Title of invention: grain-oriented electrical steel sheet Technical field [0001] The present invention relates to grain-oriented electrical steel sheets. Background technology [0002] Since grain-oriented electrical steel sheets are mainly used as iron cores of transformers, it is desired that their magnetization characteristics, especially iron loss, are low. For that purpose, it is important to highly align the crystal grains accumulated in the {110} <001> direction, to contain Si to increase the intrinsic resistance, and to reduce impurities. [0003] However, there is a limit to the control of crystal orientation and the reduction of iron loss due to the steel sheet components, and a technique for subdividing the width of the magnetic domain to reduce the iron loss (hereinafter, also referred to as "magnetic domain control technique") has been developed. There is. Magnetic domain control technology can be broadly divided into non-heat resistant type and heat resistant type technology. [0004] As a non-heat resistant magnetic domain control technique, for example, as disclosed in Patent Documents 1 and 2, a method of forming a linear thermal strain region on the surface layer of a steel sheet by irradiating the steel sheet with a laser beam is known. ing. In this method, the magnetic domain width is narrowed by the thermal strain region, so that iron loss is reduced. However, since the strain is released in the heat strain region by heat treatment, the grain-oriented electrical steel sheet to which the non-heat-resistant magnetic domain control technique is applied cannot be used for a transformer that requires strain removal and annealing after processing such as a wound steel core. Therefore, there is a problem that the usage of the grain-oriented electrical steel sheet is limited. [0005] On the other hand, grain-oriented electrical steel sheets with heat-resistant magnetic domain control technology have the advantage of not being restricted in their use. As such a heat-resistant magnetic domain control technique, for example, a method of forming a groove by electrolytic etching as disclosed in Patent Document 3 is known. In this method, for example, a glass film is first formed on the surface of the steel sheet after secondary recrystallization. Then, the glass film on the surface of the steel sheet is linearly removed by a laser or a mechanical method, and a groove is formed in the portion where the base metal is exposed by etching. Therefore, this method complicates the process and increases the manufacturing cost. Furthermore, there is a limit to the processing speed. [0006] Besides, as disclosed in Patent Document 4, a method of forming a groove on the surface of a steel sheet by a mechanical tooth mold press is known. However, Si is often added to the electromagnetic steel sheet in an amount of about 3% by mass for the purpose of increasing the electric resistance. Since such an electromagnetic steel sheet is very hard, the method disclosed in Patent Document 4 may cause wear and damage of the tooth profile. Further, the groove depth may vary, and the iron loss improving effect may also vary. [0007] Further, the heat-resistant magnetic domain control technique described above has a sufficient iron loss reduction effect as compared with the non-heat-resistant magnetic domain control technique in which a thermal strain region is introduced into the surface layer of the steel sheet by irradiating the steel sheet with a laser beam. There is also the problem of not being able to do it. Patent Documents 5 and 6 disclose, as a heat-resistant magnetic domain control technique, a technique for devising the shape of the steel plate surface and the groove shape, but the fundamental solution to each of the above problems possessed by the heat-resistant magnetic domain control technique. Has not been reached. [0008] By the way, in order to sufficiently obtain the effect of reducing iron loss by subdividing the magnetic domain as described above, the tension exerted on the steel sheet by the insulating film or the glass film (hereinafter, also referred to as “film tension”) is extremely important. Will be done. As the insulating film, for example, one formed by applying an aqueous coating solution containing a phosphate and colloidal silica to a steel sheet is known. As the glass film, which will be described in detail later, for example, a glass film containing an oxide containing forsterite as a main component is known. [0009] Patent Documents 7 and 8 disclose techniques for increasing the tension of the glass film. Specifically, Patent Document 7 discloses an electromagnetic steel sheet in which spinel (for example, MgAl 2O 4) in forsterite (that is, in a glass film) is 5% or more. Further, Patent Document 8 discloses an electromagnetic steel sheet in which the emission intensities of Al and Fe obtained by glow discharge emission analysis satisfy a predetermined condition. Further, Patent Document 9 discloses a technique for improving the adhesion of the glass film (preventing peeling during bending during transformer production). Specifically, Patent Document 9 discloses an electromagnetic steel sheet in which the emission intensity of B obtained by glow discharge emission analysis satisfies a predetermined condition. However, although the techniques disclosed in Patent Documents 7 to 9 can be expected to improve the tension or adhesion of the glass film, these techniques alone cannot obtain the magnetic domain subdivision effect. That is, the techniques disclosed in Patent Documents 7 to 9 are premised on the heat-resistant magnetic domain control technique described above. Therefore, even with these techniques, the problem that the iron loss reduction effect cannot be sufficiently obtained cannot be sufficiently solved. Prior art literature Patent documents [0010] Patent Document 1: Japanese Patent Application Laid-Open No. 6-57335 Patent Document 2: Japanese Unexamined Patent Publication No. 2003-129135 Patent Document 3: Japanese Patent Application Laid-Open No. 61-117284 Patent Document 4: Japanese Patent Application Laid-Open No. 61-117218 Patent Document 5: International Publication No. 2010/14709 Patent Document 6: Japanese Patent Application Laid-Open No. 