Patent Description:
A grain-oriented electrical steel sheet is generally produced by subjecting a steel slab, which has been adjusted to a predetermined chemical composition, to hot rolling and to cold rolling either once, or twice or more with intermediate annealing performed therebetween, and then to primary recrystallization annealing, followed by final annealing including secondary recrystallization annealing and purification annealing. In the final annealing, since the steel sheet is annealed at a high temperature of about <NUM> in coil form, the coiled steel sheets may stick together. Therefore, it is common practice to apply an annealing separator to the surface of the steel sheet, and subject the steel sheet to secondary recrystallization annealing and then continuously to purification annealing, thereby preventing the steel sheets from sticking together. An annealing separator is generally based on magnesia, and it is hydrated to form a slurry and then applied to a surface of a steel sheet.

In addition to its role as an annealing separator, magnesia also has the function of reacting with a silica-based oxidation layer formed on a surface of a steel sheet by primary recrystallization annealing to form a film of forsterite (Mg<NUM>SiO<NUM>) (hereinafter, also referred to as forsterite film). The forsterite film thus formed have functions of, for example, acting as a kind of binder that adheres an overcoated phosphate-based insulating coating to the steel substrate of the steel sheet, improving the magnetic properties of the steel sheet by applying tension to the steel sheet, and making the appearance of the steel sheet uniform. As described above, the quality of magnesia in the annealing separator is an important factor that influences the magnetic properties and film properties of a grain-oriented electrical steel sheet.

For this reason, various measures have been taken to improve the quality of conventional magnesia. For example, <CIT> (PTL <NUM>) describes a technique of setting phosphorus contained in magnesia to <NUM> mass% to <NUM> mass% in terms of P<NUM>O<NUM> and setting a molar ratio with phosphorus and sulfur of Ca/(Si+P+S) to <NUM> to <NUM> to improve the ability of magnesia to form a forsterite film.

In addition, techniques of adding various compounds to an annealing separator have also been proposed. For example, <CIT> (PTL <NUM>) describes a technique of adding B and P to an annealing separator to promote a solid state reaction between magnesia and silica, thereby obtaining a forsterite film with uniform appearance. <CIT> (PTL <NUM>) describes a technique using Sr compounds, and <CIT> (PTL <NUM>) describes a technique using B compounds, S compounds, and Ti compounds. Further, <CIT> (PTL <NUM>) describes a technique using TiO<NUM> where the surface has been treated with one or more of compounds of Ca, Sr, Ba, Zr, V, Cr, Mn, Fe, Co, Cu, Zn, Al, B, Si, Sn, P, Bi, Sb and B.

In recent years, more stringent requirements have been placed on the properties (particularly low iron loss) of electrical steel sheets from the viewpoint of energy saving. Examples of methods of achieving low iron loss include a method of reducing the thickness of the steel sheet and a method of controlling the orientation of secondary recrystallized grains with higher accuracy, but all of them are likely to deteriorate the appearance uniformity and adhesion of a film. Therefore, there is an even greater demand for an annealing separator capable of forming a forsterite film having excellent appearance uniformity and adhesion even when such a method of achieving low iron loss is applied.

Particularly in a case where the thickness of a forsterite film is reduced to reduce the thickness of a steel sheet, it is clear that the uniformity and adhesion of the forsterite film cannot be fully satisfied with the techniques described in the above patent literatures.

It could thus be helpful to provide an annealing separator with which a grain-oriented electrical steel sheet having a forsterite film with excellent appearance uniformity and adhesion can be obtained.

The invention described in PTL <NUM> is a technique of containing B in magnesia to improve the film reactivity at high temperatures and adding P to an annealing separator to promote the film reaction at low temperatures. Based on the technique described in PTL <NUM>, we have diligently studied a method of further improving the film reaction promoting properties of TiO<NUM> at high temperatures.

The present invention is based on the above findings.

We thus provide an annealing separator for grain-oriented electrical steel sheet and a method of producing a grain-oriented electrical steel sheet as defined in the claims.

According to the present invention, it is possible to provide an annealing separator with which a grain-oriented electrical steel sheet having a forsterite film with excellent appearance uniformity and adhesion can be obtained.

