The present invention relates to a grain-oriented electrical steel sheet and a method for manufacturing a grain-oriented electrical steel sheet. Background technology [0002] The grain-oriented electrical steel sheet is a steel sheet containing Si in an amount of about 2% by mass to 5% by mass, and the orientation of the crystal grains of the steel sheet is highly integrated in the {110} <001> orientation called the Goss orientation. The grain-oriented electrical steel sheet has excellent magnetic characteristics and is used, for example, as an iron core material for a static induction device such as a transformer. [0003] Various developments have been made for such grain-oriented electrical steel sheets in order to improve their magnetic properties. In particular, with the recent demand for energy saving, further reduction of iron loss is required for grain-oriented electrical steel sheets. In order to reduce the iron loss of the grain-oriented electrical steel sheet, it is effective to increase the degree of integration in the Goss direction with respect to the orientation of the crystal grains of the steel sheet to improve the magnetic flux density and reduce the hysteresis loss. [0004] Here, in the production of grain-oriented electrical steel sheets, the crystal orientation is controlled by utilizing a catastrophic grain growth phenomenon called secondary recrystallization. However, in order to appropriately control the crystal orientation in secondary recrystallization, it is important to improve the heat resistance of fine precipitates in steel called inhibitors. [0005] For example, there is a method in which the inhibitor is completely solid-solved when the steel piece is heated before hot rolling, and then finely precipitated in the hot rolling and the subsequent annealing step. Specifically, a method of rolling with a rolling reduction of more than 80% in the final cold rolling step using MnS and AlN as exemplified in Patent Document 1 below, or exemplified in Patent Document 2 below. Examples thereof include a method of performing two cold rolling steps using MnS and MnSe as inhibitors. [0006] As a technique for further improving the magnetic flux density, for example, Patent Document 3 below discloses a technique for adding 100 to 5000 g / T Bi to molten steel. A technique for improving the magnetic flux density in a final product plate by adding Bi to molten steel is disclosed. However, there is a problem that the adhesion between the primary coating film containing Mg 2SiO 4 (forsterite) as a main component and the steel sheet deteriorates, and the coating film peels off when the product plate is bent. The following Patent Documents 4 to 6 disclose a technique for improving the adhesion between the primary coating and the steel sheet by compound-adding a compound of a rare earth metal and a compound of an alkaline earth metal to an annealing separator. [0007] Further, Patent Document 7 below discloses a technique for manufacturing a grain-oriented electrical steel sheet having low iron loss over the entire length of the coil by controlling the heat pattern in the heating process of primary recrystallization annealing. There is. Further, Patent Document 8 below describes a technique for reducing the iron loss value of grain-oriented electrical steel sheets by strictly controlling the average grain size of crystal grains after secondary recrystallization and the deviation angle from the ideal orientation. Is disclosed. Prior art literature Patent documents [0008] Patent Document 1: Japanese Patent Publication No. 40-15644 Patent Document 2: Japanese Patent Publication No. 51-13469 Patent Document 3: Japanese Patent Application Laid-Open No. 6-88171 Patent Document 4: Japanese Patent No. 5419459 Patent Document 5: Japanese Patent No. 5230194 Patent Document 6: Japanese Patent Application Laid-Open No. 2012-214902 Patent Document 7: International Publication No. 2014/0497770 Pamphlet Patent Document 8: Japanese Unexamined Patent Publication No. 7-268567 Outline of the invention Problems to be solved by the invention [0009] In recent years, with the progress of global transformer efficiency regulations, the demand for reducing iron loss of grain-oriented electrical steel sheets has become even greater. As the amount of Bi added to the molten steel is increased, the magnetic flux density is improved and low iron loss can be expected, but there is a problem that the adhesion between the primary coating and the steel sheet is deteriorated. In addition, due to the need to save space in substation equipment, the miniaturization of transformer iron cores is progressing, so the degree of bending of product plates is increasing, and it is necessary to improve the adhesion between the primary coating and the steel plate. There is. [0010] However, with only the techniques disclosed in Patent Documents 4 to 6 above, there is a problem that the primary coating is peeled off from the steel sheet when the amount of Bi added is increased or the degree of bending of the product plate is increased. rice field. There was a need for technology to improve the adhesion between the primary coating and the steel