sulfide, or both of them becomes excessive, and recrystallization and growth of crystal grains in annealing such as intermediate annealing are inhibited. Therefore, the total content of the coarse precipitate-forming element is 0.0100% or less. [0028] Next, the metal structure of the non-oriented electrical steel sheet according to this embodiment will be described. The details of the manufacturing method will be described later, but the non-directional electromagnetic steel sheet according to the present embodiment has a chemical composition in which α-γ transformation can occur, and when hot rolling is completed and then cooled, austenite is changed to ferrite. It transforms and the crystal structure becomes finer. Further, the non-oriented electrical steel sheet of the present embodiment has a metal structure having a recrystallization rate of 1% to 99%. If some unrecrystallized crystals are left in this way, the magnetic flux density B50 is further improved. The reason for such control is to reduce the abundance ratio of recrystallized grains having crystal orientations other than {100} crystal orientation, which should be developed from the viewpoint of magnetic characteristics. [0029] If the recrystallization rate is less than 1% or the recrystallization rate exceeds 99%, the effect of improving the magnetic flux density cannot be obtained. The recrystallization rate is preferably 55% to 95%, and more preferably 80% to 90%. [0030] The recrystallization rate of non-oriented electrical steel sheets can be specified by the following procedure. First, the sample collected from the non-directional electromagnetic steel plate is polished so that the plate thickness is halved, and the polished surface is observed by an electron backscatter diffraction (EBSD) method. Then, the grains satisfying any one of the following conditions (a) and (b) are determined as unrecrystallized portions, and the unrecrystallized ratio = the area of ​​the unrecrystallized portions / the area of ​​the entire observation field of view is calculated. (A) The average particle size of the crystal grains exceeds 300 μm. (B) The aspect ratio of the crystal grains satisfies (length in the rolling direction) / (length in the direction of 90 degrees from the rolling direction)> 2. The observation field of view is 8 mm 2 or more. [0031] Next, the thickness of the non-oriented electrical steel sheet according to this embodiment will be described. The thickness of the non-oriented electrical steel sheet according to this embodiment is 0.50 mm or less. If the thickness is more than 0.50 mm, excellent high frequency iron loss cannot be obtained. Therefore, the thickness is set to 0.50 mm or less. Further, from the viewpoint of facilitating production, the thickness of the non-oriented electrical steel sheet according to the present embodiment is more preferably 0.10 mm or more. [0032] Further, the non-oriented electrical steel sheet according to the present embodiment may have a strain distribution so that a high magnetic flux density can be obtained in all directions as a whole. For example, when observing an arbitrary cross section, the area ratio of the {100} azimuth grain is Sac, the area ratio of the {110} azimuth grain is Sag, and { When the area ratio of 100} oriented grains is Sbc and the area ratio of {110} oriented grains in the same region is Sbg, it is more preferable that Sac> Sbc> Sag> Sbg. The {100} crystal grain (or {110} crystal grain) is a crystal grain defined within 10 ° of tolerance from the target crystal orientation. The {100} crystal grain (or {110} crystal grain, etc.) and the {100} directional grain (or {110} directional grain, etc.) have the same meaning. [0033] Here, in order to obtain the above relationship, the area ratio of crystal grains on the polished surface of the material polished so that the plate thickness of the steel plate is halved can be obtained, for example, by the EBSD method. Further, the KAM value can be obtained by calculating IPF (Inverse Pole Figure) from the observation field of view of EBSD. [0034] The KAM value indicates the directional difference between a certain measurement point and an adjacent measurement point within the same grain. The KAM value becomes high in places where there is a lot of distortion. By extracting the region up to 20% from the side where KAM is high, only the high strain region can be extracted. The measurement point is an area composed of arbitrary pixels. The region from the high KAM side to 20% means the region occupying the