JP6256693B2 - Oriented electrical steel sheet and manufacturing method thereof - Google Patents

Description

  The present invention relates to a grain-oriented electrical steel sheet and a method for producing the same, specifically, a method for producing a grain-oriented electrical steel sheet having low iron loss, small variation in iron loss value, and excellent in coating quality, and a method for producing the same. It is about.

  Electrical steel sheets are soft magnetic materials widely used as materials for transformers, motor cores, etc. Above all, grain oriented electrical steel sheets are highly integrated in the {110} <001> orientation whose crystal orientation is called the Goss orientation. Because of its excellent magnetic properties, it is mainly used for iron cores of large transformers. In order to reduce no-load loss (energy loss) in the transformer, it is important that the material steel plate has low iron loss. In a grain-oriented electrical steel sheet, iron loss can be reduced by increasing the Si content, reducing the thickness, improving the orientation of the crystal orientation, imparting tension to the steel sheet, smoothing the steel sheet surface, and secondary recrystallization. It is known that finer structure is effective.

Among the above methods, as a technique for refining the secondary recrystallized grains, the primary recrystallized texture is formed by performing rapid heating at the time of decarburization annealing or by performing heat treatment to be rapidly heated immediately before decarburization annealing. A method for improvement has been proposed. For example, in Patent Document 1, when decarburizing and annealing a cold-rolled sheet rolled to the final sheet thickness, 700 ° C./s or more is 700 in a non-oxidizing atmosphere having a PH ₂ O / PH ₂ of 0.2 or less. A technique for obtaining a grain-oriented electrical steel sheet having a low iron loss by rapid heating to a temperature of ℃ or higher is disclosed. Patent Document 2 discloses that the oxygen concentration in the atmosphere is 500 ppm or less, rapid heating is performed at a heating rate of 100 ° C./s or higher to a temperature of 800 to 950 ° C., and subsequently 775 to 840 ° C. lower than the rapidly heated temperature. A technique for obtaining a grain-oriented electrical steel sheet with low iron loss by holding at a temperature and further holding at a temperature of 815 to 875 ° C. is disclosed. Further, in Patent Document 3, a temperature range of 600 ° C. or higher is heated to 800 ° C. or higher at a rate of temperature increase of 95 ° C./s or higher, and then the atmosphere in this temperature range is appropriately controlled to obtain film characteristics and magnetic properties. A technique for obtaining an electrical steel sheet having excellent characteristics is disclosed. Furthermore, in Patent Document 4, the amount of N as AlN in the hot-rolled sheet is limited to 25 ppm or less, and at the time of decarburization annealing, heating is performed at a heating rate of 80 ° C./s to 700 ° C. A technique for obtaining loss-oriented electrical steel sheets is disclosed.

  In these techniques for improving the primary recrystallization texture by rapid heating, the temperature range for rapid heating is set from room temperature to 700 ° C. or higher, and the rate of temperature rise is regulated within a certain range. This technical idea suppresses the development of γ fibers ({111} // ND orientation) formed preferentially at a normal heating rate by raising the temperature up to the vicinity of the recrystallization temperature in a short time, The primary recrystallization texture is intended to be improved by promoting the generation of a {110} <001> structure that becomes the nucleus of secondary recrystallization. By applying this technique, crystal grains (Goss orientation grains) after secondary recrystallization are refined, and iron loss characteristics are improved.

  On the other hand, rapid heating before decarburization annealing of the steel sheet cold-rolled to the final plate thickness causes problems that the decarburization property is lowered and the structure of the internal oxide layer becomes dendritic. As a technique for solving this problem, for example, Patent Document 5 discloses a technique for improving the decarburization property by setting the oxidizing property of the atmosphere to an appropriate range and suppressing the formation of a dense oxide layer on the steel sheet surface. However, in Patent Document 6, the surface of the steel sheet after decarburization annealing is measured by high-frequency glow discharge optical emission spectrometry, and the surface of the steel sheet is determined from the change in the depth method of the amount of at least one element in the steel sheet. Methods have been proposed to evaluate and control the decarburization annealing condition projection.

Japanese Patent Laid-Open No. 07-062436 Japanese Patent Laid-Open No. 10-298653 JP 2003-027194 A Japanese Patent Laid-Open No. 10-130729 Japanese Patent Laid-Open No. 10-152724 JP 2004-191237 A

  By the way, according to the knowledge of the inventors, when the temperature increase rate of the primary recrystallization annealing (decarburization annealing) is increased, the variation of the iron loss characteristic that seems to be caused by the temperature unevenness inside the steel plate at the time of temperature increase becomes large. . The iron loss evaluation at the time of product shipment is generally performed using the average value of the iron loss of the full width of the steel sheet, but if the dispersion is large, the iron loss value of the average width of the steel sheet is compared with the best place. As a result, the desired rapid heating effect cannot be obtained.

  In general, the surface of the grain-oriented electrical steel sheet is formed with two layers of a ceramic base coating on the steel plate side and a glassy insulating coating on the surface side. Since the adhesion between the vitreous and the ground iron is low, the film adhesion is improved by interposing a base film such as forsterite between them. However, when the temperature increase rate of the primary recrystallization annealing (decarburization annealing) is increased, there is also a problem that the occurrence rate of point-like defects that may be caused by excessive film thickness of the forsterite layer formed on the steel sheet surface increases. .

  The present invention has been made in view of the above problems of the prior art, and its purpose is to optimize the temperature increase pattern of primary recrystallization annealing (decarburization annealing), thereby reducing iron loss with low iron loss. In addition to providing a grain-oriented electrical steel sheet having small variations in values and excellent coating quality, an advantageous manufacturing method thereof is proposed.