The following describes the present invention in detail.

First, the findings that led to the completion of the present invention will be described in detail.

A forsterite film and a phosphate-based insulating coating are usually formed on a surface of a grain-oriented electrical steel sheet from the surface of the steel sheet to the outside. The forsterite film is formed by a reaction of an oxide film mainly composed of SiO<NUM> formed during primary recrystallization annealing and MgO contained in an annealing separator applied on the oxide film, as indicated in the following formula.

It is known that the forsterite film reaction consists of two steps in each annealing temperature range as follows.

Step of forming olivine ((Fe<NUM>-xMgx)<NUM>SiO<NUM>) by replacing Fe in fayalite (Fe<NUM>SiO<NUM>) formed on the surface of the steel sheet because of the moisture in the annealing separator slurry with Mg by a reaction with magnesia.

Fe<NUM>SiO<NUM> + 2xMgO → (Fe<NUM>-xMgX)<NUM>SiO<NUM> + 2xFeO.

Step of forming forsterite by direct reaction of SiO<NUM> and MgO.

The progress of the reaction in the low temperature range can be confirmed by Fourier transform infrared spectroscopy (FT-IR) of the surface of the steel sheet. That is, the larger the amount of Mg in olivine is, the more the peak position (wave number) of absorbance shifts to a high-wave number side, and therefore it can be judged that the more the peak position shifts to a high-wave number side, the higher the film reactivity is in the low temperature range. Further, the film reactivity in the high temperature range can be evaluated by extracting the oxide formed on the surface of the steel sheet which has been annealed at a heating rate of <NUM>/h up to <NUM>, and analyzing the amount of forsterite formed using FT-IR.

We applied an annealing separator, which had been prepared by blending various elements with magnesia containing an appropriate amount of B, to a steel sheet after primary recrystallization annealing to evaluate the film reactivity in the low temperature range and in the high temperature range. As a result, it was found that the film reaction was promoted especially in the high temperature range and the appearance uniformity and adhesion of the forsterite film were improved by using an annealing separator obtained by blending an appropriate amount of phosphate and titanium oxide that contains alkali metal and is capable of adsorbing an appropriate amount of P on <NUM> of titanium oxide with magnesia that contains an appropriate amount of B.

The mechanism, by which the appearance uniformity and adhesion of the forsterite film are improved by using an annealing separator obtained by blending an appropriate amount of phosphate and titanium oxide that contains an appropriate amount of alkali metal and is capable of adsorbing an appropriate amount of P with magnesia that contains an appropriate amount of B, has not yet been clarified. However, we infer as follows.

MgO reacts with TiO<NUM> in the low temperature range to form double oxides such as MgTiO<NUM>, Mg<NUM>TiO<NUM>, and MgTi<NUM>O<NUM>. These double oxides act like a catalyst in the above-mentioned solid-phase reaction of MgO and SiO<NUM> in the high temperature range, thereby increasing the amount of forsterite formed. At this time, if titanium oxide contains an appropriate amount of alkali metals such as Na and K as impurities, the reaction between TiO<NUM> and MgO is promoted. As a result, the effect of increasing the amount of forsterite formed can be improved.

However, in a case where P is blended as a phosphate in the annealing separator as in the present invention, if the annealing separator is made into a slurry, the phosphate dissociates in the slurry to form phosphate ions. Because the surface of titanium oxide generally tends to adsorb P, the phosphate ions in the slurry are adsorbed on the surface of TiO<NUM>. As a result, after the slurry dries, the surface of TiO<NUM> is covered with the phosphate, which may hinder the solid-phase reaction with MgO. Therefore, it is necessary to suppress the adsorption of P on the surface of TiO<NUM>.

Thus, it is considered that the appearance uniformity and adhesion of the forsterite film are improved by using an annealing separator obtained by blending an appropriate amount of phosphate and titanium oxide that contains an appropriate amount of alkali metal and is capable of adsorbing an appropriate amount of P with magnesia that contains an appropriate amount of B.

Next, reasons for limitations on the features of the present invention will be explained. Note that in this specification, "%" indicating the content of each component element means "mass%" unless otherwise specified.