2013-510239 Patent Document 7: Japanese Unexamined Patent Publication No. 8-134660 Patent Document 8: Japanese Unexamined Patent Publication No. 2000-204450 Patent Document 9: International Publication No. 2019/146697 Outline of the invention Problems to be solved by the invention [0011] As described above, the heat-resistant magnetic domain control technology has a problem that the iron loss reduction effect cannot be sufficiently obtained. On the other hand, although the non-heat-resistant magnetic domain control technique can enhance the iron loss reduction effect as compared with the heat-resistant magnetic domain control technique, further improvement of the iron loss reduction effect has been required. [0012] The present invention has been developed in view of the above circumstances, and even in heat-resistant magnetic domain control in which the iron loss before magnetic domain control is further improved and the iron loss improving effect cannot be sufficiently obtained, the iron loss is sufficiently improved. It is an object of the present invention to provide a grain-oriented electrical steel sheet that can obtain an effect. Means to solve problems [0013] The present inventor has made extensive studies to solve the above problems. Specifically, the present inventor repeated an experiment in which heat-resistant magnetic domain control was performed on a grain-oriented electrical steel sheet having the same magnetic flux density and various iron loss characteristics before the magnetic domain control. As a result, the present inventor has found that the better the iron loss in the state before the magnetic domain control, the better the iron loss after the magnetic domain control. Then, as a result of investigating the characteristics of the steel sheet having good iron loss before the magnetic domain control, the present inventor has a structure in which the glass film is fitted into the surface layer portion of the base steel sheet (hereinafter, "fitting of the glass film") in any of the steel sheets. It was clarified that the structure (also called "structure") is developing. The present inventor came up with the present invention based on such findings. The gist of the present invention is as follows. [0014] According to a certain viewpoint of the present invention, it is a directional electromagnetic steel sheet containing a base steel sheet and a glass film formed on the surface of the base steel sheet, and the base steel sheet is a chemical component in% by mass. C: 0.010% or less, Si: 2.00 to 4.00%, Mn: 0.05 to 1.00%, Al: 0.010 to 0.065% or less, N: 0.004% or less, S: Contains 0.010% or less, the balance is Fe and impurities, the oxygen concentration in the glass film and the base steel sheet is 2500 ppm or less, and the directional electromagnetic steel sheet is analyzed by glow discharge emission from the surface of the glass film. The concentration profile of Al obtained by (GDS) has at least two peaks, and each Al peak is set as the first peak and the second peak in order from the side closest to the surface of the glass film, and the first peak of Al is set. Provided is a directional electromagnetic steel sheet characterized by satisfying the relationship of the equation (1), where I Al_1 and the second peak intensity of Al are I Al_1. I Al_1 A preferred embodiment of the present invention will be described in detail with reference to the accompanying drawings below. First, the outline of the present invention will be described. The present inventor has diligently studied a technique for promoting magnetic domain subdivision in order to further reduce iron loss. When the magnetic domain is subdivided, the width of the magnetic domain becomes narrow. When the magnetic domain width is narrowed, the moving distance of the domain wall when the steel sheet is magnetized is shortened, so that the energy loss when the domain wall is moved is reduced. That is, iron loss is reduced. [0019] Here, the magnetic domain subdivision can be realized by generating a new magnetic pole in the surface layer portion of the base steel sheet. More specifically, such magnetic poles increase the static energy of the surface layer of the base steel sheet. Then, in the surface layer portion of the base steel sheet, a new 180 ° domain wall is generated in order to reduce the static magnetic energy. As a result, the magnetic domain is subdivided. In other words, the magnetic domain width becomes narrower. [0020] As mentioned above, it is necessary to generate new magnetic poles for magnetic domain subdivision. Specifically, it is necessary to build an interface made of a substance having a magnetic permeability different from that of the base steel sheet in the surface layer portion of the base steel sheet. [0021] Therefore, the present inventor considered fitting the glass film into the surface layer portion of the base steel sheet. This is because the fitting structure of the glass film constitutes the magnetic poles at the surface layer portion of the base steel sheet, so that the magnetic domain can be subdivided. Although the details will be described later, the inset structure of the glass film contains Al precipitates, which form the magnetic poles. [0022] The present inventor has repeatedly studied for maximizing the effect of subdividing the magnetic domain by the fitting structure of the glass film, and found that the fitting structure is formed by forming a glass film satisfying a predetermined condition on the surface of the base steel sheet. It was found that it can be controlled and the magnetic domain subdivision effect can be enjoyed to the maximum. [0023] Specifically, the oxygen concentration contained in the glass film and the base steel sheet shall be 2500 ppm or less. Further, in the concentration profile of Al obtained by performing glow discharge emission analysis (GDS) on the directional electromagnetic steel plate, as shown in FIG. 1, the intensity of the first peak 1 of Al (first peak intensity) is set to I Al_1. When the intensity of the second peak 2 of Al (second peak intensity) is I Al_1, the structure of the glass film is controlled so that the relationship of I Al_1 (2-1. Overall configuration) The grain-oriented electrical steel sheet