Grain-oriented electrical steel sheet

Abstract

This grain-oriented electrical steel sheet has a magnetic flux density B8 of 1.940 T or more in the rolling direction, an iron loss W17 / 50 of 0.670 W / kg or less, and a magnetostriction velocity level Lva200@1.7T of 46.0 dB or less.

Description

grain-oriented electrical steel sheet

[0001] This application claims priority to Japanese Patent Application No. 2023-106861, filed on June 29, 2023, the contents of which are incorporated herein by reference.

[0002] Grain-oriented electrical steel sheets contain silicon, and the crystal orientation of the silicon grains is concentrated near the Goss orientation (cubic {110}<001>), with the <001> orientation, which is the axis of easy magnetization, being nearly aligned with the rolling direction during the steel sheet manufacturing process. Such grain-oriented electrical steel sheets are excellent materials for transformer cores, etc. Important magnetic properties of grain-oriented electrical steel sheets include magnetic flux density, core loss, and noise characteristics.

[0003] The magnetic flux density of a grain-oriented electrical steel sheet when a predetermined magnetizing force is applied tends to increase as the degree to which the magnetization easy axis of the crystal grains is aligned in the rolling direction of the steel sheet, i.e., the orientation of the crystal orientation, increases. ８ is used. Magnetic flux density B ８ is the value of the magnetic flux density of the magnetized grain-oriented electrical steel sheet when a magnetizing force of 800 A / m is applied in the rolling direction. That is, the magnetic flux density B ８ The larger the value of σ, the easier it is to magnetize with a certain magnetizing force and the greater the magnetic flux density, making it suitable for small, highly efficient transformers.

[0004] In addition, iron loss W is generally used as an index to represent iron loss. １７／５０ is used. Iron loss W １７／５０ is the iron loss when the grain-oriented electrical steel sheet is excited by AC under the conditions of a maximum magnetic flux density of 1.7 T and a frequency of 50 Hz. １７／５０ The smaller the value of grain-oriented electrical steel sheet, the lower the energy loss and the more suitable it is for transformers.

[0005] In addition, the magnetostrictive velocity level (Lva) is used as an index representing noise characteristics. The magnetostrictive velocity level (Lva) is a value obtained by time-differentiating the magnetostrictive waveform during AC excitation, converting it into velocity, and applying A-weighting audibility correction, which is the frequency characteristic of human hearing. The characteristics of sound that humans can perceive are not necessarily constant at all frequencies and can be expressed by an audible characteristic called A-weighting. An actual magnetostrictive waveform is not a sine wave but a waveform in which various frequency components overlap. Therefore, by Fourier transforming the magnetostrictive waveform, determining the amplitude for each frequency, and multiplying it by A-weighting, it is possible to obtain the magnetostrictive velocity level (Lva), which is an index close to the actual human audible characteristic. Reducing this magnetostrictive velocity level (Lva) can suppress iron core vibrations caused by frequencies perceived by humans in transformer noise, thereby effectively reducing transformer noise.

[0006] Regarding the above-mentioned magnetic properties, for example, Patent Documents 1 and 2 disclose a method of increasing magnetic flux density by promoting secondary recrystallization while applying a temperature gradient to a steel sheet. Patent Document 3 discloses a method of reducing iron loss by applying strain to a steel sheet through scanning irradiation with an extremely focused laser beam. Patent Document 4 discloses a method of reducing iron loss by forming multiple grooves on the surface of a steel sheet.

[0007] Japanese Patent Publication No. 57-002839 Japanese Patent Publication No. 61-190017 International Publication No. 2004 / 083465 International Publication No. 2016 / 171129

[0008] As mentioned above, attempts have been made to improve the magnetic properties of grain-oriented electrical steel sheets, but it has been difficult to simultaneously improve all of the magnetic flux density, iron loss, and noise characteristics using conventional techniques.

[0009] For example, the techniques of Patent Documents 1 and 2 increase magnetic flux density, but because secondary recrystallized grains grow coarse, iron loss characteristics are poor unless magnetic domain control technology is applied. Furthermore, the technique of Patent Document 3 reduces iron loss, but noise characteristics are degraded because strain necessary for iron loss reduction is introduced into the steel sheet. Furthermore, the technique of Patent Document 4 reduces iron loss, but magnetic flux density is reduced because grooves of a depth necessary for iron loss reduction are formed in the steel sheet.

[0010] The present invention has been made in view of the above-mentioned problems. An object of the present invention is to provide a grain-oriented electrical steel sheet that is excellent in all of magnetic flux density, iron loss, and noise characteristics. Specifically, an object of the present invention is to provide a grain-oriented electrical steel sheet that is excellent in all of magnetic flux density, iron loss, and noise characteristics even when magnetic domain control technology is applied.

[0011] That is, the gist of the present invention is as follows.

[0012] [1] A grain-oriented electrical steel sheet according to one aspect of the present invention is a grain-oriented electrical steel sheet having a base steel sheet and an insulating coating and having a controlled magnetic domain, wherein the magnetic flux density in the rolling direction when excited at 800 A / m is expressed as B in units of T. ８ The iron loss when excited to a magnetic flux density of 1.7 T at a frequency of 50 Hz is defined as W / kg. １７／５０ When the magnetostriction rate level calculated from the magnetostriction amount of the 200 Hz component of the magnetostriction waveform when excited to a magnetic flux density of 1.7 T at a frequency of 50 Hz is defined as Lva200@1.7 T in dB, ８ But B ８ ≧1.940, １７／５０ But, W １７／５０ ≦0.670, and the Lva200@1.7T satisfies ΔLva200@1.7T≦46.0.

[0013] According to the above aspects of the present invention, it is possible to provide a grain-oriented electrical steel sheet that is excellent in all of magnetic flux density, iron loss, and noise characteristics. Specifically, it is possible to provide a grain-oriented electrical steel sheet that is excellent in all of magnetic flux density, iron loss, and noise characteristics even when magnetic domain control technology is applied.

[0014] 1 is a diagram showing an example of spot current heating as a local rapid heating method, and is a schematic diagram showing an example of the arrangement of local heat affected zones in a decarburization annealed steel sheet. FIG. 2 is a schematic diagram showing the distribution of Goss oriented grains in a decarburization annealed steel sheet.

[0015] A preferred embodiment of the present invention will be described in detail. However, the present invention is not limited to the configuration disclosed in this embodiment, and various modifications are possible within the scope of the present invention. Furthermore, the numerical ranges described below include the lower and upper limits. Numerical values ​​indicated as "greater than" or "less than" are not included in the numerical range. Furthermore, "%" in relation to chemical composition means "mass %" unless otherwise specified.