The content of B in magnesia is <NUM> mass% or more and <NUM> mass% or less.

When the content of B in magnesia is less than <NUM> mass%, sufficient film reactivity cannot be obtained in the high temperature range even in the presence of TiO<NUM>. When the content is more than <NUM> mass%, B penetrates into the steel sheet and reacts with iron to form Fe<NUM>B, which may deteriorate the repeated bending properties of a final steel sheet, or cause film defects such as point-like defects because the film reaction is partially over-promoted. The content of B in magnesia is preferably <NUM> mass% or more. The content of B in magnesia is preferably <NUM> mass% or less.

In the present invention, the amount of the magnesia blended in the annealing separator is preferably <NUM> mass% or more. The amount of the magnesia blended in the annealing separator is more preferably <NUM> mass% or more.

Phosphate is blended in <NUM> parts by mass or more and <NUM> part by mass or less in terms of P per <NUM> parts by mass of magnesia.

When the amount of the phosphate blended is less than <NUM> parts by mass in terms of P, a sufficient film reaction promoting effect cannot be obtained at low temperatures. When it is more than <NUM> part by mass, film defects such as point-like defects are caused because the film reaction is partially over-promoted. The amount of the phosphate blended is preferably <NUM> parts by mass or more per <NUM> parts by mass of magnesia. The amount of the phosphate blended is preferably <NUM> parts by mass or less.

The phosphate may be a phosphate of either an alkali metal (Li, Na, K) or an alkaline earth metal (Mg, Ca, Sr, Ba). However, magnesium and calcium phosphates are preferred because they provide particularly good film appearance uniformity.

Further, examples of the phosphate include orthophosphate, pyrophosphate, and metaphosphate. However, metaphosphate is preferred because it provides particularly good film appearance uniformity.

The total amount of one or more types of alkali metals in titanium oxide is <NUM> mass% or more and <NUM> mass% or less.

When the total amount of one or more types of alkali metals in titanium oxide is less than <NUM> mass%, the effect of promoting the solid-phase reaction between MgO and TiO<NUM> is poor, which in turn leads to an insufficient effect of increasing the amount of forsterite formed. When the total amount of one or more types of alkali metals in titanium oxide is more than <NUM> mass%, the self-sintering of TiO<NUM> is excessively promoted, and the solid-phase reaction with MgO is suppressed, which in turn leads to an insufficient effect of increasing the amount of forsterite formed. The total amount of one or more types of alkali metals in titanium oxide is preferably <NUM> mass% or more and <NUM> mass% or less. The alkali metal may be, for example, one or more selected from the group consisting of Li, Na, K, Rb, Cs, and Fr. Additionally, the ionic radius of the alkali metal affects the solid-phase reaction promoting effect. From the viewpoint of having a preferable ionic radius with which a suitable solid-phase reaction promoting effect can be obtained and the viewpoint of controlling the film reaction, it is preferable to select and use one or two of Na and K among alkali metals.

In the present invention, the content of one or more types of alkali metals in titanium oxide can be quantified by pressurized acid decomposition-ICP emission spectrometry.

The amount of P that can be adsorbed on titanium oxide is <NUM> × <NUM>-<NUM> g or less in terms of P per <NUM> of titanium oxide.

When the amount of P that can be adsorbed on titanium oxide is more than <NUM> × <NUM>-<NUM> g, the solid-phase reaction between MgO and TiO<NUM> is suppressed, which is unsuitable. The amount of P that can be adsorbed on titanium oxide is preferably <NUM> × <NUM>-<NUM> g or less in terms of P per <NUM> of titanium oxide. It is preferable that the titanium oxide does not adsorb any P, so that the amount of P that can be adsorbed on titanium oxide is most preferably <NUM>.

In the present invention, the amount of P that can be adsorbed on titanium oxide is measured as follows.

First, the titanium oxide is immersed in an aqueous solution of <NUM> mass% phosphoric acid (H<NUM>PO<NUM>) for <NUM> minutes and then filtered and washed with water. The sample after being washed with water is alkali-melted and then acid decomposed. The sample after acid decomposition is analyzed by an ICP emission spectrometer, and the amount of P adsorbed on <NUM> of titanium oxide is calculated from the increase in the amount of P in the sample after the immersion in the aqueous solution of phosphoric acid as compared with the amount of P before the immersion.