according to the present embodiment includes a base steel sheet and a glass film formed on the surface of the base steel sheet. An insulating film may be further formed on the surface of the glass film. The glass film has an inset structure that fits into the base steel sheet, and the inset structure is very well developed. That is, the inset structure has a complicated three-dimensional network structure. Therefore, the glass film is classified into a covering portion that covers most of the surface layer of the base steel sheet and an fitting structure that is fitted into the inside of the surface layer portion of the base steel sheet from the covering portion. Furthermore, the inset structure contains a large amount of Al-containing precipitates. [0025] 2 and 3 show an example of a vertical cross section parallel to the rolling direction of the grain-oriented electrical steel sheet according to the present embodiment. FIG. 2 is a schematic view, and FIG. 3 is a photomicrograph of a cross section. ND indicates the plate thickness direction (normal direction of the steel plate surface), and RD indicates the rolling direction. [0026] In these examples, the grain-oriented electrical steel sheet includes the base steel sheet c and the glass film a formed on the surface of the base steel sheet c. The glass film a has an fitting structure that fits into the base steel plate c, and the fitting structure is very developed. The inset structure contains Al precipitate b. Although Al precipitates appear to be scattered in FIGS. 2 and 3, the Al precipitates are found on the plane of the paper surface (that is, in the rolling direction of the steel sheet) as shown in FIGS. 2 and 3. Not only exists only on a parallel cross section), but actually extends in a direction intersecting the paper surface of FIGS. 2 and 3 (for example, perpendicular to the paper surface) (that is, in the plate width direction of the steel plate), and extends to the covering portion. It has a connected three-dimensional network structure. Further, in FIGS. 2 and 3, the fitting structure generally appears to be fitted from the covering portion toward the surface layer portion of the base steel plate (that is, extends in the plate thickness direction), but the fitting structure extends in the rolling direction and the plate width direction. In some cases. When observing the vertical cross section of this portion, a long fitting structure is observed to the left and right (in the rolling direction and the plate width direction). Details of the inset structure and Al precipitate will be described later. The covered portion of the glass coating is a portion that covers most of the surface layer of the base steel sheet, and is a portion that is connected to the fitting structure that is fitted inside the surface layer portion of the base steel plate. The covering portion and the inset structure can be classified by the Al concentration profile as described later. [0027] (2-2. Component composition of base steel sheet) As a chemical component, the base steel sheet has C: 0.010% or less, Si: 2.00 to 4.00%, Mn: 0.05 to 1.00%, Al: 0.010 to 0 in mass%. .065% or less, N: 0.004% or less, S: 0.010% or less, and the balance consists of Fe and impurities. Hereinafter,% related to the component composition shall mean mass% with respect to the total mass of the base steel sheet. [0028] (C: 0.010% or less) C is an element that is effective in controlling the primary recrystallization structure, but it adversely affects the magnetic properties, so it is an element that is removed by decarburization annealing before finish annealing. If the C concentration exceeds 0.010% in the final product, C will age-precipitate and the hysteresis loss will deteriorate. Therefore, the C concentration should be 0.010% or less. The C concentration is preferably 0.007% or less, more preferably 0.005% or less. The lower limit of the C concentration includes 0%, but if the C concentration is reduced to less than 0.0001%, the manufacturing cost will increase significantly, so 0.0001% is a practical lower limit on the practical steel sheet. In grain-oriented electrical steel sheets, the C concentration is usually reduced to about 0.001% or less by decarburization annealing. [0029] (Si: 2.00-4.00%) Si is an element that increases the electrical resistance of steel sheets and improves iron loss characteristics. If the Si concentration is less than 2.00%, γ transformation of the iron structure occurs during finish baking and the crystal orientation of the steel sheet is impaired. Therefore, the Si concentration is set to 2.00% or more. The Si concentration is preferably 2.50% or more, more preferably 3.00% or more. On the other hand, if the Si concentration exceeds 4.00%, the workability of the grain-oriented electrical steel sheet deteriorates and cracks occur during rolling, so the Si concentration is set to 4.00% or less. The Si concentration is preferably 3.50% or less. [0030] (Mn: 0.05 to 1.00%) Mn is an element that prevents cracking during hot rolling and combines with S to produce MnS that functions as an inhibitor. If the Mn concentration is less than 0.05%, the effect of adding Mn is not sufficiently exhibited, so the Mn concentration is set to 0.05% or more. The Mn concentration is preferably 0.07% or more, more preferably 0.09% or more. On the other hand, when the Mn concentration exceeds 1.00%, the precipitation and dispersion of MnS become non-uniform, the required secondary recrystallization structure cannot be obtained, and the magnetic flux density decreases, so that the Mn concentration is 1.00% or less. And. The Mn concentration is preferably 0.80% or less, more preferably 0.60% or less. [0031] (Al: 0.010-0.065%) Al is an element that binds to N to form (Al, Si) N or AlN that functions as an inhibitor. If the Al concentration is less than 0.010%, the effect of adding Al is not sufficiently exhibited and secondary recrystallization does not proceed sufficiently, so the Al concentration is set to 0.010% or more. The Al concentration is preferably 0.015% or more, more preferably 0.020% or more. On the other hand, when the Al concentration exceeds 0.065%, the precipitation and dispersion of the inhibitor become non-uniform, the