sheet. [0011] Further, as disclosed in Patent Document 7, in the process of raising the temperature of primary recrystallization annealing, the temperature is rapidly raised at 100 ° C./s or higher between 500 ° C. and 600 ° C. to obtain a grain-oriented electrical steel sheet. It has been confirmed that the magnetic properties are greatly affected. Patent Document 8 discloses that the temperature rise to 850 ° C. is set to 300 ° C./s in the temperature rise process of primary recrystallization annealing. [0012] However, in Patent Documents 7 and 8 described above, it is described in detail how the magnetic properties of the grain-oriented electrical steel sheet are affected when the rate of rapid temperature rise in the primary recrystallization annealing is further increased. Was not considered. [0013] Further, the rapid temperature rise in the primary recrystallization annealing increases the variation in the magnetic flux density B8 value of the grain-oriented electrical steel sheet for each coil. Therefore, even when the temperature is rapidly raised, it may not be possible to obtain grain-oriented electrical steel sheets with low iron loss depending on the conditions of the content of the annealing separator. [0014] Therefore, the present invention has been made in view of the above problems and the like, and an object of the present invention is to add Bi to molten steel to enhance the heat resistance of the inhibitor, and at the same time, to rapidly perform primary recrystallization annealing. A new and improved method for manufacturing a directional electromagnetic steel sheet, which can manufacture a directional electric steel sheet having a higher magnetic flux density and excellent adhesion between the primary coating and the steel sheet when the temperature is raised, and the method thereof. It is an object of the present invention to provide a directional electromagnetic steel sheet manufactured by a manufacturing method. Means to solve problems [0015] In order to solve the above problems, according to a certain viewpoint of the present invention, in terms of mass%, C: 0.02% or more and 0.10% or less, Si: 2.5% or more and 4.5% or less, Mn: 0. 0.01% or more and 0.15% or less, total of 1 or 2 of S and Se: 0.001% or more and 0.050% or less, acid-soluble Al: 0.01% or more and 0.05% or less, N A slab containing 0.002% or more and 0.015% or less, Bi: 0.0005% or more and 0.05% or less, and the balance of Fe and impurities is heated to 1280 ° C. or higher for hot rolling. By applying, the process of making a hot-rolled steel plate, and after hot-rolling the hot-rolled steel plate, one cold rolling or two or more cold rollings sandwiching intermediate annealing are performed to cool the hot-rolled steel plate. A step of forming a rolled steel sheet, a step of subjecting the cold-rolled steel sheet to primary recrystallization annealing, and a step of applying a shrinking separator containing MgO to the surface of the cold-rolled steel sheet after the primary recrystallization annealing, and then performing finish annealing. Including a step of applying an insulating film to a steel plate after finish rolling and then flattening and rolling. In the heating process of the primary recrystallization annealing, the average temperature rise rate Va1 (° C./s) between the start of temperature rise and 550 ° C., and the average temperature rise rate Va2 (° C./s) between 550 ° C. and 700 ° C. The average temperature rise rate Va3 (° C / s) between 700 ° C and the end of temperature rise Va1 ≤ Va2, 400 ≤ Va2, Va3 ≤ Va2 The filling, In the quenching separator, when the MgO content in the annealing separator is 100% by mass%, TiO 2 is 0.5% or more and 10% or less, oxides of rare earth metals, sulfides, sulfates, and the like. One or more of silicates, phosphates, hydroxides, carbonates, boronides, chlorides, and fluorides are 0.1% or more and 10% or less in terms of rare earth metals, Ca, Sr, and Ba. One or more of sulfates, carbonates, hydroxides, chlorides and oxides of alkaline earth metals selected from the group consisting of 0.1% or more and 10% or less in terms of alkaline earth metals. , Sulfate or sulfide is contained in A% in terms of sulfur element, and the A is the following formula. (0.00025 x Va2) ≤ A ≤ 1.5 And meet In the process of raising the temperature of the finish annealing, the moisture release rate from the annealing separator between room temperature and 700 ° C. is 0.5% or more and 6.0% or less, and the average temperature rise between 900 ° C. and 1100 ° C. The formula whose velocity Vf (° C./h) is as follows 5 ≦ Vf ≦ (21-4 × A) A method for manufacturing a grain-oriented electrical steel sheet, which is characterized by satisfying the above conditions, is provided. [0016] Further, in order to solve the above problems, according to another viewpoint of the present invention, in terms of mass%, C: 0.005% or less, Si: 2.5 to 4.5%, Mn: 0.01 to 0. A directional electromagnetic steel sheet containing .15% and having a base steel sheet having a balance of Fe and impurities and a primary coating formed on the surface of the base steel sheet and containing Mg 2SiO 4 as a main component. There, The peak position