[0016] The grain-oriented electrical steel sheet according to this embodiment is a grain-oriented electrical steel sheet with controlled magnetic domains, and has a base steel sheet and an insulating coating. The magnetic flux density in the rolling direction when excited at 800 A / m is expressed as B in units of T. ８ The iron loss when excited to a magnetic flux density of 1.7 T at a frequency of 50 Hz is defined as W / kg. １７／５０ When the magnetostriction rate level calculated from the magnetostriction amount of the 200 Hz component of the magnetostriction waveform when excited to a magnetic flux density of 1.7 T at a frequency of 50 Hz is defined as Lva200@1.7 T in dB, ８ But B ８ ≧1.940, and １７／５０ But, W １７／５０ ≦0.670, and the above ΔLva200@1.7T satisfies Lva200@1.7T≦46.0.

[0017] In this embodiment, the deviation between the crystal orientation of the secondary recrystallized grains and the ideal Goss orientation is controlled to be extremely small, and the secondary recrystallized grains are prevented from growing coarsely. Therefore, even if magnetic domain control technology is applied, the energy density of the laser irradiation can be reduced compared to the conventional technology, and the depth of the grooves formed can be made shallower. As a result, the deterioration of noise characteristics due to distortion caused by laser irradiation and the magnetic flux density B due to the formation of grooves can be reduced. ８ Therefore, the grain-oriented electrical steel sheet according to this embodiment is excellent in all of magnetic flux density, iron loss, and noise characteristics (particularly, magnetostriction rate level in a medium magnetic field).

[0018] As mentioned above, when applying magnetic domain control technology to grain-oriented electrical steel sheets of the prior art, in order to achieve the magnetic domain refining effect, the energy density of the laser irradiation had to be increased to a certain extent, and the grooves formed had to be deeper to a certain extent. As a result, even if magnetic domain refining improved the iron loss characteristics, it was impossible to avoid a decrease in magnetic flux density and an increase in noise. In other words, it was difficult for grain-oriented electrical steel sheets of the prior art to simultaneously improve all of the magnetic flux density, iron loss, and noise characteristics.

[0019] In this embodiment, multiple coarse Goss-oriented grains close to the ideal Goss orientation are formed before secondary recrystallization, and these coarse Goss-oriented grains grow preferentially during secondary recrystallization. The preferentially grown coarse Goss-oriented grains collide with each other to terminate secondary recrystallization. Therefore, in the grain-oriented electrical steel sheet according to this embodiment, the crystal orientation of the secondary recrystallized grains is close to the ideal Goss orientation, and the secondary recrystallized grains are fine. The method for manufacturing the grain-oriented electrical steel sheet according to this embodiment will be described later.

[0020] The grain-oriented electrical steel sheet according to this embodiment has a magnetic flux density B ８ The magnetic flux density B is 1.940 T or more. ８ When the magnetic flux density B is 1.940 T or more, it can be determined that the magnetic flux density is good. ８ is preferably 1.950 T or more, more preferably 1.960 T or more, more preferably 1.970 T or more, more preferably 1.980 T or more, and even more preferably 1.990 T or more. On the other hand, when used as a wound core, the magnetic flux density B ８ The larger the value, the better, so there is no particular upper limit. For example, ８ It is sufficient that the value is 2.00T or less, or 1.99T or less.

[0021] In addition, the grain-oriented electrical steel sheet according to this embodiment has an iron loss W １７／５０ is 0.670 W / kg or less. １７／５０ The value of changes depending on the thickness t of the base steel plate. When the thickness t of the base steel plate becomes thinner, the iron loss W １７／５０However, in the grain-oriented electrical steel sheet according to this embodiment, the iron loss W １７／５０ is 0.670 W / kg or less. １７／５０ is preferably 0.650 W / kg or less, and more preferably 0.600 W / kg or less. １７／５０ The smaller the value, the better, and there is no particular lower limit. ８ If the steel sheet is irradiated with laser light to the extent that the iron loss reduction effect becomes saturated with respect to the value of , the magnetostriction velocity level Lva (particularly the magnetostriction velocity level of the 200 Hz component) that affects the noise characteristics of the transformer increases, resulting in a deterioration of the noise characteristics. Therefore, the iron loss value in the range where the above-mentioned Lva200@1.7T satisfies 46.0 dB or less is the iron loss W １７／５０ For example, the iron loss W １７／５０ The lower limit may be set to 0.500 W / kg.

[0022] Furthermore, the grain-oriented electrical steel sheet according to this embodiment has a Lva200@1.7T of 46.0 dB or less. ８ However, in the grain-oriented electrical steel sheet according to this embodiment, the value changes depending on the magnetic flux density B ８ However, it is sufficient that Lva200@1.7T is 46.0 dB or less. When Lva200@1.7T is 46.0 dB or less, it can be determined that the noise characteristics are good. Lva200@1.7T is preferably 45.0 dB or less, and more preferably 40.0 dB or less. On the other hand, the smaller the value of Lva200@1.7T, the more preferable it is, and there is no particular limit on the lower limit. For example, the lower limit of Lva200@1.7T may be 34.0 dB.

[0023] The magnetic properties of the grain-oriented electrical steel sheet may be measured based on the Single Sheet Tester (SST) method specified in JIS C 2556:2015. For example, 20 samples for single sheet magnetic measurement, each measuring 100 mm x 500 mm, are prepared from the grain-oriented electrical steel sheet, and the single sheet magnetic properties are measured. ８ The iron loss W can be calculated as the magnetic flux density in the rolling direction of the steel sheet when excited with 800 A / m.１７／５０ can be obtained as iron loss, which is defined as the power loss per unit weight (1 kg) of the steel sheet under the conditions of an AC frequency of 50 Hz and an excitation magnetic flux density of 1.7 T.

[0024] Furthermore, as the magnetic properties, the magnetostriction λp-p@1.7 T generated in the steel sheet may be measured under the conditions of an AC frequency of 50 Hz and an excitation magnetic flux density of 1.7 T. Specifically, the maximum length L of the test piece (steel sheet) under the above excitation conditions ｍａｘ and the minimum length L ｍｉｎ , and the length L of the test piece at magnetic flux density 0 T ０ Using this, λp-p@1.7T=(L ｍａｘ -L ｍｉｎ ) ÷ L ０ It can be calculated as follows.