required secondary recrystallization structure cannot be obtained, and the magnetic flux density decreases, so that the Al concentration is 0.065% or less. And. The Al concentration is preferably 0.050% or less, more preferably 0.040% or less. Although the details will be described later, Al in the base steel sheet also has a function of reacting with a glass film having a developed inset structure to form an Al precipitate. [0032] (N: 0.004% or less) N is an element that binds to Al to form AlN that functions as an inhibitor. However, if the N concentration in the final product exceeds 0.004%, N in the steel sheet precipitates as AlN, which deteriorates the hysteresis loss. Therefore, the N concentration is set to 0.004% or less. The lower limit of the N concentration includes 0%, but if the N concentration is to be reduced to less than 0.0001%, the manufacturing cost will increase significantly, so 0.001% is a practical lower limit on the practical steel sheet. In grain-oriented electrical steel sheets, the N concentration is usually reduced to about 0.001% or less by finish annealing. [0033] (S: 0.010% or less) S is an element that binds to Mn to produce MnS that functions as an inhibitor. However, if the S concentration exceeds 0.010% in the final product, S in the steel sheet precipitates as MnS, which deteriorates the hysteresis loss. Therefore, the S concentration is set to 0.010% or less. The lower limit of the S concentration includes 0%, but if the S concentration is reduced to less than 0.0001%, the manufacturing cost will increase significantly, so 0.0001% is a practical lower limit on the practical steel sheet. In grain-oriented electrical steel sheets, the S concentration is usually reduced to about 0.005% or less by finish annealing. [0034] In the components of the base steel sheet, the balance excluding the above elements is Fe and impurities. Impurities are basically unavoidable impurities, but when the base steel sheet contains optional additive elements described later, the impurities are composed of these optional additive elements in addition to the unavoidable impurities. The unavoidable impurities are elements that are inevitably mixed from the steel raw material and / or in the steelmaking process, and are permissible elements as long as they do not impair the characteristics of the grain-oriented electrical steel sheet according to the present embodiment. [0035] Further, in the base steel plate, Cr: 0.30% or less, Cu: 0.40% or less, P: 0.50% for the purpose of not impairing the magnetic characteristics and enhancing other characteristics. Below, Ni: 1.00% or less, Sn: 0.30% or less, Sb: 0.30% or less, B: 0.0100% or less, Mo: 0.1% or less, and Bi: 0.01% or less. One or more of the above may be added as an optional additive element. Since these elements are optional additives, the lower limit of the concentration may be 0%. [0036] (Cr: 0.30% or less) Cr is an element that improves the oxide layer of decarburization annealing and is effective for forming a glass film. Therefore, Cr may be added to the base steel sheet in the range of 0.30% or less. If the Cr concentration exceeds 0.30%, the decarburization property is significantly inhibited. Therefore, the upper limit of the Cr concentration is preferably 0.30%. [0037] (Cu: 0.40% or less) Cu is an element effective in increasing the specific resistance of the base steel sheet and reducing iron loss. If the C concentration exceeds 0.40%, the iron loss reducing effect is saturated and it causes a surface defect called "copper hegging" during hot rolling. Therefore, the upper limit of the C concentration is preferably 0.40%. [0038] (P: 0.50% or less) P is an element effective in increasing the specific resistance of the base steel sheet and reducing iron loss. If the P concentration exceeds 0.50%, a problem may occur in rollability. Therefore, the upper limit of the P concentration is preferably 0.50%. [0039] (Ni: 1.00% or less) Ni is an element effective in increasing the specific resistance of the base steel sheet and reducing iron loss. Ni is also an effective element for controlling the iron structure of the hot-rolled sheet and improving the magnetic properties. However, if the Ni concentration exceeds 1.00%, secondary recrystallization becomes unstable, so the upper limit of the Ni concentration is preferably 1.00%. [0040] (Sn: 0.30% or less, Sb: 0.30% or less) Sn and Sb are well-known grain boundary segregation elements. Since the base steel sheet according to the present embodiment contains Al, Al may be oxidized by the moisture released from the annealing separator depending on the conditions of finish annealing, and the inhibitor strength may fluctuate at the coil position. As a result, the magnetic characteristics may fluctuate depending on the coil position. As one of the countermeasures, there is a method of preventing the oxidation of Al by adding these grain boundary segregating elements, and for that purpose, Sn and Sb may be added to the base steel sheet at a concentration of 0.30% or less, respectively. .. On the other hand, when the concentration of these elements exceeds 0.30%, Si is less likely to be oxidized during decarburization annealing, the formation of a glass film becomes insufficient, and the decarburization annealing is significantly impaired. Therefore, the upper limit of the concentration of these elements is preferably 0.30%. [0041] (B: 0.0100% or less) B is an element that binds to N in the base steel sheet and complex-precipitates with MnS to form BN that functions as an inhibitor. The lower limit of the B concentration is not particularly limited, and may be 0% as described above. However, in order to fully exert the effect of adding B, the lower limit of the B concentration is preferably 0.0005%. The B concentration is preferably 0.001% or more, more preferably 0.0015% or more. On the other hand, when the B concentration exceeds 0.0100%, the precipitation and dispersion of BN become non-uniform, the required secondary recrystallization structure cannot be obtained, and the magnetic flux density decreases. Therefore, the B concentration is preferably 0.0100% or less. The B concentration is preferably 0.0080% or less, more preferably 0.0060% or less, and