The amount of titanium oxide blended in the annealing separator is <NUM> part by mass or more and <NUM> parts by mass or less per <NUM> parts by mass of magnesia.

When the amount of titanium oxide blended is less than <NUM> part by mass, the effect of promoting the film reaction cannot be obtained. When the amount of titanium oxide blended is more than <NUM> parts by mass, Ti penetrates into the steel to cause magnetic defects or form black point-like defects on the film, which is unsuitable. The amount of titanium oxide blended in the annealing separator is preferably <NUM> parts by mass or more per <NUM> parts by mass of magnesia. The amount of titanium oxide blended in the annealing separator is preferably <NUM> parts by mass or less per <NUM> parts by mass of magnesia.

Known examples of crystal forms of TiO<NUM> include anatase type, rutile type and brookite type. In the present invention, anatase-type TiO<NUM> is preferred. This is because, although both anatase-type and brookite-type TiO<NUM> improve the solid-phase reactivity between MgO and TiO<NUM> by straining the crystal when it changes to a rutile type at high temperatures, the transition temperature of the anatase type is about <NUM>, which is higher than the transition temperature of the rutile type and the brookite type, so that anatase-type TiO<NUM> enhances the solid-phase reactivity between MgO and TiO<NUM> more easily in the high temperature range.

The basic components of the annealing separator of the present invention have been described above. In addition to these basic components, Sr compounds, sulfates, borates, and the like may be added to the annealing separator as necessary.

Next, a method of producing the above-described annealing separator will be described.

Magnesia may be produced with a known method such as a method of firing magnesium hydroxide or a method of spray firing magnesium chloride (Aman method). At this time, the contents of B and P in the magnesia can be adjusted as specified above by adding a predetermined amount of B compounds and P compounds to the raw material. For example, in the method of firing magnesium hydroxide or the method of spray firing magnesium chloride, a predetermined amount of B compounds and P compounds, such as H<NUM>BO<NUM> and H<NUM>PO<NUM>, may be added to the raw material before firing. In this way, the contents of B and P in the magnesia after firing can be adjusted as specified above.

Titanium oxide may be produced with a known production method such as a sulfuric acid method or a chlorine method. At this time, the content of alkali metals such as Na and K in the titanium oxide can be adjusted as specified above by adding a predetermined amount of alkali metal compounds such as NaOH or KOH to the raw material. For example, in a process of washing titanium hydroxide, which is obtained by a hydration reaction of titanium sulfate, with water in the sulfuric acid method, the content of alkali metals such as Na and K in the titanium oxide can be adjusted as specified above by adding a predetermined amount of alkali metal compounds such as NaOH or KOH to the washing water.

Further, the amount of P that can be adsorbed on <NUM> of titanium oxide can be controlled by, for example, adjusting the firing temperature and firing time when firing titanium hydroxide to obtain TiO<NUM> in the sulfuric acid method. For example, the amount of P that can be adsorbed on titanium oxide can be reduced by performing firing at a relatively low temperature for a long time.

Titanium oxide can be blended with magnesia according to a known method. Further, an annealing separator slurry can be obtained by, for example, mixing magnesia and titanium oxide with water and stirring the mixture at a liquid temperature of <NUM> or lower, preferably <NUM> or lower, and more preferably <NUM> or lower for <NUM> minutes or longer. The content of water of hydration in the annealing separator slurry is <NUM> % to <NUM> %.

Next, a method of producing a grain-oriented electrical steel sheet of the present invention will be described.

The method of producing a grain-oriented electrical steel sheet of the present invention is a method where the above-described annealing separator is used as an annealing separator in a common method of producing a grain-oriented electrical steel sheet using an annealing separator.

First, a steel slab is produced according to a common production method. For example, a steel slab is produced by performing ingot casting or continuous casting using molten steel that has been adjusted to a predetermined chemical composition.