The inventors have intensively studied to solve the above problems. As a result, when rapid heating is performed in the temperature raising process of primary recrystallization annealing (decarburization annealing), the temperature inside the steel sheet is made uniform by repeatedly performing a holding process for a predetermined time in a temperature range where recovery occurs. The effect of rapid heating, ie, <111> // ND orientation preferentially recovers, <111> // ND orientation after primary recrystallization decreases, and Goss nuclei increase, resulting in secondary recrystallization. Since the effect that the subsequent recrystallization is refined can be obtained uniformly over the entire width of the steel sheet, it is possible to stably obtain a grain-oriented electrical steel sheet with low iron loss and small variations in iron loss values. In addition, by performing the retention treatment, in the oxidation process in the initial stage of decarburization annealing, the core of silica SiO ₂ is densely formed, and a thin and uniform internal oxide layer is formed. During the subsequent decarburization annealing, Uniform inside It has been found that a grain-oriented electrical steel sheet having a very small variation in the film thickness of the forsterite film after finish annealing and with few film defects can be obtained. It came to develop.

を用いて求められるａを被膜成分密度と定義したとき、上記被膜成分密度ａが０．８０〜０．９７の領域における、下記（２）式；

で定義される上記被膜成分密度ａの深さ方向の傾きの平均値ｂが８μｍ^−１以上３００μｍ ^−１ 以下であることを特徴とする方向性電磁鋼板。
本発明の方向性電磁鋼板は、上記成分組成に加えてさらに、Ｎｉ：０．００１〜０．０１５ｍａｓｓ％、Ｓｂ：０．００５〜０．５０ｍａｓｓ％、Ｓｎ：０．００５〜０．５０ｍａｓｓ％、Ｂｉ：０．００５〜０．５０ｍａｓｓ％、Ｍｏ：０．００５〜０．１０ｍａｓｓ％、Ｂ：０．０００２〜０．００２５ｍａｓｓ％、Ｔｅ：０．０００５〜０．０１０ｍａｓｓ％、Ｎｂ：０．００１０〜０．０１０ｍａｓｓ％、Ｖ：０．００１〜０．０１０ｍａｓｓ％およびＴａ：０．００１〜０．０１０ｍａｓｓ％のうちから選ばれる１種または２種以上を含有することを特徴とする。 That is, the present invention comprises a component composition containing C: 0.005 mass% or less, Si: 2.0-8.0 mass%, and Mn: 0.005-1.0 mass%, with the balance being Fe and inevitable impurities. In a grain-oriented electrical steel sheet having a ceramic base coating and a glassy insulating coating on the steel sheet surface, the steel sheet surface was analyzed by glow discharge optical emission spectrometry, and the obtained Si, Mg, O and Fe The emission intensity in the depth direction (z direction) of each element of I is I _Si , I _Mg , I 2 _O, and I 2 _Fe , respectively, and from the emission intensity, the following formula (1):

When a defined as a film component density is defined as the following formula (2) in the region where the film component density a is 0.80 to 0.97;

The grain ^- oriented electrical steel sheet, wherein the average value b of the gradient in the depth direction of the film component density a defined by is 8 μm ⁻¹ or more and 300 μm ⁻¹ or less .
In addition to the above component composition, the grain-oriented electrical steel sheet of the present invention further includes Ni: 0.001 to 0.015 mass%, Sb: 0.005 to 0.50 mass%, Sn: 0.005 to 0.50 mass%, Bi: 0.005-0.50 mass%, Mo: 0.005-0.10 mass%, B: 0.0002-0.0025 mass%, Te: 0.0005-0.010 mass%, Nb: 0.0010 It contains one or more selected from 0.010 mass%, V: 0.001 to 0.010 mass%, and Ta: 0.001 to 0.010 mass%.

  The grain-oriented electrical steel sheet of the present invention is characterized in that the average value b of the gradient in the depth direction of the film component density a is in the range of 12 to 200.

Further, the grain-oriented electrical steel sheet of the present invention, the steel sheet surface, in a direction crossing the rolling direction, having a groove, or have a thermal strain or impact strain by continuously or intermittently electron beam irradiation or laser irradiation It is characterized by.

Further, the present invention contains C: 0.002 to 0.10 mass%, Si: 2.0 to 8.0 mass%, Mn: 0.005 to 1.0 mass%, and further contains Al as an inhibitor forming component. And N in a range of Al: 0.010 to 0.050 mass%, N: 0.003 to 0.020 mass%, and / or S: 0.002 to 0.030 mass% and Se: 0, respectively. A steel material containing one or two selected from 0.003 to 0.030 mass%, the balance of which is composed of Fe and inevitable impurities, is hot-rolled into a hot-rolled sheet, After annealing or hot-rolled sheet annealing without annealing, it is cold-rolled to the final thickness by one or more cold rollings sandwiching intermediate annealing, and primary recrystallization annealing to form an internal oxide layer In the method for producing a grain-oriented electrical steel sheet comprising a series of steps in which an annealing separator is applied to the steel sheet surface, dried and wound on a coil, then subjected to finish annealing, and then an insulating coating is formed on the steel sheet surface. In addition, the section of 100 to 700 ° C. in the heating process of the primary recrystallization annealing is rapidly heated at a heating rate of 50 ° C./s or more, and at any temperature between 250 and 600 ° C. during the heating, 0.5 to A method for producing a grain-oriented electrical steel sheet according to any one of the above is proposed, wherein the holding treatment for 10 seconds is repeated 2 to 6 times.
Moreover, this invention contains C: 0.002-0.10 mass%, Si: 2.0-8.0mass%, Mn: 0.005-1.0mass%, Furthermore, Al: 0.01 mass% Less than N, less than 0.0050 mass%, S: less than 0.0050 mass%, and Se: less than 0.0030 mass%, and the steel material which consists of the component composition which consists of Fe and an unavoidable impurity in the remainder is hot-rolled. After hot-rolled sheet annealing or hot-rolled sheet annealing, the final thickness of the cold-rolled sheet is obtained by one or more cold rollings sandwiching intermediate annealing. A series of steps to perform primary recrystallization annealing to form an oxide layer, apply and dry an annealing separator on the surface of the steel sheet, wind it on a coil, then finish annealing, and then form an insulating film on the surface of the steel sheet Direction consisting of In the manufacturing method of the electrical steel sheet, the section of 100 to 700 ° C. in the heating process of the primary recrystallization annealing is rapidly heated at a temperature rising rate of 50 ° C./s or more, and any one of 250 to 600 ° C. during the heating is performed. The method for producing a grain-oriented electrical steel sheet according to any one of claims 1 to 4, wherein a holding treatment for holding at a temperature for 0.5 to 10 seconds is repeated 2 to 6 times.
In addition to the above component composition, the steel material in the production method of the present invention further includes Ni: 0.001 to 0.015 mass%, Sb: 0.005 to 0.50 mass%, Sn: 0.005 to 0.50 mass. %, Bi: 0.005-0.50 mass%, Mo: 0.005-0.10 mass%, B: 0.0002-0.0025 mass%, Te: 0.0005-0.010 mass%, Nb: 0.0. It contains one or more selected from 0010 to 0.010 mass%, V: 0.001 to 0.010 mass%, and Ta: 0.001 to 0.010 mass%.