more preferably 0.0040% or less. [0042] (Mo: 0.1% or less) Mo is an element effective for improving the surface texture during hot spreading. However, if the Mo concentration exceeds 0.1%, the Mo addition effect is saturated, so the upper limit of the Mo concentration is preferably 0.1%. [0043] (Bi: 0.01% or less) Bi has the effect of stabilizing precipitates such as sulfides and strengthening the function as an inhibitor. However, if the Bi concentration exceeds 0.01%, Bi adversely affects the formation of the glass film, so the upper limit of the Bi concentration is preferably 0.01%. [0044] (2-3. Oxygen concentration in glass film and base steel sheet) The total oxygen concentration in the glass film and the base steel sheet is 2500 ppm or less. Most of the oxygen is contained in the glass film, and the oxygen contained in the steel sheet is about 10 to 100 ppm. When the grain-oriented electrical steel sheet contains an insulating film described later, the oxygen concentration is measured after the insulating film is removed from the grain-oriented electrical steel sheet. That is, the insulating film is not included in the measurement target of oxygen concentration. The insulating film is, for example, sodium hydroxide.It is removed using an aqueous solution or the like. [0045] The oxygen analysis method uses a gas analysis method in which a sample is placed in a graphite crucible, the sample is melted and heated, and CO and CO 2 are measured by the infrared absorption method. [0046] When the oxygen concentration exceeds 2500 ppm, the magnetic flux density of the base steel sheet decreases (more specifically, the amount of magnetite decreases), and the iron loss deteriorates. Therefore, the upper limit of the oxygen concentration is 2500 ppm. The lower limit of the oxygen concentration is not particularly limited, but when the oxygen concentration is extremely low as 500 ppm or less, the glass film is not actually formed on the surface of the base steel sheet, and the inset structure of the glass film does not develop. Therefore, the iron loss is inferior. Furthermore, the adhesion of the insulating film may decrease. Therefore, the oxygen concentration is preferably more than 500 ppm, more preferably 1000 ppm or more. The oxygen concentration is measured using a gas analyzer using the principle of the inert gas melting method. In the examples described later, it is a value measured by this method. Examples of the method for setting the oxygen concentration to 2500 ppm or less include decarburization annealing conditions, particularly a method for adjusting the dew point. For example, the oxygen concentration can be 2500 ppm or less by adjusting the dew point while considering the annealing time and annealing temperature. [0047] (2-4. Al concentration profile by GDS) When the grain-oriented electrical steel sheet according to this embodiment is subjected to glow discharge emission analysis (GDS), the emission intensity distribution of Al (Al concentration profile) is observed in the plate thickness direction. When the grain-oriented electrical steel sheet contains an insulating film described later, the Al concentration profile is measured after the insulating film is removed from the grain-oriented electrical steel sheet. That is, the insulating film is not included in the measurement target of the Al concentration profile. The measurement by GDS is performed from the surface of the glass film. [0048] GDS analysis requires appropriate adjustment of conditions according to the sample, and the adjustment is within the range of normal practice for those skilled in the art. Therefore, the measurement conditions of GDS are not limited, but for example, the output is 35 W, and the data is taken in at intervals of 0.01 to 0.10 seconds. [0049] The Al concentration profile has at least two peaks. The peaks of each Al are designated as the first peak, the second peak, and so on in order from the side closest to the surface of the glass film. FIG. 1 shows an example of the Al concentration profile. The Al concentration profile shown in FIG. 1 has two peaks, that is, a first peak 1 and a second peak 2. The number of peaks is preferably two. The peaks may partially overlap or may be separated from each other. [0050] The first peak is derived from the Al precipitate in the coated portion of the glass film, and the second peak is derived from the Al precipitate in the inlaid structure of the glass film. The Al precipitate from which each peak is derived is, for example, Mg 2Al 2O 4 in which Si of forsterite (Mg 2SiO 4) constituting the glass film is replaced with Al. MgAl 2O 4 has a similar composition of constituent elements to forsterite (Mg 2SiO 4), has a polymorphic relationship, and is easily produced. However, the Al precipitate is not necessarily limited to Mg 2Al 2O 4, and is not particularly limited as long as it constitutes a magnetic pole in the surface layer portion of the base steel sheet. Examples of other Al precipitates assumed in the present embodiment include precipitates in which other elements are substituted and solid-solved in MgAl 2O 4, Al 2O 3 and the like. [0051] Further, when the first peak intensity of Al is I Al_1 and the second peak intensity of Al is I Al_1, the relationship of the formula (1) is satisfied. I Al_1 P1> P2. The details will be described later, but by gradually lowering the nitrogen partial pressure in this way, the inset structure of the glass film can be greatly developed. When T4 is set to a temperature lower than 1200 ° C., the nitrogen partial pressure P2 at T4 to 1200 ° C. is 0% (hydrogen partial pressure 100%). [0090] (3-10. Purification annealing process) In the purification annealing step following the finish annealing step, the precipitates (AlN, MnS, etc.) used as inhibitors are detoxified by performing purification after the completion of secondary recrystallization. This makes it possible to reduce the hysteresis loss in the final magnetic characteristics. In the purification annealing step, for example, it is preferable to retain the steel sheet at 1200 ° C. for 10 hours or more in a hydrogen atmosphere. [0091] (3-11. Cooling process) After the purification annealing process, cool the steel sheet. Here, it is preferable