D Al of Al emission intensity obtained when elemental analysis by glow discharge emission spectrometry is performed from the surface of the primary coating in the plate thickness direction of the directional electromagnetic steel plate is the thickness of the primary coating from the surface of the primary coating. It exists in the range of 2.0 to 12.0 μm in the direction, The number density ND of Al oxide is 0.02 to 0.20 / μm 2 and The peak position DS of the S emission intensity obtained when elemental analysis by the glow discharge emission spectrometry method is performed from the surface of the primary coating in the plate thickness direction of the grain-oriented electrical steel sheet is the thickness from the surface of the primary coating. It exists in the range of 1.0 to 10.0 μm in the direction, and DS Va2, the temperature of the steel sheet becomes non-uniform before the rapid temperature rise between 550 ° C and 700 ° C, the rapid heating effect varies, and the magnetic characteristics of the finally obtained grain-oriented electrical steel sheet are improved. It is not preferable because it may not be possible. [0050] The average temperature rise rate Va3 (° C./s) between 700 ° C. and the end of temperature rise is Va3 ≦ Va2. When Va3> Va2, the oxide film after decarburization annealing changes, and the effect of sulfur infiltration from the annealing separator in the expected finish annealing temperature rise process cannot be obtained, and the final grain-oriented electrical steel sheet is obtained. It is not preferable because the magnetic characteristics of the above may not be improved. This mechanism is not always clear, but when Va3> Va2, the oxide film after decarburization annealing becomes too thick, the amount of sulfur infiltrated from the annealing separator in the process of raising the temperature of finish annealing decreases, and primary recrystallization occurs. It is presumed that the effect of increasing the Goss azimuth grain due to the rapid temperature rise in the temperature rise process cannot be fully utilized. [0051] Here, the temperature raising process may be carried out by a plurality of devices. For example, recovery of the steel sheet, that is, holding or slowly cooling at a temperature lower than 550 ° C., which causes a decrease in the dislocation density in the steel, can also improve the temperature soaking property of the steel sheet before the temperature rise. It doesn't matter. Further, a heating process including a temperature increase from 550 ° C to 700 ° C may also be performed by one or more devices. [0052] The point at which the temperature rise is started is the transition from the state where the temperature of the steel sheet is lowered to the state where the temperature of the steel sheet is raised on the low temperature side of 550 ° C. or lower (that is, the point where the temperature change takes a minimum value). Is. Further, the point where the temperature rise is completed is the point where the temperature of the steel sheet changes from the state where the temperature of the steel sheet rises to the state where the temperature of the steel sheet decreases on the high temperature side of 700 ° C. or higher (that is, the point where the temperature change reaches a maximum value). ). [0053] Here, the method for discriminating the temperature rise start point and the rapid temperature rise end point is not particularly limited, but it can be discriminated by measuring the steel plate temperature using, for example, a radiation thermometer or the like. The method for measuring the temperature of the steel sheet is not particularly limited. Further, even if the temperature rise end temperature of the primary recrystallization becomes lower or higher than the subsequent decarburization annealing temperature, the effect of the present invention is not impaired. If the temperature rise end temperature of the primary recrystallization is lower than the decarburization annealing temperature, heating may be performed in the decarburization annealing step. When the temperature rise end temperature of the primary recrystallization is higher than the decarburization annealing temperature, the steel sheet temperature may be cooled by performing heat treatment or gas cooling treatment. Further, after cooling to a temperature lower than the decarburization annealing temperature, reheating may be performed in the decarburization annealing step. [0054] However, if it is difficult to measure the temperature of the steel sheet and it is difficult to estimate the exact location of the temperature rise start point and rapid temperature rise end point, it is possible to infer the heat patterns of the temperature rise process and the cooling process. , These locations may be estimated. Further, the temperature on the entrance side and the temperature on the exit side of the steel sheet to the temperature riser in the temperature rise process may be set as the temperature rise start point and the rapid temperature rise end point. [0055] Here, the atmosphere of the temperature rise process of the primary recrystallization annealing is the oxygen partial pressure