  According to the present invention, when the primary recrystallization annealing (decarburization annealing) is rapidly heated, the holding treatment for a predetermined time is repeatedly performed a predetermined number of times in a temperature region where the recovery occurs, so that the iron loss value is low. It becomes possible to stably manufacture grain-oriented electrical steel sheets with small variations. Further, by performing the above-described retention treatment in a temperature region where the nucleus of the internal oxide layer is generated, it becomes possible to stably manufacture a grain-oriented electrical steel sheet having a uniform and excellent coating appearance.

It is a figure explaining the temperature rising pattern of this invention in primary recrystallization annealing (decarburization annealing). It is a graph which shows the influence of the retention process which acts on the inclination (da / dz) between 0.80-0.97 of the film component density a. It is a graph which shows the relationship between the holding _{| maintenance} process frequency in the middle of the heating of primary recrystallization annealing (decarburization annealing), and iron loss _{W17 / 50} . It is a graph which shows the relationship between the holding temperature in the middle of the heating of primary recrystallization annealing (decarburization annealing), and iron loss _{W17 / 50} . It is a graph which shows the relationship between the holding time in the middle of the heating of primary recrystallization annealing (decarburization annealing), and iron loss _{W17 / 50} .

First, an experiment that triggered the development of the present invention will be described.
<Experiment 1>
Steel containing C: 0.065 mass%, Si: 3.4 mass%, Mn: 0.08 mass% was melted and made into a steel slab by a continuous casting method, then reheated to 1410 ° C and hot-rolled. The steel sheet is then hot-rolled with a thickness of 2.4 mm and subjected to hot-rolled sheet annealing at 1050 ° C. for 60 seconds, followed by primary cold rolling to an intermediate sheet thickness of 1.8 mm, and intermediate annealing at 1120 ° C. for 80 seconds. Then, a cold rolled sheet having a final thickness of 0.27 mm was obtained by warm rolling at 200 ° C.
Next, primary recrystallization annealing was performed in a wet atmosphere of 50 vol% H ₂ -50 vol% N ₂ , which also served as decarburization annealing at 840 ° C. for 80 seconds. The heating for the primary recrystallization annealing is performed at a temperature increase rate of 100 ° C./s between 100 and 700 ° C. At this time, as shown in Table 1, any temperature between 450 and 700 ° C. during the heating is used. The holding treatment for 2 seconds at that temperature was repeated 0 times (no holding treatment) to 7 times, and then the temperature was raised from 700 ° C. to 840 ° C. at 100 ° C./s. Here, as shown in FIG. 1, the temperature increase rate of 100 ° C./s is the average temperature increase rate in the time of (t1 + t3 + t5) excluding the holding time t2 and t4 from the time to reach from 100 ° C. to 700 ° C. ((700-100) / (t1 + t3 + t5)) (Hereafter, the average rate of temperature increase during the heating time excluding the holding time is used in the same manner as described above, regardless of the number of times of holding).
Next, an annealing separator mainly composed of MgO is applied to the surface of the steel sheet and dried, and then wound on a coil to be subjected to a secondary recrystallization annealing and a final annealing consisting of 1200 ° C. × 7 hours of purification annealing in a hydrogen atmosphere. Was given. Then, the product coil was obtained by performing flattening annealing for forming a tension-imparting coating. At that time, the surface of the steel sheet was visually observed over the entire length of the coil, the length of the occurrence of the point-like film defects was measured, and the occurrence rate of the point-like defects was obtained. Here, the occurrence rate of the point-like defects was defined by (defect occurrence length / coil length) × 100 (%) (hereinafter the same).

で定義される被膜成分密度ａが０．８０〜０．９７の間における、下記（２）式；

で定義される上記ａの深さ方向の傾き（ｄａ／ｄｚ）の平均値ｂ（以降、単に「被膜成分密度ａの傾きｂ」とも称する）を求めた。 In addition, from each product coil obtained as described above, 10 test pieces each having a width of 100 mm and a length of 500 mm were collected in the plate width direction of the steel sheet, and the iron loss W _{17 /} was measured by the method described in JIS C2556. ₅₀ was measured, and the average value of the iron loss values of 10 sheets was obtained. This is because, according to this iron loss measurement method, when the variation in iron loss is in the sheet width direction, the average value is deteriorated, so it is considered that the iron loss can be evaluated including the variation.
Moreover, the surface of the test piece collected from each product coil is analyzed by glow discharge emission spectroscopy (GDS), and Si, Mg, in the depth direction (the z direction, hereinafter the same) are analyzed. The emission intensity (I _Si , I _Mg , I _{O and} I _Fe ) distribution of _{O and Fe} was measured, and the following formula (1):

The following formula (2) when the film component density a defined by is between 0.80 and 0.97:

The average value b of the inclination (da / dz) in the depth direction of the a defined by (hereinafter, also simply referred to as “the inclination b of the film component density a”) was obtained.