Next, the steel slab is subjected to hot rolling to obtain a hot-rolled steel sheet. For example, the steel slab is heated to <NUM> or higher and then subjected to hot rolling. The reheating method may be a known method using, for example, a gas furnace, an induction heating furnace, or an electric furnace. The conditions of the hot rolling may be any conventionally known conditions, which are not particularly limited.

Next, the hot-rolled steel sheet is subjected to hot-rolled sheet annealing as necessary, then scale on the surface of the steel sheet is removed by, for example, pickling, and then the hot-rolled steel sheet is subjected to cold rolling either once, or twice or more with intermediate annealing performed therebetween to obtain a cold-rolled steel sheet with a final sheet thickness.

Next, the cold-rolled steel sheet is subjected to primary recrystallization annealing to obtain a primary recrystallized sheet. The primary recrystallization annealing may also serve as decarburization annealing.

Next, the above-described annealing separator is applied as a slurry on the surface of the primary recrystallized sheet. The amount of the annealing separator applied to the primary recrystallized sheet is not particularly limited, but it is preferably <NUM> or more and <NUM> or less per <NUM><NUM> of the surface of the primary recrystallized sheet on both sides. Note that the amount applied is the weight of the annealing separator slurry after it is applied and dried. When the amount of the annealing separator applied on both sides is <NUM> or more per <NUM><NUM> of the surface of the primary recrystallized sheet, it is possible to suitably prevent the steel sheets from sticking together during final annealing. On the other hand, it is useless to apply more than <NUM> per <NUM><NUM> of the surface of the primary recrystallized sheet on both sides from an economic point of view.

Next, the primary recrystallized sheet applied with the annealing separator is subjected to secondary recrystallization annealing to obtain a secondary recrystallized sheet. In the secondary recrystallization annealing, it is preferable to hold the primary recrystallized sheet in a temperature range of <NUM> or higher and <NUM> or lower for <NUM> hours or longer and <NUM> hours or shorter. This is because, in order to control the orientation of secondary recrystallized grains with high accuracy, it is preferable to hold the sheet in a temperature range in which secondary recrystallization progresses for a long time. When the holding temperature is lower than <NUM>, secondary recrystallization does not occur. When the holding temperature is higher than <NUM>, the growth rate of secondary recrystallized grains is too fast to control the orientation. When the holding time is shorter than <NUM> hours, secondary recrystallization is not completed. When the holding time is longer than <NUM> hours, the shape of the coil may be deteriorated due to high temperature creep phenomenon, which is unsuitable. It is more preferable to hold the primary recrystallized sheet in a temperature range of <NUM> or higher and <NUM> or lower for <NUM> hours or longer and <NUM> hours or shorter.

Note that in the present specification, being held in a predetermined temperature range for a predetermined time not only means being held isothermally at a predetermined temperature, but also includes being held for a predetermined time while changing the temperature within a predetermined temperature range. Therefore, for example, a process of raising the temperature up to a temperature range of the purification annealing described later may also serve as the secondary recrystallization annealing described above. For example, in a process of raising the temperature of the primary recrystallized sheet that has been applied with the annealing separator to about <NUM>, the heating rate from <NUM> to <NUM> is set to <NUM>/h or more and <NUM>/h or less, and then the holding time in the temperature range of <NUM> to <NUM> can be set to <NUM> hours or longer and <NUM> hours or shorter.

After the secondary recrystallization annealing, the secondary recrystallized sheet is subjected to purification annealing. The purification annealing may be performed with a known method. For example, the secondary recrystallized sheet may be held at a high temperature of about <NUM> for <NUM> hours or longer.

Magnesium hydroxide was added with H<NUM>BO<NUM>, and the mixture was fired at <NUM> for <NUM> minutes to prepare magnesia. The content of B in the magnesia was as listed in Table <NUM>.

Titanium oxide was prepared with a sulfuric acid method. At this time, NaOH and KOH were added to the washing water in the process where titanium hydroxide formed by a hydration reaction of titanium sulfate was washed with water as described above. After being washed with water, the titanium hydroxide cake was fired at <NUM> to <NUM> for <NUM> hours to <NUM> hours to prepare titanium oxide. The contents of Na and K in the prepared titanium oxide and the amount of P that can be adsorbed on <NUM> of titanium oxide were as listed in Table <NUM>. The TiO<NUM> in titanium oxide was anatase-type TiO<NUM>.