[0025] Based on the magnetostriction characteristics described above, the magnetostriction rate level Lva200@1.7 T can be calculated. The magnetostriction rate level can be derived using the following formula 1 by performing a Fourier transform on a magnetostriction waveform of two or more periods acquired at a sampling frequency of 6.4 kHz, and using the magnetostriction amount λ(fi) (0 Hz to 3.2 kHz) obtained for each frequency. In this embodiment, Lva200@1.7 T can be calculated with the frequency fi set to 200 Hz.

[0026] Lva = 20 × log １０ [{ρc×{Σ(2 １／２ π×fi×λ(fi)×α(fi)) ２} １／２} / P ０ ] ...(Formula 1)

[0027] Where, ρ: air density (kg / m ３ ) c: Speed ​​of sound (m / sec) P ０ : The minimum pressure (Pa) at which a 1 kHz sound can be heard by humans. fi: Frequency (Hz) λ(fi): Magnetostriction amount for each frequency obtained by Fourier transformation α(fi): A-weighting of frequency fi π: Circular constant

[0028] To calculate Lva200@1.7T, the following value should be substituted: ρ = 1.185 (kg / m ３ ) c=346.3 (m / sec) P ０= 2 x 10 －５ (Pa) fi = 200 (Hz) α(fi): Values ​​listed in Table 2 of JIS C 1509-1 (2005)

[0029] The grain-oriented electrical steel sheet according to this embodiment is basically premised on the application of magnetic domain control technology to reduce iron loss. As described above, when magnetic domain control technology that applies distortion by laser irradiation or the like is implemented, the noise characteristics of the transformer are deteriorated. However, in this embodiment, the magnetic flux density B ８ Because the secondary recrystallized grain size can be made smaller than in conventional materials with the same properties, the iron loss reduction effect can be achieved even if the amount of strain applied for magnetic domain refinement is reduced. In other words, compared to steel sheets in which iron loss is reduced using conventional magnetic domain control technology alone, noise characteristics can be significantly improved while maintaining iron loss characteristics at the same level or higher.

[0030] The improvement effect can be evaluated by evaluating the harmonic magnetostriction characteristics as described above. Specifically, when excited at a frequency f=50 Hz, the improvement effect can be evaluated as the amount of change in the 4f=200 Hz component, which is four times the magnetization frequency.

[0031] The grain-oriented electrical steel sheet according to this embodiment may have the following chemical composition.

[0032] The grain-oriented electrical steel sheet according to this embodiment may contain, as a chemical composition, 2.0% to 7.0% Si by mass fraction, with the remainder being Fe and impurities.

[0033] Furthermore, this grain-oriented electrical steel sheet may contain known optional elements in place of a portion of Fe for the purpose of improving magnetic properties. There is no need to set a lower limit for the optional elements, and the lower limit may be 0%. Furthermore, the upper limit for the optional elements may be set within a range in which a significant decrease in magnetic flux density or iron loss does not occur. The upper limit values ​​serving as a guide for each optional element are listed below.

[0034] Specifically, the grain-oriented electrical steel sheet (base steel sheet) according to this embodiment has a chemical composition, in mass %, of Si: 2.0 to 7.0%, C: 0 to 0.0050%, Mn: 0 to 1.0%, S and Se: 0 to 0.0150% in total, Al: 0 to 0.0650%, N: 0 to 0.0050%, Nb, V, Mo, Ta, and W: 0 to 0.050% in total, Cu: 0 to 0.40%, Bi: 0 to 0.010%, B: 0 to 0.080%, P: 0 to 0.50%, Ti: 0 to 0.0150%, Sn: 0 to 0.10%, Sb: 0 to 0.10%, Cr: 0 to 0.30%, Ni: 0 to 1.0%, and the remainder may be Fe and impurities.

[0035] Si: 2.0 to 7.0% Si (silicon) is a basic element for the base steel sheet. If the Si content is less than 2.0%, eddy current loss cannot be sufficiently reduced, and good magnetic properties cannot be obtained. Therefore, the Si content of the base steel sheet is set to 2.0% or more. The Si content is preferably 2.50% or more, and more preferably 3.0% or more. On the other hand, if the Si content exceeds 7.0%, the steel sheet becomes embrittled and threadability during production deteriorates significantly, so the Si content of the base steel sheet is set to 7.0% or less. The Si content is preferably 4.50% or less, and more preferably 4.0% or less.

[0036] C: 0 to 0.0050% C (carbon) is an optional element for the base steel sheet. C is contained in the steel billet (slab), but if excessive C remains in the base steel sheet after finish annealing, good iron loss characteristics may not be obtained. Therefore, the C content of the base steel sheet may be 0.0050% or less. The C content is preferably 0.0040% or less, more preferably 0.0030% or less. On the other hand, the lower limit of the C content of the base steel sheet is not particularly limited, and may be 0%. However, since it is not industrially easy to achieve a C content of 0%, the C content may be more than 0% or may be 0.00010% or more.

[0037] Mn: 0 to 1.0% Mn (manganese) is an optional element for the base steel sheet. Although Mn is contained in steel slabs, excessive Mn can cause phase transformation of the steel during secondary recrystallization annealing, preventing secondary recrystallization from progressing sufficiently and resulting in poor magnetic properties. Therefore, the Mn content of the base steel sheet may be 1.0% or less. The Mn content is preferably 0.50% or less, more preferably 0.20% or less. On the other hand, the lower limit of the Mn content of the base steel sheet is not particularly limited, and may be 0%. However, since Mn forms MnS and MnSe and acts as an inhibitor during secondary recrystallization, the Mn content may be greater than 0% or may be 0.00010% or more.

[0038] Sum of S and Se: 0 to 0.0150% S (sulfur) and Se (selenium) are optional elements for the base steel sheet. S and Se are contained in steel slabs, but if excessive S and Se remain in the base steel sheet after finish annealing, it may adversely affect the magnetic properties. Therefore, the total content of S and Se in the base steel sheet may be 0.0150% or less. The total content of S and Se is preferably 0.010% or less, more preferably 0.0050% or less. On the other hand, the lower limit of the total content of S and Se in the base steel sheet is not particularly limited and may be 0%. However, since S and Se form MnS and MnSe and have the effect of acting as inhibitors during secondary recrystallization, the total content of S and Se may be more than 0% or may be 0.00010% or more.

[0039] Al: 0 to 0.0650% Al (aluminum) is an optional element for the base steel sheet. Al is contained in steel slabs, but if excessive Al remains in the base steel sheet after finish annealing, it may adversely affect magnetic properties. Therefore, the Al content of the base steel sheet may be 0.0650% or less. The Al content is preferably 0.040% or less, more preferably 0.035% or less. On the other hand, the lower limit of the Al content of the base steel sheet is not particularly limited and may be 0%. However, since Al forms AlN and has the effect of acting as an inhibitor during secondary recrystallization, the Al content may be greater than 0% or may be 0.00010% or more. The above Al content is acid-soluble Al (sol. Al).