frequency from the high KAM side to 20% in the graph obtained by converting the frequency diagram of the KAM value into the cumulative frequency diagram. [0035] The above inequality Sac> Sag relationship indicates that the proportion of {100} directional grains is larger than that of {110} directional grains. Annealing after the skin pass facilitates the growth of both {100} oriented grains and {110} oriented grains. Here, since the {100} azimuth grain is superior to the {110} azimuth grain in the magnetic characteristics of the whole circumference average, it is more preferable to increase the number of the {100} azimuth grain. The same applies to the relationship of Sbc> Sbg in the high strain region. [0036] Next, the relationship of Sac> Sbc means that there are relatively few regions with a lot of distortion in the {100} azimuth grain. It is known that in the annealing after the skin pass, the grains with less distortion eat the grains with more distortion. Therefore, this inequality means that {100} oriented grains are likely to grow. Further, the KAM value is a value measured by the EBSD method, and the KAM value at a portion having a lot of distortion is higher than that around the portion. The same applies to the relationship of Sag> Sbg. [0037] Next, the magnetic characteristics of the non-oriented electrical steel sheet according to this embodiment will be described. When investigating the magnetic characteristics, the magnetic flux density is measured after the non-oriented electrical steel sheet according to the present embodiment is further annealed at 800 ° C. for 2 hours. The non-oriented electrical steel sheet according to the present embodiment has the best magnetic characteristics in two directions in which the smaller angle of the rolling direction is 45 °. On the other hand, the magnetic characteristics are the worst in the two directions where the angles formed with the rolling direction are 0 ° and 90 °. Here, the "45 °" is a theoretical value, and it may not be easy to match it with 45 ° in actual manufacturing. Therefore, theoretically, if the directions in which the magnetic characteristics are the best are the two directions in which the smaller angle of the rolling direction is 45 °, the actual non-oriented electrical steel sheet has the 45 °. ° shall include those that do not (exactly) match 45 °. This also applies to the "0 °" and "90 °". [0038] Theoretically, the magnetic characteristics in the two directions having the best magnetic characteristics are the same, but in actual manufacturing, it may not be easy to make the magnetic characteristics in the two directions the same. Therefore, theoretically, if the magnetic properties in the two directions having the best magnetic properties are the same, the "same" includes those that are not (exactly) the same. This is the same in the two directions with the worst magnetic properties. It should be noted that the above angles are expressed assuming that the angles in both the clockwise and counterclockwise directions have positive values. When the clockwise direction is a negative direction and the counterclockwise direction is a positive direction, the two directions in which the smaller angle of the above-mentioned rolling directions is 45 ° are the above-mentioned rolling directions. Of the angles to be formed, the angle with the smaller absolute value is 45 ° and −45 ° in two directions. Further, the two directions in which the smaller angle of the angles formed with the rolling direction is 45 ° can be described as the two directions in which the angles formed with the rolling direction are 45 ° and 135 °. [0039] When the magnetic flux density of the non-directional electromagnetic steel plate according to the present embodiment is measured, the magnetic flux density B50 (corresponding to B50D1 and B50D2) in the 45 ° direction with respect to the rolling direction is 1.75T or more. In the non-directional electromagnetic steel plate according to the present embodiment, the magnetic flux density in the 45 ° direction with respect to the rolling direction is high, but a high magnetic flux density can be obtained even in the all-around average (omnidirectional average). [0040] In the non-directional electromagnetic steel plate according to the present embodiment, the value of the magnetic flux density B50 in the rolling direction after being annealed at 800 ° C. for 2 hours is B50L, and the value of the magnetic flux density B50 in the direction inclined by 45 ° from the rolling direction is B50D1. Assuming