The prepared titanium oxide was blended in the amount listed in Table <NUM> per <NUM> parts by weight of magnesia. Magnesium metaphosphate (Mg(PO<NUM>)<NUM>) was blended as a phosphate in the amount listed in Table <NUM> per <NUM> parts by weight of magnesia. The annealing separator was mixed with water, and the mixture was stirred at a liquid temperature of <NUM> or lower for <NUM> minutes or longer to obtain an annealing separator slurry. The content of water of hydration in the annealing separator slurry was <NUM> % to <NUM> %.

A steel slab containing C: <NUM> %, Si: <NUM> %, Mn: <NUM> %, Al: <NUM> ppm, N: <NUM> ppm and S: <NUM> ppm, with the balance being Fe and inevitable impurities, was subjected to slab heating at <NUM> for <NUM> minutes and then to hot rolling to obtain a sheet thickness of <NUM>, thereby obtaining a hot-rolled sheet. The hot-rolled sheet was coiled by a coiler to obtain a hot-rolled sheet coil. The hot-rolled sheet was subjected to hot-rolled sheet annealing at <NUM> for <NUM> seconds. After the hot-rolled sheet annealing, scale on the surface of the steel sheet was removed. Next, cold rolling was performed using a tandem mill to obtain a final cold rolled sheet thickness of <NUM>. Next, primary recrystallization annealing was performed at a soaking temperature of <NUM> for <NUM> seconds to obtain a primary recrystallized sheet.

Next, the annealing separator prepared as described above was made into a slurry, applied on the primary recrystallized sheet on both sides in an amount of <NUM> per <NUM><NUM> of the steel sheet and dried, and then the steel sheet was coiled into a coil. The coil was subjected to secondary recrystallization annealing where the temperature was raised to <NUM> at <NUM>/h to obtain a secondary recrystallized sheet. The secondary recrystallized sheet was then subjected to purification annealing at <NUM> for <NUM> hours. Next, it was annealed for smoothing at <NUM> for <NUM> seconds to obtain a grain-oriented electrical steel sheet.

The appearance uniformity and adhesion of the forsterite film of the obtained grain-oriented electrical steel sheet were evaluated. The appearance uniformity of the film was evaluated visually. When the total length of pattern (non-uniformity of color tone of the film) or defect was <NUM> % or more of the total length of the coil, it was judged as "poor"; when the total length of pattern or defect was less than <NUM> % and <NUM> % or more, it was judged as "good"; when the total length of pattern or defect was less than <NUM> %, it was judged as "excellent". The adhesion of the film was judged by coiling steel sheets that had been sheared to a width of <NUM> and a length of <NUM> around the surfaces of <NUM> round bars with different diameters in <NUM> increments from <NUM> to <NUM> in diameter, and determining the minimum diameter that did not cause defect or peeling in the film. When the minimum diameter at which peeling occurred was <NUM> or more, it was judged as "poor"; when the minimum diameter was <NUM> or less and more than <NUM>, it was judged as "fair"; when the minimum diameter was <NUM> or less and more than <NUM>, it was judged as "good"; when the minimum diameter was <NUM> or less, it was judged as "excellent". When the judgment is "good" or "excellent" for the appearance uniformity or the adhesion of the film, it can be said that the appearance uniformity or the adhesion of the film is excellent. The evaluation results are listed in Table <NUM>.

From Table <NUM>, it can be seen that, by applying an annealing separator in which the content of B in magnesia, the total amount of one or more types of alkali metals in titanium oxide, the amount of P that can be adsorbed on <NUM> of titanium oxide, and the amount of phosphate and titanium oxide blended with magnesia are as specified in the present invention, it is possible to obtain a grain-oriented electrical steel sheet having a film with excellent appearance uniformity and adhesion.

Magnesium hydroxide was added with H<NUM>BO<NUM>, and the mixture was fired at <NUM> for <NUM> hours to prepare magnesia. The content of B in the magnesia was <NUM> mass%.