[0040] N: 0 to 0.0050% N (nitrogen) is an optional element for the base steel sheet. N is contained in the steel billet (slab), but if excessive N remains in the base steel sheet after finish annealing, it may adversely affect the magnetic properties. Therefore, the N content of the base steel sheet may be 0.0050% or less. The N content is preferably 0.0040% or less, more preferably 0.0030% or less. On the other hand, the lower limit of the N content of the base steel sheet is not particularly limited and may be 0%. However, since N forms AlN and has the effect of acting as an inhibitor during secondary recrystallization, the N content may be more than 0% or may be 0.00010% or more.

[0041] Total of Nb, V, Mo, Ta, and W: 0 to 0.050% Nb (niobium), V (vanadium), Mo (molybdenum), Ta (tantalum), and W (tungsten) are optional elements for the base steel sheet. If an excessive amount of Nb group elements (one or more of Nb, V, Mo, Ta, and W) remains in the base steel sheet, it may adversely affect the magnetic properties. Therefore, the total content of Nb, V, Mo, Ta, and W in the base steel sheet may be 0.050% or less. The Nb group elements are preferably 0.030% or less, preferably 0.020% or less, and more preferably 0.010% or less. On the other hand, the total content of Nb, V, Mo, Ta, and W in the base steel sheet is not particularly limited and may be 0%. However, since Nb, V, Mo, Ta, or W forms carbides, nitrides, or carbonitrides and has the effect of acting as an inhibitor during secondary recrystallization, the total content of Nb, V, Mo, Ta, and W may be more than 0% or may be 0.003% or more.

[0042] Cu: 0 to 0.40% Cu (copper) is an optional element for the base steel sheet. If the Cu content exceeds 0.40%, the steel sheet may become embrittled during hot rolling. Therefore, the Cu content of the base steel sheet may be 0.40% or less. The Cu content is preferably 0.30% or less, more preferably 0.10% or less. On the other hand, the lower limit of the Cu content is not particularly limited, and may be 0%. However, since Cu has the effect of increasing the concentration of Goss orientation and improving magnetic properties, the Cu content may be more than 0% or may be 0.010% or more.

[0043] Bi: 0 to 0.010% Bi (bismuth) is an optional element for the base steel sheet. If the Bi content exceeds 0.010%, coating adhesion may decrease. Furthermore, if purification during finish annealing is insufficient and excessive Bi remains, it may adversely affect magnetic properties. Therefore, the Bi content of the base steel sheet may be 0.010% or less. The Bi content is preferably 0.0050% or less, more preferably 0.0020% or less, and more preferably 0.0010% or less. On the other hand, the lower limit of the Bi content is not particularly limited and may be 0%. However, since Bi has the effect of improving magnetic flux density, the Bi content may be more than 0% or may be 0.00050% or more.

[0044] B: 0 to 0.080% B (boron) is an optional element for the base steel sheet. If the B content exceeds 0.080%, the variation (standard deviation) of magnetic flux density may become large. Therefore, the B content may be 0.080% or less. The Bi content is preferably 0.070% or less, more preferably 0.060% or less. On the other hand, the lower limit of the B content is not particularly limited, and may be 0%. However, since B forms nitrides and has the effect of acting as an inhibitor during secondary recrystallization, the B content may be more than 0% or may be 0.00050% or more.

[0045] P: 0 to 0.50% P (phosphorus) is an optional element for the base steel sheet. If the P content exceeds 0.50%, the workability of the steel sheet may be significantly reduced. Therefore, the P content of the base steel sheet may be 0.50% or less. The P content is preferably 0.30% or less, and more preferably 0.10% or less. On the other hand, the lower limit of the P content is not particularly limited, and may be 0%. However, since P has the effect of improving the texture and improving the magnetic properties of the steel sheet, the P content may be more than 0% or may be 0.0020% or more.

[0046] Ti: 0 to 0.0150% Ti (titanium) is an optional element for the base steel sheet. If the Ti content exceeds 0.0150%, the magnetic properties may deteriorate. Therefore, the Ti content of the base steel sheet may be 0.0150% or less. The Ti content is preferably 0.0130% or less, and more preferably 0.010% or less. On the other hand, the lower limit of the Ti content is not particularly limited, and may be 0%. However, since Ti forms carbides, nitrides, and carbonitrides and has the effect of acting as an inhibitor during secondary recrystallization, the Ti content may be more than 0% or may be 0.0020% or more.

[0047] Sn: 0 to 0.10% Sn (tin) is an optional element for the base steel sheet. If the Sn content exceeds 0.10%, secondary recrystallization becomes unstable, which may adversely affect the magnetic properties. Therefore, the Sn content of the base steel sheet may be 0.10% or less. The Sn content is preferably 0.090% or less, more preferably 0.080% or less. On the other hand, the lower limit of the Sn content is not particularly limited, and may be 0%. However, since Sn has the effect of increasing the concentration of Goss orientation and improving the magnetic properties, the Sn content may be more than 0% or may be 0.0050% or more.

[0048] Sb: 0 to 0.10% Sb (antimony) is an optional element for the base steel sheet. If the Sb content exceeds 0.10%, it may have an adverse effect on magnetic properties. Therefore, the Sb content of the base steel sheet may be 0.10% or less. The Sb content is preferably 0.090% or less, more preferably 0.080% or less. On the other hand, the lower limit of the Sb content is not particularly limited, and may be 0%. However, since Sb functions as an inhibitor and has the effect of stabilizing secondary recrystallization, the Sb content may be more than 0% or may be 0.010% or more.

[0049] Cr: 0 to 0.30% Cr (chromium) is an optional element for the base steel sheet. If the Cr content exceeds 0.30%, Cr oxides may be formed, which may adversely affect the magnetic properties. Therefore, the Cr content of the base steel sheet may be 0.30% or less. The Cr content is preferably 0.20% or less, and more preferably 0.10% or less. On the other hand, the lower limit of the Cr content is not particularly limited, and may be 0%. However, since Cr has the effect of increasing the concentration of Goss orientation and improving the magnetic properties, the Cr content may be more than 0% or may be 0.010% or more.

[0050] Ni: 0 to 1.0% Ni (nickel) is an optional element for the base steel sheet. If the Ni content exceeds 1.0%, secondary recrystallization may become unstable. Therefore, the Ni content of the base steel sheet may be 1.0% or less. The Ni content is preferably 0.20% or less, more preferably 0.10% or less. On the other hand, the lower limit of the Ni content is not particularly limited, and may be 0%. However, since Ni has the effect of increasing electrical resistance and reducing iron loss, the Ni content may be more than 0% or may be 0.010% or more.