that the value of the magnetic flux density B50 in the direction inclined by 90 ° from the rolling direction is B50C and the value of the magnetic flux density B50 in the direction inclined by 135 ° from the rolling direction is B50D2, B50D1 and B50D2 are the highest, and B50L and B50C are the lowest. Anisotropy of magnetic flux density can be seen. [0041] Here, for example, when considering the omnidirectional (0 ° to 360 °) distribution of the magnetic flux density with the clockwise (or counterclockwise) direction as the positive direction, the rolling directions are 0 ° (one direction) and 180. When ° (other direction), B50D1 is the value of the magnetic flux densities B50 of 45 ° and 225 °, and B50D2 is the value of the magnetic flux densities B50 of 135 ° and 315 °. Similarly, B50L has a magnetic flux density B50 value of 0 ° and 180 °, and B50C has a magnetic flux density B50 value of 90 ° and 270 °. The value of the magnetic flux density B50 at 45 ° and the value of the magnetic flux density B50 at 225 ° exactly match, and the value of the magnetic flux density B50 at 135 ° and the value of the magnetic flux density B50 at 315 ° exactly match. However, B50D1 and B50D2 may not exactly match because it may not be easy to make the magnetic characteristics the same in actual manufacturing. Similarly, the value of the magnetic flux density B50 at 0 ° and the value of the magnetic flux density B50 at 180 ° exactly match, and the value of the magnetic flux density B50 at 90 ° and the value of the magnetic flux density B50 at 270 ° exactly match. On the other hand, B50L and B50C may not exactly match. In the manufactured non-oriented electrical steel sheet, one of the rolling directions and the other (the direction opposite to the rolling direction) cannot be distinguished. Therefore, in the present embodiment, the rolling direction means both one and the other. [0042] In the non-oriented electrical steel sheet according to the present embodiment, it is more preferable to satisfy the following equation (2) by using the average value of B50D1 and B50D2 and the average value of B50L and B50C. [0043] (B50D1 + B50D2) / 2> (B50L + B50C) / 2 ... (2) [0044] Having such anisotropy with high magnetic flux density has the advantage of being suitable for split iron core type motor materials. [0045] Further, the non-oriented electrical steel sheet according to the present embodiment can be more preferably used as a split iron core type motor material by satisfying the following equation (3). [0046] (B50D1 + B50D2) / 2> 1.1 x (B50L + B50C) / 2 ... (3) [0047] The magnetic flux density can be measured by cutting out a 55 mm square sample from the 45 °, 0 ° direction, etc. with respect to the rolling direction and using a single plate magnetic measuring device. [0048] Next, an example of the method for manufacturing the non-oriented electrical steel sheet according to the present embodiment will be described. In this embodiment, hot rolling, cold rolling, intermediate annealing, skin pass rolling and the like will be described. [0049] First, the above-mentioned steel material is heated and hot-rolled. The steel material is, for example, a slab manufactured by ordinary continuous casting. Rough rolling and finish rolling of hot rolling are performed at a temperature in the γ region (Ar1 temperature or higher). That is, it is preferable to perform hot rolling so that the temperature (finishing temperature) when passing through the final pass of finish rolling is Ar1 temperature or higher. As a result, the crystal structure is refined by transforming austenite to ferrite by subsequent cooling. If cold rolling is subsequently performed in a state where the crystal structure is refined, bulging is likely to occur, and {100} crystal grains that are normally difficult to grow can be easily grown. In this embodiment, the Ar1 temperature is obtained from the change in thermal expansion of the steel material (steel plate) being cooled at an average cooling rate of 1 ° C./sec. Further, in the present embodiment, the Ac1 temperature is obtained from the change in thermal expansion of the steel material (steel plate) being heated at an average heating rate of 1 ° C./sec. [0050] After that, the hot-rolled plate is wound without annealing. The temperature at the time of winding is preferably more than 250 ° C and 600 ° C or less. By winding the hot-rolled steel sheet after hot-rolling at a temperature of more than 250 ° C and 600 ° C or less, the crystal structure before cold rolling can be made finer, and