  For reference, FIG. 2 shows a comparison of the GDS measurement results when the number of holding processes is zero (no holding process) and two times in the above experiment. When the retention treatment is not performed, the film component density gradually decreases (FIG. 2A), whereas when the retention treatment is performed twice, the film component density a rapidly decreases. (FIG. 2B). That is, it can be seen that the slope (da / dz) of the coating component density a between 0.80 and 0.97 is greatly changed by performing the retention treatment.

The measurement results of the incidence rate of the above point defects, the iron loss W _17/50, and the slope b of the coating component density a are shown in Table 1, and the relationship between the number of holding treatments and the iron loss W _17/50 is shown in FIG. Indicated.
From these results, it was found that the iron loss was reduced and the occurrence rate of point-like defects was reduced by repeatedly performing the holding treatment in the range of 2 to 6 times during heating.
Further, it was found that the slope b of the coating component density a is 8 μm ⁻¹ or more in the product coil in which the iron loss is reduced and the occurrence rate of the point-like defects is also reduced.

<Experiment 2>
A primary recrystallization annealing performed on the cold rolled sheet having a final thickness of 0.27 mm obtained in Experiment 1 in a wet atmosphere of 50 vol% H ₂ -50 vol% N ₂ and also performing decarburization annealing at 840 ° C. for 80 seconds. Was given. In addition, in the heating of the primary recrystallization annealing, the temperature is raised between 100 and 700 ° C. at a rate of temperature increase of 100 ° C./s. At this time, as shown in Table 2, any heating temperature between 200 and 700 ° C. The holding treatment of holding at that temperature for 2 seconds was repeated twice, and then the temperature was increased from 700 ° C. to 840 ° C. at 100 ° C./s.
Next, an annealing separator mainly composed of MgO is applied to the surface of the steel sheet and dried, and then wound on a coil to be subjected to a secondary recrystallization annealing and a final annealing consisting of 1200 ° C. × 7 hours of purification annealing in a hydrogen atmosphere. Was given. Then, the product coil was obtained by performing flattening annealing for forming a tension-imparting coating. At that time, the surface of the steel sheet was visually observed over the entire length of the coil, the length of the point-like film defect occurrence was measured, and the occurrence rate of the point-like defect was obtained.

A test piece was collected from the product coil thus obtained, and in the same manner as in Experiment 1, the iron loss W _17/50 was measured by the method described in JIS C2556, and the surface of the test piece was analyzed by GDS. The slope b of the density a was determined. The results of measurement of the incidence of the above point-like defects, iron loss W _17/50 and slope b of the coating component density a are shown in Table 2 and the relationship between the two holding temperatures during heating and the iron loss _17/50. Is shown in FIG. The holding temperature in FIG. 4 is the lower holding temperature when the higher holding temperature is 450 ° C. or lower, and the higher holding temperature when the higher holding temperature exceeds 450 ° C. Using.
From these results, by setting the holding temperature between 250 and 600 ° C., the iron loss is reduced, the slope b of the coating component density a is 8 μm ⁻¹ or more, and the incidence of coating failure is reduced. I found out.

<Experiment 3>
A primary recrystallization annealing performed on the cold rolled sheet having a final thickness of 0.27 mm obtained in Experiment 1 in a wet atmosphere of 50 vol% H ₂ -50 vol% N ₂ and also performing decarburization annealing at 840 ° C. for 80 seconds. Was given. In addition, the heating of the said primary recrystallization annealing raises between 100-700 degreeC with the temperature increase rate of 100 degree-C / s, At this time, as shown in Table 3, in 450 degreeC and 500 degreeC in the middle of heating, Each holding process for 0.5 to 20 seconds was repeated twice, and then the temperature was increased from 700 ° C. to 840 ° C. at 100 ° C./s.
Next, an annealing separator mainly composed of MgO is applied to the surface of the steel sheet and dried, and then wound on a coil to be subjected to a secondary recrystallization annealing and a final annealing consisting of 1200 ° C. × 7 hours of purification annealing in a hydrogen atmosphere. Was given. Then, the product coil was obtained by performing flattening annealing for forming a tension-imparting coating. At that time, the surface of the steel sheet was visually observed over the entire length of the coil, the length of the point-like film defect occurrence was measured, and the occurrence rate of the point-like defect was obtained.

A test piece was collected from the product coil thus obtained, and in the same manner as in Experiment 1, the iron loss W _17/50 was measured by the method described in JIS C2556, and the surface of the test piece was analyzed by GDS. The slope b of the density a was determined. The results of measurement of the incidence of the above point defects, the iron loss W _17/50 and the slope b of the coating component density a are shown in Table 3, and the relationship between the two holding times during heating and the iron loss _17/50 Is shown in FIG. In addition, when the holding time of 2 times differs, the longer time was used for the holding time of FIG.
From these results, by setting the retention treatment time per time in the range of 0.5 to 10 seconds, the iron loss is reduced, the slope b of the coating component density a is 8 μm ⁻¹ or more, and the coating failure is poor. It was found that the incidence was reduced.

As for the results of Experiments 1 to 3 above, the reason why the iron loss is reduced by repeating the retention treatment for the appropriate time at the appropriate temperature in the heating process of primary recrystallization annealing (decarburization annealing) is still Although not sufficiently clear, the inventors consider as follows.
As described above, the rapid heating has an effect of suppressing the development of <111> // ND orientation in the recrystallized texture. In general, since more strain is introduced in the <111> // ND orientation of the cold rolled sheet after cold rolling than in other orientations, the accumulated strain energy is high. For this reason, in normal heating at a heating rate of about 20 ° C./s, recrystallization occurs preferentially from the <111> // ND orientation where the accumulated strain energy is high. In recrystallization, <111> // ND orientation grains appear from the <111> // ND orientation, and thus the structure after recrystallization has the <111> // ND orientation as the main orientation. However, since rapid heating gives more thermal energy than that released by recrystallization, recrystallization occurs even in orientations with relatively low strain energy, and relatively recrystallization occurs. The <111> // ND orientation after crystallization is reduced and the magnetic properties are improved. This is the reason for rapid heating in the prior art.