[0051] The base steel sheet of the grain-oriented electrical steel sheet according to this embodiment may contain impurities. Here, "impurities" refer to substances that are mixed in from raw materials such as ore or scrap, or from the manufacturing environment, when steel is industrially produced.

[0052] The chemical composition of the base steel sheet may be measured by a common analytical method. For example, it may be measured using ICP-AES (Inductively Coupled Plasma-Atomic Emission Spectrometry). Acid-soluble Al may be measured by ICP-AES using the filtrate obtained by thermally decomposing a sample with acid. C and S may be measured using a combustion-infrared absorption method, N may be measured using an inert gas fusion-thermal conductivity method, and O may be measured using an inert gas fusion-non-dispersive infrared absorption method.

[0053] The above chemical composition is that of the base steel sheet. If the grain-oriented electrical steel sheet to be measured has an insulating coating on its surface, the coating is removed by the following method before measuring the chemical composition.

[0054] For example, the insulating coating can be removed by immersing the grain-oriented electrical steel sheet having the coating in a high-temperature alkaline solution. ２ O: The insulating coating can be removed from the grain-oriented electrical steel sheet by immersing the sheet in a 50 to 70 mass % aqueous sodium hydroxide solution at 80 to 90°C for 5 to 10 minutes, followed by rinsing with water and drying. The immersion time in the aqueous sodium hydroxide solution can be changed depending on the thickness of the insulating coating.

[0055] Furthermore, a method for removing a forsterite coating (glass coating) can be achieved by immersing the electrical steel sheet from which the insulating coating has been removed by the above method in high-temperature hydrochloric acid. Specifically, the concentration of hydrochloric acid preferred for removing the forsterite coating to be dissolved is determined in advance, and the forsterite coating can be removed by immersing the sheet in hydrochloric acid of this concentration (e.g., 30 to 40 mass % hydrochloric acid) at 80 to 90°C for 1 to 5 minutes, followed by rinsing with water and drying. Typically, different treatment solutions are used to remove each coating, such as using an alkaline solution to remove the insulating coating and hydrochloric acid to remove the forsterite coating.

[0056] The process by which the grain-oriented electrical steel sheet according to this embodiment was obtained will be described below.

[0057] The frequency of practical Goss orientation grains, which have a small angular deviation from the ideal Goss orientation, {110}<001>, increases as the heating rate of the primary annealing (decarburization annealing) increases. In contrast, crystal grains that are easily encroached upon by Goss orientation grains, such as those with {778}<447> (≒{111}<112>) and {411}<148> orientations, which have a Σ9 correspondence orientation relationship with the Goss orientation, (called "corresponding orientation grains"), decrease as the heating rate of the primary annealing increases. Therefore, it has been difficult to increase the proportion of practical Goss orientation grains while also increasing the proportion of corresponding orientation grains during the primary annealing.

[0058] In this embodiment, it has been discovered for the first time that a grain-oriented electrical steel sheet having excellent quality can be obtained by performing local rapid heating on a cold-rolled steel sheet to form a locally heated region, and then performing primary annealing (decarburization annealing) and secondary annealing (finish annealing).

[0059] The locally heated region formed before the primary annealing is located locally on the surface of the steel sheet. The crystalline structure of this locally heated region consists of one or both of a recrystallized structure and a recovered structure at the end of the local rapid heating. The crystalline structure of the non-rapidly heated portion of the steel sheet surface other than the locally heated region consists of a cold-worked structure that remains as it was cold-rolled.

[0060] The localized rapid heating is preferably performed at a heating rate of 500°C / s or more, preferably 2000°C / s or more, and more preferably 10000°C / s or more. Thus, it has been found that when a locally heated region is formed on the surface of a steel sheet before primary annealing and then primary annealing is performed on this steel sheet, many crystal grains having the practical Goss orientation are formed in the region heat-affected by the localized rapid heating (localized heat-affected region). It has also been found that, among the formed Goss-oriented grains, the proportion of Goss-oriented grains with a smaller angular deviation from the ideal Goss orientation increases, and the grain size of the Goss-oriented grains after primary annealing increases.

[0061] The frequency of coarse Goss-oriented grains in the local heat-affected zone is higher than that obtained by conventional rapid heating of the entire sheet. This characteristic is thought to be due to the fact that the peripheral area of ​​the locally heated zone has a deformed structure that retains a lot of strain. Specifically, when local rapid heating is performed, the practical Goss-oriented grains generated in the locally heated zone preferentially encroach on the peripheral unrecrystallized region, which retains a lot of strain, during primary annealing, thereby increasing in diameter. However, when the entire steel sheet is heated, the formation and growth of recrystallized grains occurs uniformly within the steel sheet, so the above-mentioned enlargement of grain diameter is thought to be prevented.

[0062] After the primary annealing has scattered local heat-affected zones with the above characteristics on the steel sheet surface, secondary annealing is then performed. The Goss-oriented grains formed in the local heat-affected zone grow preferentially during secondary annealing. Many Goss-oriented grains are formed in the local heat-affected zone, including Goss-oriented grains with particularly small angular deviation, close to the ideal Goss orientation, and large crystal grain sizes after the primary annealing. These Goss-oriented grains grow preferentially during secondary recrystallization.

[0063] Since Goss-oriented grains, which serve as nuclei for secondary recrystallization, are supplied to the local heat-affected zone, there is no need to form Goss-oriented grains in the matrix portion other than the local heat-affected zone, i.e., the local heat-unaffected zone, during primary annealing. Therefore, the primary annealing conditions may be slow heating conditions with a low heating rate, which allows for the formation of many corresponding-oriented grains with the {111}<112> and {411}<148> orientations, which are susceptible to corrosion, in the local heat-unaffected zone. For example, by setting the heating rate of the primary annealing to 300°C / sec or less, many Goss-oriented grains with large grain sizes and close to the ideal Goss orientation are formed in the local heat-affected zone, while almost no Goss-oriented grains are formed in the local heat-unaffected zone, resulting in the formation of many corresponding-oriented grains.

[0064] As described above, in the local heat affected zone of a steel sheet (decarburized annealed steel sheet) that has undergone local rapid heating and primary annealing, many Goss-oriented grains with large grain sizes and close to the ideal Goss orientation are present. On the other hand, in the matrix portion (zone not affected by local heating), there are almost no large-sized Goss-oriented grains, and many corresponding-orientation grains that are susceptible to erosion can be present.