the {100} orientation with excellent magnetic properties can be obtained during bulging. The effect of being able to enrich is obtained. The temperature at the time of winding is more preferably 400 ° C. to 500 ° C., further preferably 400 ° C. to 480 ° C. [0051] After that, after pickling, the hot-rolled steel sheet is cold-rolled. In cold rolling, the rolling reduction is preferably 80% to 92%. The higher the rolling reduction ratio, the easier it is for {100} crystal grains to grow due to subsequent bulging, but it becomes more difficult to wind the hot-rolled steel sheet and the operation becomes more difficult. [0052] When cold rolling is completed, intermediate annealing is subsequently performed. In the present embodiment, the recrystallization rate is set to 1% to 99% by controlling the intermediate annealing temperature to be lower than the Ac1 temperature. If the intermediate annealing temperature is too low, recrystallization may not occur and bulging may not occur. Therefore, {100} crystal grains may not grow sufficiently and the magnetic flux density may not increase. Therefore, the temperature of intermediate annealing is preferably 600 ° C. or higher. Further, when the intermediate annealing temperature is Ac1 temperature or higher, the recrystallization rate of ferrite is close to 100%, but the presence of recrystallized grains having a crystal orientation other than the {100} crystal orientation that should be developed from the viewpoint of magnetic characteristics. Since the ratio is high, the magnetic flux density is not high. Balging occurs by performing intermediate annealing, and {100} crystal grains are likely to grow. However, in the present embodiment, {100} crystal grains are further grown by further mixing unrecrystallized and recrystallized. Can be done. The intermediate annealing time is preferably 5 to 60 seconds. [0053] The recrystallization rate is preferably 50% or more at the time after intermediate annealing from the viewpoint that {100} oriented grains are more likely to grow after finish annealing or strain relief annealing. [0054] After the intermediate annealing is completed, skin pass rolling is performed next. When rolling is performed in a state where bulging has occurred as described above, {100} crystal grains are further grown starting from the portion where bulging has occurred. The rolling reduction of skin pass rolling is preferably 5% to 25%, and from the viewpoint of obtaining anisotropy with high magnetic flux density, the rolling reduction of skin pass rolling is more preferably 5% to 15%. [0055] When the non-oriented electrical steel sheet has the above-mentioned strain distribution, the rolling reduction rate (%) for cold rolling is Rm, and the rolling reduction rate (%) for skin pass rolling is Rs. , 86 0% ... (1) [Claim 2] After being annealed at 800 ° C. for 2 hours, the value of the magnetic flux density B50 in the rolling direction is B50L, the value of the magnetic flux density B50 in the direction inclined by 45 ° from the rolling direction is B50D1, and the value of the magnetic flux density B50 in the direction inclined by 90 ° from the rolling direction is B50. When the value of is B50C and the value of the magnetic flux density B50 in the direction inclined by 135 ° from the rolling direction is B50D2, the following equation (2) is satisfied. The non-oriented electrical steel sheet according to claim 1. (B50D1 + B50D2) / 2> (B50L + B50C) / 2 ... (2) [Claim 3] Satisfy the following formula (3) The non-oriented electrical steel sheet according to claim 2. (B50D1 + B50D2) / 2> 1.1 x (B50L + B50C) / 2 ... (3) [Claim 4] By mass% Sn: 0.020% to 0.400%, Sb: 0.020% to 0.400%, and P: 0.020% to 0.400% Contains one or more species selected from the group consisting of The non-oriented electrical steel sheet according to any one of claims 1 to 3, wherein the non-oriented electrical steel sheet is characterized by the above. [Claim 5] One or more selected from the group consisting of Mg, Ca, Sr, Ba, Ce, La, Nd, Pr, Zn, Cd in% by mass: contains 0.0005% to 0.0100% in total. The non-oriented electrical steel sheet according to any one of claims 1 to 4, characterized in that. [Claim 6] In the metal structure, the recrystallization rate is 50% to 99%. The non-oriented electrical steel sheet according to any one of claims 1 to 5, characterized in that. [Claim 7] In the metal structure, the recrystallization rate is 80% to 99%. The non-oriented electrical steel sheet according to any one of claims 1 to 6, characterized in that.