Titanium oxide was prepared with a sulfuric acid method. At this time, NaOH and KOH were added to the washing water in the process where titanium hydroxide formed by a hydration reaction of titanium sulfate was washed with water. After being washed with water, the titanium hydroxide cake was fired under Condition A, that is, fired at <NUM> for <NUM> hours, to obtain titanium oxide containing anatase-type TiO<NUM> with an amount of P adsorption of <NUM> × <NUM>-<NUM> g (indicated as type "A" of titanium oxide in Table <NUM>). Additionally, after being washed with water, the titanium hydroxide cake was fired under Condition R, that is, fired at <NUM> for <NUM> hour, to obtain titanium oxide containing rutile-type TiO<NUM> where an amount of P that can be adsorbed on <NUM> of the titanium oxide was <NUM> × <NUM>-<NUM> g (indicated as type "R" of titanium oxide in Table <NUM>). In both cases of the anatase-type TiO<NUM> and the rutile-type TiO<NUM>, the content of Na in the titanium oxide was <NUM> mass%, and the content of K in the titanium oxide was <NUM> mass%.

The prepared titanium oxide and various phosphates were blended in the amount listed in Table <NUM> per <NUM> parts by mass of magnesia to prepare an annealing separator. The annealing separator was mixed with water, and the mixture was stirred at a liquid temperature of <NUM> or lower for <NUM> minutes or longer to obtain an annealing separator slurry. The content of water of hydration in the annealing separator slurry was <NUM> % to <NUM> %.

A steel slab containing C: <NUM> %, Si: <NUM> %, Mn: <NUM> %, Al: <NUM> ppm, N: <NUM> ppm, S: <NUM> ppm, Se: <NUM> %, Sb: <NUM> % and Cr: <NUM> %, with the balance being Fe and inevitable impurities, was subjected to slab heating at <NUM> for <NUM> minutes and then to hot rolling to obtain a sheet thickness of <NUM>, thereby obtaining a hot-rolled sheet. The hot-rolled sheet was coiled by a coiler to obtain a hot-rolled sheet coil. The hot-rolled sheet was subjected to hot-rolled sheet annealing at <NUM> for <NUM> seconds. After the hot-rolled sheet annealing, scale on the steel sheet surface was removed. Next, the steel sheet was subjected to cold rolling with intermediate annealing at <NUM> for <NUM> seconds performed therebetween, to obtain a final cold rolled sheet thickness of <NUM>. Next, primary recrystallization annealing was performed at a soaking temperature of <NUM> for <NUM> seconds to obtain a primary recrystallized sheet.

The annealing separator was applied on the primary recrystallized sheet on both sides in an amount of <NUM> per <NUM><NUM> of the steel sheet and dried. Next, the steel sheet was subjected to secondary recrystallization annealing where the temperature was raised from <NUM> to <NUM> at <NUM>/h to obtain a secondary recrystallized sheet. Next, the temperature of the secondary recrystallized sheet was raised from <NUM> to <NUM> at <NUM>/h. Next, after performing purification annealing at <NUM> for <NUM> hours, the steel sheet was annealed for smoothing at <NUM> for <NUM> seconds to obtain a grain-oriented electrical steel sheet.

With respect to the obtained grain-oriented electrical steel sheet, the appearance uniformity and adhesion of the forsterite film were evaluated based on the same criteria as in Example <NUM>. The evaluation results are listed in Table <NUM>.

Claim 1:
An annealing separator for grain-oriented electrical steel sheet, comprising:
magnesia that contains <NUM> mass% or more and <NUM> mass% or less of B and is mainly composed of MgO,
a phosphate in <NUM> parts by mass or more and <NUM> part by mass or less in terms of P per <NUM> parts by mass of the magnesia, and
titanium oxide in <NUM> part by mass or more and <NUM> parts by mass or less per <NUM> parts by mass of the magnesia, where the titanium oxide contains one or more types of alkali metals in a total amount of <NUM> mass% or more and <NUM> mass% or less and is mainly composed of TiO<NUM>, wherein
the titanium oxide is capable of adsorbing P in an amount of <NUM> × <NUM>-<NUM> g or less on <NUM> of the titanium oxide, and
the amount of P that can be adsorbed on <NUM> of the titanium oxide is measured according to the method disclosed in the description.