[0065] When such a steel sheet (decarburization-annealed steel sheet) is subjected to secondary annealing, Goss-oriented grains that are close to the ideal Goss orientation and have large grain sizes in the local heat-affected zone begin preferential growth and grow toward the local heat-unaffected zone. When these Goss-oriented grains that have begun preferential growth collide with other Goss-oriented grains that have begun growing from the adjacent local heat-affected zone, grain growth stops. In this embodiment, by favorably positioning the local heat-affected zone, coarse Goss-oriented grains that preferentially grow close to the ideal Goss orientation are favorably positioned in the steel sheet, resulting in a smaller grain size of the Goss-oriented grains at the end of secondary annealing. In other words, a secondary recrystallized structure with a fine grain size can be obtained despite the steel sheet having a crystal orientation close to the ideal Goss orientation.

[0066] The details of the investigations carried out by the present inventors will be specifically described below.

[0067] As one embodiment of the localized rapid heating, a case where spot resistance heating is used will be described. In spot resistance heating, spot electrodes are pressure-bonded to both surfaces of a steel sheet so as to face each other, and an electric current is passed between the spot electrodes to spot-heat the electrode-holding portion of the steel sheet. A steel having the chemical composition shown in Table 1 was hot-rolled and cold-rolled to a thickness of 0.22 mm. This steel sheet was subjected to spot resistance heating. Spot resistance heating was performed using copper electrodes with a diameter of 3 mm under the following conditions: a current of 5.0 kA or less, which is within a range that does not melt the steel sheet surface; a current time of 20 to 80 milliseconds; an electrode pressure of 50 kgf to 150 kgf; and an electrode holding time after current application of 0.2 seconds. Spot resistance heating was performed on the surface of the cold-rolled steel sheet in a grid pattern at a 20 mm pitch in the rolling direction and a 30 mm pitch in the width direction (perpendicular to the rolling direction), forming a locally heated region. This cold-rolled steel sheet was subjected to decarburization annealing (primary annealing), in which the cold-rolled steel sheet was heated at a heating rate of 20°C / sec and held at 830°C for 90 seconds.

[0068] An example of the arrangement of the local heat affected zone in a decarburization-annealed steel sheet produced under the above conditions is shown in Figure 1. The decarburization-annealed steel sheet 1, the local heat affected zone 2, the rolling direction 21, and the width direction (direction perpendicular to the rolling direction) 22 are schematically shown in Figure 1.

[0069]

[0070] To prepare an observation surface for EBSD (Electron Back Scattering Diffraction pattern) on the surface of the decarburized annealed steel sheet (steel sheet after localized rapid heating and primary annealing), a smooth surface was prepared by mechanical polishing, and electrolytic polishing was performed to remove surface processing strain. The IQ (Image Quality) value and crystal orientation were measured in 0.5 μm steps in a region including the locally heated region by EBSD. Figure 2 is a schematic diagram showing the distribution of Goss orientation grains in the decarburized annealed steel sheet produced under the above conditions.

[0071] The current-carrying electrode used in spot resistance heating is circular, and its diameter, in terms of circle equivalent diameter, is preferably 0.5 mmφ to 10 mmφ, more preferably 1 mmφ to 5 mmφ. Note that, although a circular current-carrying electrode was used in the above, it is sufficient to locally increase the heating rate of the cold-rolled steel sheet, form Goss-oriented grains in this region, and cause the grains to grow, and the electrode shape may be other shapes, for example, elliptical or linear.

[0072] In FIG. 2, the angle deviation φ=(α ２ +β ２ ) １／２ Based on the definition of "Goss orientation," crystal grains (Goss-oriented grains 14) with an angular deviation φ of 10° or less from the ideal Goss orientation were marked with a "○." Furthermore, from among the crystal grains with an angular deviation φ of 10° or less, crystal grains with coarse grain sizes (coarse Goss-oriented grains 15) were marked with a "◎." Note that coarse Goss-oriented grains 15 refer to Goss-oriented grains with a grain size three times or more larger than the average grain size.

[0073] As shown in Figure 2, the decarburization annealed steel sheet 1 produced under the above conditions contains Goss-oriented grains 14 as well as coarse Goss-oriented grains 15. In particular, the region containing the coarse Goss-oriented grains 15 corresponds to the local heat-affected zone 2. Note that although Figure 2 schematically illustrates the local heat-affected zone boundary 4 and the local heat-affected zone boundary 5, it is not easy to distinguish these boundaries by observing the structure. However, the region containing the coarse Goss-oriented grains 15 can be considered the local heat-affected zone 2.

[0074] The decarburized annealed steel sheets were further nitrided, coated with an annealing separator mainly composed of MgO, and then subjected to secondary annealing under the conditions of a hydrogen-nitrogen atmosphere, a temperature rise rate of 15°C / hr (°C / hr), and a holding time of 1200°C for 20 hr (hr).

[0075] The resulting steel sheets were subjected to macro-etching to reveal the grain boundaries. Observation of the areas corresponding to the local heat-affected zones on the steel sheets after macro-etching revealed that multiple secondary recrystallized grains had grown from the areas corresponding to the local heat-affected zones, and that secondary recrystallized grains had spread from the center of the areas corresponding to the local heat-affected zones. Furthermore, in areas corresponding to the local heat-affected zones, small grains of 2 mm or less were sometimes observed as traces of the local heat-affected zones, but not in other cases. Although the secondary recrystallized macrostructure may change slightly depending on the local heating conditions, the degree of integration in the Goss orientation was increased compared to when local heat treatment was not performed.

[0076] It was confirmed that the obtained grain-oriented electrical steel sheet had an extremely small deviation between the crystal orientation of the secondary recrystallized grains and the ideal Goss orientation, and that the grains did not grow coarsely. Furthermore, although magnetic domain control technology was applied to this grain-oriented electrical steel sheet, the magnetic flux density B ８ is 1.940T or more, and iron loss W １７／５０ It was confirmed that the Lva200@1.7T was 46.0 dB or less.

[0077] Considering the above results, it is believed that the formation of coarse Goss orientation grains close to the ideal Goss orientation with a size advantage in the decarburized annealed steel sheet is the reason for the favorable secondary recrystallization orientation. In addition, it is believed that the favorable arrangement of the localized heating region before the primary annealing, the favorable control of the annealing conditions during the primary annealing, and then the secondary annealing are the reasons for the favorable combination of the Goss orientation concentration and the grain size.