that the cooling rate (temperature lowering rate) CR in the temperature range (T5) of 1200 to 1000 ° C. is 30 to 100 ° C./h. The cooling rate CR is more preferably 30 to 50 ° C./h. Although the details will be described later, the fitting structure can be further developed by lowering the cooling rate CR. [0092] By the above-mentioned process, the grain-oriented electrical steel sheet according to the present embodiment can be manufactured. The reason why the grain-oriented electrical steel sheet according to the present embodiment can be produced by each of the above-mentioned steps is not clear, but the present inventor generally considers the reason as follows. [0093] First, in the heating process of the decarburization annealing step, by controlling the heating rate HR1 in the temperature range of t0 to t2 to 40 ° C./sec or more, internal oxidation containing a large amount of SiO 2 in the surface layer portion of the steel sheet before finish annealing. Layers can be formed. [0094] Next, in the finish annealing step, forsterite (Mg 2SiO 4) is produced by the solid phase reaction between SiO 2 in the internal oxide layer and MgO in the annealing separator. Then, forsterite accumulates on the surface of the steel sheet to form a glass film. As a result, a glass film is formed on the surface of the steel sheet (base steel sheet). Here, as described above, in the finish annealing step, the nitrogen partial pressure is gradually lowered from a high partial pressure to a low partial pressure at 700 to 1200 ° C. As a result, MgO in the annealing separator reacts stably with SiO 2 existing at a deeper position in the internal oxide layer to generate forsterite. That is, the glass film is fitted into the surface layer portion of the base steel sheet, and the fitting structure is formed. Furthermore, the inset structure develops as the generated forsterite grows in Ostwald. Specifically, the three-dimensional network structure of the fitting structure becomes complicated, and the branches constituting the fitting structure become thicker. [0095] On the other hand, at a temperature of about 1000 ° C. or higher, AlN, which is an inhibitor in the base steel sheet, floats toward the glass film side, and N separates. After that, Al reaching the tip of the inset structure reacts with forsterite in the inset structure to form an Al precipitate (MgAl 2O 4, etc.). This Al precipitate is trapped in the inset structure and stays in place. Further, in the cooling step, by controlling the cooling rate CR in the temperature range (T5) of 1200 to 1000 ° C. in the range of 30 to 100 ° C./h, Ostwald ripening of the Al precipitate constituting the inlaid structure is promoted. The inset structure develops further. Here, the branches of the Al precipitate become complicated and thick. The Al precipitates that are abundantly distributed in this inlaid structure correspond to the second peak of the Al concentration profile. Most of the Al separated from AlN, which is an inhibitor in the base steel sheet, forms an Al precipitate in the inlaid structure, but a part of the separated Al reaches a portion of the glass film that is not an inlaid structure, that is, a coated portion. Al precipitates are formed on the coated portion of the glass film. The Al precipitate present in this glass film corresponds to the first peak of the Al concentration profile. Therefore, the second peak derived from the Al precipitate of the inlaid structure becomes larger than the first peak derived from the Al precipitate of the glass film. That is, the Al precipitate grows in the inset structure and develops in the surface layer portion of the base steel sheet so that the mathematical formula (1) is satisfied. 2 and 3 show an example in which the inset structure is developed (that is, the equation (1) is satisfied), and FIG. 4 shows an example in which the inset structure is not developed (that is, the equation (1) is not satisfied). [0096] Here, the lower the cooling rate CR, the more the fitting structure develops. That is, the lower the cooling rate CR, the higher the precipitation frequency of Al precipitates, and by extension, 50 pieces / mm or more. [0097] After performing each of the above steps, an insulating film coating step and a magnetic domain control step may be further performed. [0098] (3-12. Insulation film coating) Apply an insulating film coating to the surface of the steel sheet after the cooling process and bake it. The type of the insulating film is not particularly limited, and any conventionally known insulating film is suitable for the grain-oriented electrical steel sheet of the present embodiment. Examples of the insulating film include a film formed by applying an aqueous coating solution containing a phosphate and colloidal silica. In this case, examples of the phosphate include phosphates such as Ca, Al, and Sr. Of these, the aluminum phosphate salt is more preferable. Colloidal silica is not particularly limited, and its particle size can be used as appropriate. A particularly preferable particle size (average particle size) is 200 nm or less. Even if the particle size is less than 100 nm, there is no problem in dispersion, but the manufacturing cost becomes high and it may not be realistic. If the particle size exceeds 200 nm, it may settle in the treatment liquid. [0099] It is preferable to apply the insulating film coating liquid to the surface of the steel sheet by a wet coating method such as a roll coater and bake it in an air atmosphere at a temperature of 800 to 900 ° C. for 10 to 60 seconds to form a tension insulating film. .. [0100] (3-13. Magnetic domain control process) The specific processing method of the magnetic domain control process is not particularly limited, and lower iron loss can be obtained by performing magnetic domain control by, for example, laser irradiation, electron beam, etching, or a groove forming method using gears. As described above, the iron loss is greatly improved in the grain-oriented electrical steel sheet according to the present embodiment even before the magnetic domain control. Therefore, even if the heat-resistant magnetic domain control is performed in which the iron loss improving effect cannot be sufficiently obtained, the iron