  However, when a holding treatment is performed at a temperature at which recovery during the rapid heating occurs for a predetermined time, the <111> // ND orientation with high strain energy is preferentially recovered. For this reason, the driving force that causes <111> // ND orientation to cause recrystallization selectively decreases, and as a result, other orientations cause recrystallization. // ND orientation further decreases.

  In addition, the reason why the holding process is repeated twice or more is that the <111> // ND orientation can be reduced more efficiently than when the holding process is performed once, so that the iron loss characteristic is further improved. Can do. On the other hand, if the number of holding treatments exceeds 7, and if the holding treatment for a predetermined time is performed, recovery occurs in a wide range of the rolled structure, so that the recovered structure remains as it is without causing recrystallization. Become an organization. As a result, the secondary recrystallization is greatly adversely affected, leading to a decrease in iron loss characteristics.

  In addition, according to the above-mentioned idea, the effect of improving the magnetic characteristics by performing a short-time holding treatment at a temperature at which recovery during the primary recrystallization annealing (decarburization annealing) occurs can be obtained. It is considered that the heating rate is higher than the rate of temperature increase (10 to 20 ° C./s) using a tube or the like, specifically, the rate of temperature increase is 50 ° C./s or more. Therefore, in the present invention, the rate of temperature rise in the section of 100 to 700 ° C. in the heating process of primary recrystallization annealing (decarburization annealing) is defined as 50 ° C./s or more.

In addition, as in the results of Experiments 1 to 3, the occurrence rate of coating failure is reduced by repeating the retention treatment for an appropriate time at an appropriate temperature in the heating process of primary recrystallization annealing (decarburization annealing). The reason is not clear enough, but I think as follows.
In the decarburization annealing process of the grain-oriented electrical steel sheet, an internal oxide layer containing firelite (Fe ₂ SiO ₄ ) and SiO ₂ is formed simultaneously with the formation of the primary recrystallization texture. In the heating process, which is the initial stage, nuclei that serve as the starting point for the growth of the internal oxide layer are generated and grown to form an initial oxide film mainly composed of SiO ₂ , and then further grown on the internal oxide layer. Go.

  Here, the rapid heating of the heating process shortens the time for generating the nuclei of the internal oxide layer, so that it is difficult to form a uniform film in the subsequent film growth process. However, by repeating the holding treatment in the middle of the rapid heating, nuclei of the internal oxide layer are sufficiently generated, so that a uniform internal oxide layer is formed. As a result, the product plate coating (forsterite coating) that inherits the structure of the internal oxide layer is also uniform and free of defects.

で定義される被膜成分密度ａを求めたときに、上記被膜成分密度ａが０．８０〜０．９７の間における、下記（２）式；

で定義される上記被膜成分密度ａの深さ方向の傾きの平均値ｂは８μｍ^−１以上の値となる。そして、上記被膜成分密度ａの傾きｂが８μｍ^−１以上の被膜は、被膜欠陥のない被膜品質に優れたものとなる。 In addition, the product plate obtained by the above-described annealing method has a light emission intensity (I _Si , I _Mg , I _{O and} I _Fe ) of Si, Mg, O and Fe in the depth direction obtained by analyzing the steel plate surface by GDS. From the following formula (1);

When the film component density a defined by the formula (2) is obtained, the following formula (2) when the film component density a is between 0.80 and 0.97;

The average value “b” of the gradient in the depth direction of the film component density “a” defined in the above is a value of 8 μm ⁻¹ or more. And the film whose inclination b of the said film | membrane component density a is 8 micrometers- ¹ or more becomes the thing excellent in the film quality without a film defect.

The inventors consider the reason as follows.
First, as can be understood from the equation (1), the coating component density a can be considered as the concentration of coating components Si, Mg, O in the coating (in other words, Fe concentration in the coating). In addition, the slope (da / dz) of the a in the region where the film component density a is 0.80 to 0.97 (the region where Fe is 0.03 to 0.20) is the Fe from the layer not containing Fe. It can be considered as the gradient of the coating component density a in the initial region shifted to the containing layer, that is, the initial region shifted from the glassy insulating coating on the steel sheet surface to the ceramic base coating (forsterite coating). The reason why the average value is used to represent the inclination is that there is a large variation in the inclination of the film component density during this period.

The slope b of the coating component density a has a strong correlation with the uniformity (flatness) of the interface between the base coating and the base iron because it reflects the base iron component that has entered the base coating region. It means that the larger the gradient b of the coating component density a, the less likely the coating defects are generated. Therefore, in this invention, based on the result of the said experiments 1-3, the inclination b of the film | membrane component density a is prescribed | regulated as 8 micrometers- ¹ or more. However, when the slope b of the coating component density a increases beyond 300 μm ⁻¹ , the change from the forsterite coating to the ground iron occurs at a short distance, that is, the interface between the forsterite coating and the ground iron is flattened, Since there is no mechanical catch, film adhesion is significantly reduced. Therefore, it is desirable that the upper limit of the gradient b of the film component density a is about 300 μm ⁻¹ . Preferably it is the range of 12-200 micrometers- ¹ , More preferably, it is the range of 15-100 micrometers- ¹ .