[0078] For example, when the above-described decarburized annealed steel sheet is used, during secondary recrystallization, among the numerous Goss-oriented grains in the local heat-affected zone, coarse Goss-oriented grains (Goss-oriented grains with large grain sizes) close to the ideal Goss orientation preferentially grow. Therefore, even without growing the secondary recrystallized grains large, a steel sheet dominated by secondary recrystallized grains close to the ideal Goss orientation can be obtained. For example, when scattering the local heat-affected zones on the steel sheet surface, the size, shape, and arrangement of the grains after secondary annealing can be controlled by appropriately arranging the local heat-affected zones on the steel sheet surface. For example, if a Goss-oriented grain that starts growing from one local heat-affected zone collides with another Goss-oriented grain that starts growing from an adjacent local heat-affected zone, the grain size of the Goss-oriented grains at the end of secondary annealing will be small, resulting in a steel sheet with excellent core loss. In particular, as mentioned above, in the early stage of secondary annealing, the Goss-oriented grains that grow preferentially from the local heat-affected zone have a crystal orientation close to the ideal Goss orientation, so that good magnetic flux density can be obtained despite the small secondary recrystallized grain size.

[0079] In other words, the above-mentioned grain-oriented electrical steel sheet can increase the magnetic flux density while suppressing the coarsening of the secondary recrystallized grain size, thereby reducing the introduction of strain and groove formation for magnetic domain refinement. Specifically, since the grain boundaries that increase with the refinement of the secondary recrystallized grain size can achieve a certain degree of magnetic domain refinement effect, the energy density of the laser irradiation can be lowered and the depth of the grooves formed can be made shallower than in the conventional technology. Therefore, compared to the conventional technology, the increase in the magnetostriction rate level Lva due to the distortion caused by the laser irradiation and the increase in the magnetic flux density B due to the formation of the grooves can be reduced. ８ The decrease in the amount of the ion exchange resin can be preferably suppressed.

[0080] Next, a preferred method for manufacturing the grain-oriented electrical steel sheet according to this embodiment will be described.

[0081] The method for manufacturing the grain-oriented electrical steel sheet according to the present embodiment is not limited to the method described below. The manufacturing method described below is one example for manufacturing the grain-oriented electrical steel sheet according to the present embodiment.

[0082] Furthermore, the steps and quantitative conditions for each step shown below are examples adopted to demonstrate the feasibility of this embodiment, and this embodiment is not limited to these steps and quantitative values. The method for manufacturing a grain-oriented electrical steel sheet according to this embodiment can adopt various conditions as long as they do not deviate from the gist of this embodiment and achieve the object of this embodiment.

[0083] The method for manufacturing the grain-oriented electrical steel sheet according to the present embodiment can apply, as a basic step, conventional methods for manufacturing grain-oriented electrical steel sheets. For example, conventional methods for manufacturing grain-oriented electrical steel sheets include a method for forming inhibitors such as MnS or AlN by high-temperature slab heating, and a method for forming AlN inhibitors by low-temperature slab heating and nitriding. The method for manufacturing the grain-oriented electrical steel sheet according to the present embodiment is not limited to a specific manufacturing method. Below, a method for applying nitriding as the low-temperature slab heating process will be described.

[0084] (Casting Process) In the casting process, a slab is prepared. An example of a method for producing a slab is as follows: Molten steel is produced (smelted). A slab is produced using the molten steel. The slab may be produced by continuous casting. The molten steel may be used to produce an ingot, and the ingot may be bloomed to produce a slab. The thickness of the slab is not particularly limited. The thickness of the slab is, for example, 150 to 350 mm. The thickness of the slab is preferably 220 to 280 mm. A so-called thin slab having a thickness of 10 to 70 mm may be used as the slab. When a thin slab is used, rough rolling before finish rolling can be omitted in the hot rolling process.

[0085] For example, the above slab may contain the following elements as its chemical composition:

[0086] C: 0.085% or less. Carbon (C) is an effective element for controlling the primary recrystallization structure during the manufacturing process, but excessive C content in the final product adversely affects the magnetic properties. Therefore, the C content is 0.085% or less. The preferred upper limit of the C content is 0.075%. C is purified in the decarburization annealing process and the finish annealing process, resulting in a C content of 0.005% or less. When C is contained, taking into account productivity in industrial production, the lower limit of the C content may be more than 0%, or even 0.001%.

[0087] Si: 2.0 to 7.0% Silicon (Si) increases the electrical resistance of grain-oriented electrical steel sheets and reduces iron loss. If the Si content is less than 2.0%, γ transformation occurs during finish annealing, damaging the crystal orientation of the grain-oriented electrical steel sheets. On the other hand, if the Si content exceeds 7.0%, cold workability decreases, making cracks more likely to occur during cold rolling. The preferred lower limit of the Si content is 2.5%, more preferably 3.0%. The preferred upper limit of the Si content is 4.5%, more preferably 4.0%.

[0088] Mn: 0.05 to 1.00% Manganese (Mn) combines with S or Se to form MnS or MnSe, which functions as an inhibitor. When Mn is contained, secondary recrystallization is stabilized when the Mn content is within the range of 0.05 to 1.00%. Note that part of the inhibitor function can be performed by nitrides of Nb group elements. In this case, the strength of MnS or MnSe as a general inhibitor is controlled to be weak. For this reason, the preferred upper limit of the Mn content is 0.50%, and more preferably 0.20%.

[0089] At least one of S and Se: 0.003 to 0.035% in total. Sulfur (S) and selenium (Se) combine with Mn to form MnS or MnSe, functioning as an inhibitor. When at least one of S and Se is contained, secondary recrystallization is stabilized if the total content of S and Se is 0.003 to 0.035%. It is possible for part of the inhibitor function to be performed by nitrides of Nb group elements. In this case, the strength of MnS or MnSe as a general inhibitor is controlled to be weak. For this reason, the preferred upper limit of the total S and Se content is 0.025%, more preferably 0.010%. If S and Se remain after final annealing, they form compounds that deteriorate iron loss. Therefore, it is preferable to reduce S and Se as much as possible through purification during final annealing.

[0090] Here, the total content of S and Se means that at least one of S and Se is included and the total content thereof is included.

[0091] Al: 0.010 to 0.065% Aluminum (Al) combines with N to precipitate as (Al, Si)N, functioning as an inhibitor. When Al is contained, if the Al content is within the range of 0.010 to 0.065%, AlN, which acts as an inhibitor formed by nitriding (described later), expands the secondary recrystallization temperature range, stabilizing secondary recrystallization particularly in the high-temperature range. Therefore, the Al content is 0.010 to 0.065%. The preferred lower limit of the Al content is 0.020%, and more preferably 0.025%. From the viewpoint of secondary recrystallization stability, the preferred upper limit of the Al content is 0.040%, and more preferably 0.035%.