ratio, that is, the water vapor partial pressure PH2O and the hydrogen partial pressure PH2 in the atmosphere so as not to inhibit the decarburization property in the subsequent decarburization annealing. The ratio PH2O / PH2 of may be, for example, 0.1 or less. [0056] Next, the cold-rolled steel sheet is decarburized and annealed. Decarburization annealing is performed at a temperature of 900 ° C. or lower in a moist atmosphere containing hydrogen and nitrogen. In the step of primary recrystallization annealing, the cold-rolled steel sheet may be subjected to reduction annealing following decarburization annealing for the purpose of improving magnetic properties and coating properties. [0057] [Process of finishing annealing] After that, finish annealing is applied to the cold-rolled steel sheet after primary recrystallization annealing. At that time, an annealing separator containing MgO as a main component is applied before finish annealing for the purpose of preventing seizure between steel sheets, forming a primary film, and controlling secondary recrystallization behavior. The annealing separator is generally applied and dried on the surface of a steel sheet in the state of a water slurry, but an electrostatic coating method or the like may be used. Here, the additive of the annealing separator has a great influence on the adhesion between the primary coating and the steel sheet and the secondary recrystallization behavior. The additive content and effect of the annealing separator are described below. Here, the content is the content (mass%) of the additive when the content of MgO, which is the main component of the annealing separator, is 100% by mass. The "main component" means a component contained in a substance in an amount of 50% by mass or more, preferably 70% by mass or more, and more preferably 90% by mass or more. [0058] The amount of the annealing separator adhered to the steel sheet is preferably 2 g / m 2 or more and 10 g / m 2 or less per one side, for example. When the amount of the annealing separator adhered to the steel sheet is less than 2 g / m 2, it is not preferable because the steel sheets are seized with each other in the finish annealing. If the amount of the annealing separator adhered to the steel sheet exceeds 10 g / m 2, the manufacturing cost increases, which is not preferable. [0059] In the annealing separator, the content of TiO 2 is 0.5% or more and 10% or less. TiO 2 has a great influence on the adhesion between the primary coating and the steel sheet. If it is less than 0.5%, the effect of improving the adhesion is not sufficient, and if it is more than 10%, Ti is solid-solved in the steel sheet in the finish annealing process, and later fine precipitates such as TiC are formed. It is not preferable because it may deteriorate the magnetism (magnetic aging). Therefore, the content of TiO 2 is 0.5% or more and 10% or less, and more preferably 1.0% or more and 8% or less. [0060] The content of the rare earth metal compound in the annealing separator is 0.1% or more and 10% or less in terms of rare earth metal. If it is less than 0.1%, the effect of improving the adhesion is not sufficient, and if it is more than 10%, the manufacturing cost increases, which is not preferable. Therefore, the content of the rare earth metal compound is 0.1% or more and 10% or less in terms of rare earth metal, and more preferably 0.2% or more and 8% or less. The rare earth metal compound is not particularly limited, and is one of oxides, sulfides, sulfates, silices, phosphates, hydroxides, carbonates, borohydrides, chlorides, and fluorides. Two or more kinds may be mixed. As the rare earth metal compound, it is more preferable to use the compound of La, Ce, Y from the viewpoint of availability and cost. That is, in the present invention, the rare earth metal is more preferably selected from the group consisting of La, Ce, and Y. [0061] In the annealing separator, the content of the alkaline earth metal compound is 0.1% or more and 10% or less in terms of alkaline earth metal. If it is less than 0.1%, the effect of improving the adhesion is not sufficient, and if it is more than 10%, the coatability of the annealing separator slurry is deteriorated, which is not preferable. Therefore, the content of the alkaline earth metal compound is 0.1% or more and 10% or less in terms of alkaline earth metal, and more preferably 0.2% or more and 8% or less. The compound of the alkaline earth metal is not particularly limited, but the sulfate, carbonate, hydroxide, chloride and oxidation of the alkaline earth metal selected from the group consisting of Ca, Sr and Ba. It is preferably a product, and these compounds may be mixed alone or in combination of two or more. [0062] In the annealing separator, the content of sulfate or sulfide is A% in terms of sulfur element, and satisfies the condition of (0.00025 × Va2) ≦ A ≦ 1.5. When A <(0.00025 × Va2), the effect of increasing the temperature rise rate of the primary recrystallization annealing and increasing the Goss directional particles cannot be utilized, and the effect of improving the magnetic flux density becomes small, which is not preferable. When 1.5