Next, the manufacturing method of the grain-oriented electrical steel sheet of this invention is demonstrated.
The grain-oriented electrical steel sheet of the present invention needs to have a ceramic base coating and a glassy insulating coating on the surface of the steel plate, and the manufacturing method is performed by heating a steel material having a predetermined component composition. Hot-rolled sheet by hot rolling, and after hot-rolled sheet annealing or after hot-rolled sheet annealing, cold-rolled sheet with final thickness by one or more cold rolling sandwiching intermediate annealing Apply primary recrystallization annealing that also serves as primary recrystallization annealing or decarburization annealing, apply an annealing separator on the steel sheet surface, dry it and wind it on a coil, then subject it to finish annealing, and then an insulating coating on the steel sheet surface It consists of a series of processes for forming the film.
Here, conventionally well-known manufacturing conditions can be employ | adopted about manufacturing conditions other than after the component composition of the said steel raw material, and primary recrystallization annealing (decarburization annealing), and there is no restriction | limiting in particular. Therefore, the component composition of the steel material and the conditions after the primary recrystallization annealing (decarburization annealing) will be described below.

First, it is preferable that the steel raw material (slab) used as the raw material of the grain-oriented electrical steel sheet of the present invention has the following component composition.
C: 0.002-0.10 mass%
If C is less than 0.002 mass%, the grain boundary strengthening ability is lost, and the slab is cracked, which causes problems in production. On the other hand, if it exceeds 0.10 mass%, it will be difficult to reduce it to 0.005 mass% or less at which magnetic aging does not occur by decarburization annealing in a later step. Therefore, the C content is in the range of 0.002 to 0.10 mass%. Preferably it is the range of 0.010-0.080 mass%.

Si: 2.0 to 8.0 mass%
Si is an element necessary for increasing the specific resistance of steel and reducing iron loss. If the effect is less than 2.0 mass%, it is not sufficient. On the other hand, if it exceeds 8.0 mass%, the workability is lowered and it is difficult to roll and manufacture. Therefore, Si is set to a range of 2.0 to 8.0 mass%. Preferably it is the range of 2.5-4.5 mass%.

Mn: 0.005 to 1.0 mass%
Mn is an element necessary for improving the hot workability of steel. If the effect is less than 0.005 mass%, it is not sufficient. On the other hand, if it exceeds 1.0 mass%, the magnetic flux density of the product plate is lowered. Therefore, Mn is set to a range of 0.005 to 1.0 mass%. Preferably it is the range of 0.02-0.20 mass%.

Components other than C, Si and Mn are classified into cases where an inhibitor is used and cases where no inhibitor is used in order to cause secondary recrystallization.
First, when an inhibitor is used to cause secondary recrystallization, for example, when an AlN-based inhibitor is used, Al and N are changed to Al: 0.010 to 0.050 mass%, N: 0.0. It is preferable to make it contain in the range of 003-0.020 mass%. When using an MnS / MnSe-based inhibitor, the amount of Mn described above and one or two of S: 0.002-0.030 mass% and Se: 0.003-0.030 mass% are contained. It is preferable to make it. If the addition amount is less than the above lower limit value, the inhibitory effect of the inhibitor cannot be sufficiently obtained. On the other hand, if the addition amount exceeds the upper limit value, the inhibitor component remains in an insoluble state during slab heating, and secondary recrystallization occurs. Defects are caused and magnetic properties are deteriorated. AlN and MnS / MnSe inhibitors may be used in combination.

  On the other hand, when an inhibitor is not used to cause secondary recrystallization, the content of Al, N, S and Se, which are the above-described inhibitor forming components, is reduced as much as possible, Al: less than 0.01 mass%, N : It is preferable to use a steel material reduced to less than 0.0050 mass%, S: less than 0.0050 mass%, and Se: less than 0.0030 mass%.

  In addition, the remainder other than the said component of the steel raw material (slab) used for this invention is Fe and an unavoidable impurity. However, for the purpose of improving magnetic properties, Ni: 0.001 to 0.015 mass%, Sb: 0.005 to 0.50 mass%, Sn: 0.005 to 0.50 mass%, Bi: 0.005 to 0 .50 mass%, Mo: 0.005-0.10 mass%, B: 0.0002-0.0025 mass%, Te: 0.0005-0.010 mass%, Nb: 0.0010-0.010 mass%, V: You may contain suitably 1 type (s) or 2 or more types chosen from 0.001-0.010mass% and Ta: 0.001-0.010mass%.

Next, the primary recrystallization annealing conditions in the manufacturing method of the grain-oriented electrical steel sheet according to the present invention will be described.
In the primary recrystallization annealing that also serves as primary recrystallization annealing or decarburization annealing in the present invention, it is necessary to set the temperature rising rate in the heating process to 50 ° C./s or more. By the above rapid heating, the ratio of Goss orientation in the primary recrystallization texture can be increased, and the number of Goss grains after secondary recrystallization can be increased to reduce the average grain size. Can be improved. However, if the heating rate becomes too fast, the amount of {lll} structure phagocytosed in the Goss orientation {110} <001> decreases and secondary recrystallization failure tends to occur. It is preferable to set it as about deg. A preferable temperature increase rate is in the range of 50 to 700 ° C./s.

  Moreover, the temperature range which performs rapid heating by primary recrystallization annealing shall be between 100-700 degreeC. Since the temperature at which the steel sheet reaches the annealing furnace varies depending on the outside air temperature, the processing temperature in the previous process, the conveying time of the steel sheet, and the like, control from 100 ° C. becomes easy. On the other hand, even if the temperature at which rapid heating is terminated exceeds 700 ° C. at which primary recrystallization starts, the effect of rapid heating is saturated and energy required for rapid heating only increases, which is not preferable.

  Moreover, in the heating process of the primary recrystallization annealing, it is necessary to repeat the holding treatment for 0.5 to 10 seconds at any temperature between 250 to 600 ° C. during the rapid heating 2 to 6 times. is there. When the holding temperature is less than 250 ° C. or the holding time is less than 0.5 seconds, the effect of the holding treatment is small. On the other hand, when the holding temperature exceeds 600 ° C. or the holding time exceeds 10 seconds, the rolling structure covers a wide range. This is because the recovery proceeds and the structure after annealing becomes a recovered structure that has not been recrystallized. In addition, preferable holding temperature is the range of 300-550 degreeC, and preferable holding time is the range of 0.5-5.0 second.