loss improving effect can be sufficiently obtained. Example [0101] Next, an embodiment of the present invention will be described. The conditions in the examples are one condition example adopted for confirming the feasibility and effect of the present invention, and the present invention is not limited to this one condition example. The present invention can adopt various conditions as long as the gist of the present invention is not deviated and the object of the present invention is achieved. [0102] <1. Example 1>In Example 1, a steel slab having the composition shown in Table 1 was heated to 1150 ° C. and then subjected to hot rolling to obtain a hot-rolled plate having a plate thickness of 2.6 mm. Then, the hot-rolled plate was annealed by setting the temperature of the first stage to 1100 ° C. and the temperature of the second stage to 900 ° C. Then, the hot-rolled plate was subjected to one cold-rolling or a plurality of cold-rolling with intermediate annealing sandwiched between them to prepare a cold-rolled plate having a final plate thickness of 0.23 mm. [0103] [table 1] [0104] Then, the cold-rolled sheet having a final thickness of 0.23 mm was subjected to decarburization annealing and nitriding treatment (annealing to increase the nitrogen content of the steel sheet). The heating rate HR1 in decarburization annealing was set to 100 ° C./s. The heating method was a radiant tube method. Here, t0 is 550 ° C and t2 is 840 ° C. In the tropics, the temperature t2 was maintained for 100 seconds. The nitrogen concentration is 200 to 25. The range was set to 0 ppm, and analysis was performed by the method described in JIS G1228. [0105] After that, an annealing separator containing magnesia (MgO) as a main component was applied to the surface of the steel sheet, and finish annealing was performed. In the finish annealing step, the steel sheet was heated to 1200 ° C. Here, the heating temperature in the temperature range of 1000 to 1100 ° C. was set to 10 ° C./h. Further, regarding the annealing atmosphere, the nitrogen partial pressure P0 up to 800 ° C. (up to T2) is 80%, the nitrogen partial pressure P1 up to 1000 ° C. (up to T3) is 50%, and the nitrogen partial pressure up to 1200 ° C. (up to T4). P2 was set to 20%. However, the annealing atmosphere of Comparative Examples b10 and b11 was the atmosphere described later. Purification was at 1200 ° C. for 10 hours. [0106] In the subsequent cooling step, the steel sheet was cooled at a cooling rate CR of 60 ° C./h in the temperature range (T5) from 1200 ° C. to 1000 ° C. However, the cooling rate CR of Comparative Examples b12 and b13 was set to a value described later. A grain-oriented electrical steel sheet was produced by the above steps. [0107] Then, the oxygen concentration of the grain-oriented electrical steel sheet was measured, and the Al concentration profile was further measured by GDS. Here, the oxygen concentration was analyzed by the method described in JIS G 1239. The GDS had an output of 35 W, and data was acquired at 0.01 second intervals. The results are shown in Table 2. [0108] After that, a water-based coating liquid consisting of phosphate and colloidal silica was applied to the steel sheet, and the steel sheet was baked in air at 800 ° C. for 60 seconds. As a result, a tension insulating film was formed on the surface of the steel sheet (more specifically, the surface of the glass film). Then, the iron loss W 17/50 (energy loss measured under the excitation conditions of 1.7 T and 50 Hz) of the grain-oriented electrical steel sheet to which the tension insulating film was applied was measured. The measurement was carried out based on JIS C 2550. The results are shown in Table 2. [0109] [Table 2] [0110] In Invention Examples B1 to B17 that satisfy all the requirements (formula (1) regarding component composition, oxygen concentration, and Al concentration profile) of the grain-oriented electrical steel sheet according to the present embodiment, the iron loss is 0.85 W / kg or less, which is good magnetism. The characteristics have been obtained. [0111] On the other hand, in Comparative Examples b1, b2, b4, and b5, since a steel slab whose mass% by mass of some of the component compositions was out of the range of this embodiment was used, secondary recrystallization did not occur and the iron loss was 1.0 W / W /. It exceeded kg and was significantly inferior. In Comparative Examples b3 and b9, since steel slabs having a mass% of a part of the component composition lower than the range of the present embodiment were used, the intrinsic resistance was small and the iron loss was 0.9 W / kg or more, which was inferior. In Comparative Examples b6 and b7, since steel slabs having a mass% of a part of the component composition exceeding the range of the present embodiment were used, impurities remained and the iron loss was inferior to 0.9 W / kg or more. In Comparative Example b8, since a steel slab having a mass% of a part of the component composition outside the range of the present embodiment was used, the steel sheet after reheating became brittle and had to be stopped rolling. In Comparative Examples b10 and b11, the nitrogen partial pressure P0 up to 800 ° C. (up to T2) is 50%, the nitrogen partial pressure P1 up to 1000 ° C. (up to T3) is 50%, and up to 1200 ° C. (up to T4) with respect to the atmosphere of finish annealing. ), The nitrogen partial pressure P2 was set to 50%. That is, the partial pressure of nitrogen was kept constant. Therefore, the fitting structure of the glass film did not develop, and the iron loss was inferior to more than 0.85 W / kg. In Comparative Examples b12 and b13, the cooling rate CR in the temperature range (T5) from 1200 ° C. to 1000 ° C. was set to 150 ° C./h in the cooling step after finish annealing. Therefore, the inlaid structure of the glass film, particularly Al precipitates, did not develop, and the iron loss was inferior to more than 0.85 W / kg. [0112] <2. Example 2> In Example 2, the steel slab having the composition shown in Table 1 was heated to 1150 ° C. and then subjected to hot rolling to obtain a hot-rolled steel sheet having a plate thickness of 2.6 mm. Then, the hot-rolled plate was annealed by setting the temperature of the first stage