  Moreover, the reason for setting the number of times of the retaining process to 2 to 6 is that the effect of reducing the <111> // ND orientation is insufficient with only one time, and the effect of improving the iron loss characteristic is small. This is because the recovery proceeds over a wide range of the rolled structure, and the structure after annealing becomes a non-recrystallized recovered structure. In addition, by setting the number of times of the retention treatment to 2 to 6, the core of the internal oxide layer is finely precipitated and the internal oxide layer is uniformly formed, so that the film characteristics are improved. The preferable number of times of holding treatment is in the range of 2 to 5 times.

  In addition, the decarburization annealing in the primary recrystallization annealing is not necessarily performed in combination with the primary recrystallization annealing, and may be performed separately, but when performing the decarburization annealing before the primary recrystallization annealing, It is necessary to perform rapid heating by decarburization annealing. Moreover, when performing decarburization annealing, it is preferable to implement so that C in a steel plate may be less than 0.0050 mass%. Therefore, it is not necessarily performed when C of the steel material (slab) is less than 0.0050 mass%.

  Next, the annealing separator applied to the steel sheet surface after the primary recrystallization annealing and before the finish annealing is mainly composed of MgO or MgO in order to form a ceramic film such as forsterite. It is preferable to use the contained annealing separator.

  The steel sheet with the annealing separator applied to the steel sheet surface is then wound into a coil and then subjected to finish annealing to develop a secondary recrystallized structure highly accumulated in the Goss orientation and a forsterite coating (undercoat) To form. In the above finish annealing, it is preferable to heat to a temperature of 800 ° C. or higher in order to develop secondary recrystallization and to a temperature of 1100 ° C. to complete the secondary recrystallization. Furthermore, in order to form a forsterite film and perform a purification treatment, it is preferable to continue heating to a temperature of about 1200 ° C.

  It is effective in reducing the iron loss that the steel plate after the above-mentioned finish annealing is subjected to planarization annealing for shape correction after removing the unreacted annealing separator adhering to the steel plate surface. At this time, it is necessary to deposit an insulating coating on the surface of the steel sheet simultaneously with the above-described planarization annealing, or before or after that. It is preferable to apply a glassy tension-imparting film having a great effect of imparting tension to the steel sheet and reducing iron loss. Specifically, it is preferable to use a silicic acid-based glass film or the like. In addition, in the formation of the above tension-imparting coating, if a method of applying a tension coating through a binder or a method of forming an inorganic coating on the steel sheet surface by physical vapor deposition or chemical vapor deposition is employed, the coating adhesion is further improved. An insulating film that is excellent and has a large iron loss reduction effect can be formed.

  Moreover, in order to further reduce the iron loss of the grain-oriented electrical steel sheet of the present invention, it is preferable to perform a magnetic domain refinement process. As a processing method, generally used is a method of forming a groove in a final product plate, or introducing thermal strain or impact strain in a linear or dotted manner by electron beam irradiation, laser irradiation, or plasma irradiation, and finally. In an intermediate process after cold rolling to a plate thickness, a method of forming a groove by etching the steel plate surface can be used.

No. 1 having the component composition shown in Table 4 with the balance being Fe and inevitable impurities. 1 to 17 steel was melted and made into a steel slab by a continuous casting method, then reheated to 1380 ° C., hot-rolled to form a hot-rolled sheet having a thickness of 2.0 mm, and a heat of 1030 ° C. × 10 seconds. After performing the sheet annealing, the sheet was cold-rolled to obtain a cold-rolled sheet having a final sheet thickness of 0.27 mm.
Next, primary recrystallization annealing was performed in a wet atmosphere of 50 vol% H ₂ -50 vol% N ₂ , which also served as decarburization annealing at 840 ° C. for 60 seconds. In addition, the heating of the said primary recrystallization annealing raises between 100-700 degreeC with the temperature increase rate of 75 degreeC / s, and hold | maintenance process hold | maintained at 450 degreeC and 500 degreeC in the middle of heating at this time for 2 second, respectively. Thereafter, the temperature was increased from 700 ° C. to 840 ° C. at 75 ° C./s.
Next, an annealing separator mainly composed of MgO is applied to the surface of the steel sheet and dried, and then wound around a coil, followed by secondary recrystallization annealing and finishing annealing consisting of 1220 ° C. × 7 hours of purification annealing in a hydrogen atmosphere. gave. The atmosphere of the finish annealing was H ₂ gas at the time of 1220 ° C. for purification, Ar gas at the time of temperature rise (including secondary recrystallization annealing) and at the time of temperature fall. Then, the product coil was obtained by performing flattening annealing for forming a tension-imparting coating. At that time, the surface of the steel sheet was visually observed over the entire length of the coil, the length of the point-like film defect occurrence was measured, and the occurrence rate of the point-like defect was obtained.

Ten test pieces each having a width of 100 mm and a length of 500 mm were collected from the product coil thus obtained in the plate width direction of the steel sheet, and the iron loss W _17/50 was measured by the method described in JIS C2556. The average value of the measured values of the sheets was obtained.
Furthermore, a linear groove is provided on the surface of the above-mentioned test piece where the iron loss has been measured in a direction perpendicular to the rolling direction and parallel to the plate width direction, or an electron beam is applied to impart thermal strain. After _{performing the} magnetic domain fragmentation treatment, the iron loss W _17/50 was measured again, and the average value was obtained.

で定義される被膜成分密度ａを求め、上記ａが０．８０〜０．９７の間における、下記（２）式；

で定義される被膜成分密度ａの深さ方向の傾きの平均値ｂを求めた。 Further, the surface of the test piece collected from each product coil is analyzed for the concentration distribution of Si, Mg, O and Fe in the depth direction by glow discharge emission spectroscopy (GDS), and the obtained Si, Mg , O and Fe from the emission intensities (I _Si , I _Mg , I _{O and} I _Fe ), the following formula (1):

The film component density a defined by ## EQU2 ## is obtained, and the above a is between 0.80 and 0.97.