to 1100 ° C. and the temperature of the second stage to 900 ° C. Then, the hot-rolled plate was subjected to one cold-rolling or a plurality of cold-rolling with intermediate annealing sandwiched between them to prepare a cold-rolled plate having a final plate thickness of 0.23 mm. [0113] Then, the cold-rolled steel sheet having a final thickness of 0.23 mm was subjected to decarburization annealing and nitriding treatment (annealing to increase the nitrogen content of the steel sheet). The heating rate HR in decarburization annealing was 100 ° C./s. The heating method was a radiant tube method. Here, t0 is 580 ° C. and t2 is 860 ° C. In the tropics, the temperature t2 was maintained for 120 seconds. The nitrogen concentration is 220-26. The range was set to 0 ppm, and analysis was performed by the method described in JIS G1228. [0114] After that, an annealing separator containing magnesia (MgO) as a main component was applied to the surface of the steel sheet, and finish annealing was performed. In the finish annealing step, the steel sheet was heated to 1200 ° C. Here, the heating temperature in the temperature range of 1000 to 1100 ° C. was set to 10 ° C./h. Here, the annealing atmosphere and the cooling rate CR in the subsequent cooling step were changed for each invention example. Specifically, regarding the incineration atmosphere of Invention Examples C1 to C3 (see Table 3), the nitrogen partial pressure P0 up to 800 ° C. (up to T2) is 90%, and the nitrogen partial pressure P1 up to 1000 ° C. (up to T3) is set. The nitrogen partial pressure P2 up to 60% and 1200 ° C. (up to T4) was set to 30%. In the subsequent cooling step, the cooling rate CR in the temperature range (T5) from 1200 ° C. to 1000 ° C. was set to 100 ° C./h. [0115] On the other hand, regarding the annealing atmosphere of Invention Examples C4 to C17 (see Table 3), the nitrogen partial pressure P0 up to 800 ° C. (up to T2) was 75%, and the nitrogen partial pressure P1 up to 1000 ° C. (up to T3) was 50%. The nitrogen partial pressure P2 up to 1200 ° C. (up to T4) was set to 30%. Further, the cooling rate CR in the temperature range (T5) from 1200 ° C. to 1000 ° C. was set to 40 ° C./h. [0116] After that, the oxygen concentration of the grain-oriented electrical steel sheet was measured in the same manner as in Example 1, and the Al concentration profile was further measured by GDS. Here, the oxygen concentration was analyzed by the method described in JIS G 1239. Further, in Example 2, the cross-sectional observation of the grain-oriented electrical steel sheet was also performed. Specifically, in the vertical cross section of the surface layer portion of the base steel sheet parallel to the rolling direction, a region from the surface of the glass film to a depth of 10 μm, that is, an observation region was photographed with an optical microscope. The magnification at the time of shooting was 400 times, and 10 images were taken for each sample. Then, the composition of the observation region in each image was analyzed by SEM-EDS to identify the composition in the observation region. By measuring the precipitation frequency (precipitation frequency in the rolling direction) of Al precipitates having a circle equivalent diameter of 1 μm or more from each of the 10 images and arithmetically averaging these, the precipitation frequency (number frequency) of Al precipitates in each sample ) Was calculated. The results are shown in Table 3. [0117] Then, a water-based coating liquid composed of phosphate and colloidal silica was applied to the steel sheet, and the steel sheet was baked in air at 800 ° C. for 60 seconds. As a result, a tension insulating film was formed on the surface of the steel sheet (more specifically, the surface of the glass film). Then, the iron loss W 17/50 (energy loss measured under the excitation conditions of 1.7 T and 50 Hz) of the grain-oriented electrical steel sheet to which the tension insulating film was applied was measured. The measurement was carried out based on JIS C 2550. The results are shown in Table 3. [0118] [Table 3] [0119] The iron loss of Invention Examples C4 to C17 satisfying the precipitation frequency of Al precipitates of 50 pieces / mm or more is higher than that of Invention Examples C1 to C3 in which the precipitation frequency of Al precipitates is less than 50 pieces / mm. It was even better at 0.80 W / kg or less. Since the cooling rates in Invention Examples C4 to C17 are lower than the cooling rates in Invention Examples C1 to C3, it is presumed that such a result was obtained. [0120] Although the preferred embodiments of the present invention have been described in detail with reference to the accompanying drawings, the present invention is not limited to these examples. It is clear that any person having ordinary knowledge in the field of the art to which the present invention belongs can come up with various modifications or modifications within the scope of the technical ideas described in the claims. , These are also naturally understood to belong to the technical scope of the present invention. Code description [0121] 1: First peak of Al 2: Second peak of Al a: Glass film (Mg 2SiO 4) b: Al precipitate c: Base steel plate The scope of the claims [Claim 1] Base steel plate and A grain-oriented electrical steel sheet containing a glass film formed on the surface of the base steel sheet. The base steel sheet has C: 0.010% or less, Si: 2.00 to 4.00%, Mn: 0.05 to 1.00%, Al: 0.010 to% in mass% as a chemical component. It contains 0.065% or less, N: 0.004% or less, S: 0.010% or less, and the balance consists of Fe and impurities. The oxygen concentration contained in the glass film and the base steel sheet is 2500 ppm or less, The concentration profile of Al obtained by glow discharge emission spectrometry (GDS) of the grain-oriented electrical steel sheet from the surface of the glass film has at least two peaks. When the peaks of each Al are the first peak and the second peak in order from the side closer to the surface of the glass film, the intensity of the first peak of Al is I Al_1, and the intensity of the second peak of Al is I Al_2. A directional electromagnetic steel plate characterized by satisfying the relationship (1). I Al_1