The average value b of the gradient in the depth direction of the film component density a defined by

Table 4 also shows the measurement results of the incidence rate of the point defects, the iron loss W _17/50, and the slope b of the coating component density a. From now on, the grain-oriented electrical steel sheet manufactured by performing the retaining treatment under the conditions suitable for the present invention using the steel material having the component composition suitable for the present invention is excellent in the iron loss characteristics and the film quality. I understand that. Moreover, it was also confirmed that the iron loss characteristics of the grain-oriented electrical steel sheet of the present invention are further improved by performing the magnetic domain refinement treatment.

Claims (7)

C: 0.005 mass% or less, Si: 2.0-8.0 mass% and Mn: 0.005-1.0 mass%, with the balance being composed of Fe and unavoidable impurities, steel plate surface In a grain-oriented electrical steel sheet having a ceramic base coating and a glass insulating coating on
The surface of the steel sheet was analyzed by glow discharge optical emission spectrometry, and the obtained luminescence intensity in the depth direction (z direction) of each element of Si, Mg, O and Fe was obtained by I _Si , I _Mg , I _O and I, respectively. _{When Fe} is defined as the film component density from the above emission intensity using the following formula (1) as the film component density, the following formula (2) in the region where the film component density a is 0.80 to 0.97: A grain ^- oriented electrical steel sheet, characterized in that the average value b of the slope in the depth direction of the film component density a is 8 μm ⁻¹ or more and 300 μm ⁻¹ or less.
Record

In addition to the above component composition, Ni: 0.001 to 0.015 mass%, Sb: 0.005 to 0.50 mass%, Sn: 0.005 to 0.50 mass%, Bi: 0.005 to 0.50 mass %, Mo: 0.005-0.10 mass%, B: 0.0002-0.0025 mass%, Te: 0.0005-0.010 mass%, Nb: 0.0010-0.010 mass%, V: 0.00. The grain-oriented electrical steel sheet according to claim 1, comprising one or more selected from 001 to 0.010 mass% and Ta: 0.001 to 0.010 mass%. 3. The grain-oriented electrical steel sheet according to claim 1, wherein an average value “b” in the depth direction of the coating component density “a” is in a range of 12 to 200. 4. The steel plate surface has a groove in a direction intersecting with the rolling direction, or has thermal strain or impact strain due to electron beam irradiation or laser irradiation continuously or intermittently. The grain-oriented electrical steel sheet according to claim 1. It is a manufacturing method of the grain-oriented electrical steel sheet according to claim 1,
C: 0.002 to 0.10 mass%, Si: 2.0 to 8.0 mass%, Mn: 0.005 to 1.0 mass%, and further, Al and N are added as an inhibitor forming component, respectively. : 0.010 to 0.050 mass%, N: 0.003 to 0.020 mass%, and / or S: 0.002 to 0.030 mass% and Se: 0.003 to 0.030 mass % Or hot-rolled steel material comprising a component composition consisting of Fe and unavoidable impurities, and without subjecting to hot-rolled sheet annealing or After the hot-rolled sheet annealing, the cold-rolled sheet with the final sheet thickness is formed by cold rolling at least once with intermediate or intermediate annealing, and the primary recrystallization annealing to form the internal oxide layer is applied to the steel sheet surface. After winding into a coil by applying and drying a blunt separating agent, subjected to finish annealing, then, in the manufacturing method of a grain-oriented electrical steel sheet consisting of a series of steps of HiNaru insulating coatings on the surface of the steel sheet,
While rapidly heating the section of 100 to 700 ° C. in the heating process of the primary recrystallization annealing at a heating rate of 50 ° C./s or more,
Method for producing oriented electrical steel sheets towards you and performing repeated 2-6 times the retention process of holding 0.5 to 10 seconds at any temperature between the heating during the 250 to 600 ° C.. It is a manufacturing method of the grain-oriented electrical steel sheet according to claim 1,
C: 0.002 to 0.10 mass%, Si: 2.0 to 8.0 mass%, Mn: 0.005 to 1.0 mass%, Al: less than 0.01 mass%, N: 0.00. It is reduced to less than 0050 mass%, S: less than 0.0050 mass%, and Se: less than 0.0030 mass%, and the steel material consisting of the component composition consisting of Fe and inevitable impurities is hot-rolled to form a hot-rolled sheet First, after the hot-rolled sheet annealing is performed or after the hot-rolled sheet annealing is performed, the final thickness of the cold-rolled sheet is formed by cold rolling at least once with the intermediate annealing interposed therebetween, and an internal oxide layer is formed. A grain-oriented electrical steel sheet consisting of a series of steps in which recrystallization annealing is performed, an annealing separator is applied to the steel sheet surface, dried and wound on a coil, then subjected to finish annealing, and then an insulating film is formed on the steel sheet surface. Manufacturing of In law,
While rapidly heating the section of 100 to 700 ° C. in the heating process of the primary recrystallization annealing at a heating rate of 50 ° C./s or more,
Method for producing oriented electrical steel sheets towards you and performing repeated 2-6 times the retention process of holding 0.5 to 10 seconds at any temperature between the heating during the 250 to 600 ° C.. In addition to the above component composition, the steel material further includes Ni: 0.001 to 0.015 mass%, Sb: 0.005 to 0.50 mass%, Sn: 0.005 to 0.50 mass%, Bi: 0.00. 005 to 0.50 mass%, Mo: 0.005 to 0.10 mass%, B: 0.0002 to 0.0025 mass%, Te: 0.0005 to 0.010 mass%, Nb: 0.0010 to 0.010 mass% The direction of Claim 5 or 6 containing 1 type, or 2 or more types chosen from V: 0.001-0.010mass% and Ta: 0.001-0.010mass%. Method for producing an electrical steel sheet.

Images