[0092] N: 0.012% or less Nitrogen (N) combines with Al and functions as an inhibitor. Since N can be incorporated by nitriding during the manufacturing process, no lower limit is specified. For example, the lower limit of the N content may be greater than 0%, or even 0.001%. On the other hand, when N is incorporated, if the N content exceeds 0.012%, blisters, a type of defect, tend to occur in the steel sheet. The preferred upper limit of the N content is 0.010%, more preferably 0.009%. N is purified in the final annealing process, and the N content is 0.005% or less after the final annealing process.

[0093] The balance of the above chemical composition is composed of Fe and impurities. The term "impurities" refers to elements that are mixed in from raw materials such as ore or scrap, or from the manufacturing environment, during industrial production of steel. The upper limit of the total content of impurities may be, for example, 5%.

[0094] The above-mentioned chemical composition may contain known optional elements in place of a portion of Fe, taking into consideration not only solving problems in production but also strengthening the inhibitor function by compound formation and the influence on magnetic properties. Examples of optional elements that can be contained in place of a portion of Fe include the following elements.

[0095] Nb group elements: 0.050% or less The total content of Nb group elements (one or more of Nb, V, Mo, Ta, and W) may be 0.050% or less. When Nb group elements are used as part of the inhibitor, a total content of Nb group elements of 0.030% or less is preferable because it initiates secondary recrystallization at an appropriate timing. In addition, the orientation of the secondary recrystallized grains that occur becomes very favorable, and ultimately, it is possible to control the structure to be favorable for magnetic properties. In particular, Nb and Ta have a strong effect and are preferable. There is no need to set a lower limit for the total content of Nb group elements; the lower limit may be 0%. This lower limit is preferably 0.003%.

[0096] The total content of Nb group elements is more preferably 0.004 to 0.020%, and even more preferably 0.005 to 0.010%.

[0097] Here, the total content of Nb group elements means the total content including at least one of Nb, V, Mo, Ta, and W.

[0098] The slab may also contain, as optional elements, at least one of the following in mass%: Cu: 0.40% or less, Bi: 0.010% or less, B: 0.080% or less, P: 0.50% or less, Ti: 0.015% or less, Sn: 0.10% or less, Sb: 0.10% or less, Cr: 0.30% or less, and Ni: 1.00% or less. These optional elements may be contained according to known purposes, so there is no need to set a lower limit for the content of the optional elements, and the lower limit may be 0%.

[0099] The chemical composition of the slab may be measured by the above-mentioned analytical method, in the same manner as the chemical composition of the grain-oriented electrical steel sheet as the final product.

[0100] (Hot Rolling Process) The hot rolling process is a process in which a slab heated to a predetermined temperature (for example, 1100 to 1400°C) is hot-rolled to obtain a hot-rolled steel sheet. In the hot rolling process, for example, the silicon steel material (slab) heated in the heating process is rough-rolled, and then finish-rolled to obtain a hot-rolled steel sheet with a predetermined thickness, for example, 1.8 to 3.5 mm. After the finish rolling is completed, the hot-rolled steel sheet is coiled at a predetermined temperature.

[0101] In the case of a process that includes a nitriding step during or after decarburization annealing, the strength of MnS as an inhibitor is not so necessary, so in consideration of productivity, the slab heating temperature should be set to 1100°C to 1280°C.

[0102] (Hot-rolled sheet annealing process) The hot-rolled sheet annealing process is a process in which the hot-rolled steel sheet obtained in the hot-rolling process is annealed under predetermined temperature conditions (e.g., at 750 to 1200°C for 30 seconds to 10 minutes) to obtain an annealed steel sheet. Hot-rolled sheet annealing is generally performed to control the steel sheet structure, such as the recrystallization rate, residual strain, and crystal grain size, by annealing the hot-rolled steel sheet after the hot-rolling process, and to favorably adjust the precipitate morphology in the steel. For example, in a high-temperature slab heating process, this is a process that ultimately controls the morphology of precipitates such as AlN, and conditions are adjusted to precipitate uniformly and finely. In hot-rolled sheet annealing, for example, the steel sheet is heated to 1050°C to 1150°C, and then slowly cooled to an intermediate temperature (850°C to 950°C) over 50 to 150 seconds to properly precipitate AlN, etc., followed by water cooling.

[0103] (Cold Rolling Step) The cold rolling step is a step in which the annealed steel sheet obtained in the hot-rolled sheet annealing step is subjected to a single cold rolling or multiple (two or more) cold rolling steps (e.g., a total cold rolling rate of 80 to 95%) via annealing (intermediate annealing) to obtain a cold-rolled steel sheet having a thickness of, for example, 0.10 to 0.50 mm. In order to improve the magnetic properties, for example, the interpass temperature in the cold rolling may be set to about 100°C to 300°C.

[0104] (Localized Rapid Heating Process) In this embodiment, localized rapid heating is performed on the cold-rolled steel sheet after the cold rolling process to form a locally heated region. The rapid heating method is not particularly limited as long as it can locally heat the steel sheet. For example, a method of heating by contacting spot electrodes to the front and back surfaces of the steel sheet and passing an electric current through the steel sheet, a method of heating by irradiating the steel sheet surface with laser light or an electron beam, a method of locally heating by induction heating, or a method of heating by contacting a hot piece can be used. The size of each locally heated region can be a dot-like region with a diameter of about 10 μm to 10 mm, or a linear region with a width of about 10 μm to 10 mm. Furthermore, the electrodes used for electrical heating may be circular electrodes as described above, or linear electrodes.

[0105] Regarding the size of the locally heated region, the minimum diameter and width depend on the shape of the spot electrode and the technology for reducing the focused diameter of the laser light or electron beam. While it is theoretically possible to further reduce the size of the locally heated region, considering that the current size of recrystallized grain nuclei is approximately 1 μm, it is believed that the effect can be achieved if the size of the locally heated region is 1 μm or more. Industrially, the minimum diameter and width should be 10 μm or more. Regarding the size of the locally heated region, if the maximum diameter or width exceeds 10 mm, the area proportion of Goss-oriented grains with a relatively large angular deviation that cannot grow outside the locally heated region increases. In this case, the effect of local rapid heating is less likely to be achieved.

[0106] In localized rapid heating, the heating rate should be 500°C / s or more at the center of the locally heated region as viewed in the thickness direction and at 1 / 5 of the thickness of the steel plate. If the heating rate in the above region is 500°C / s or more, the structure of the locally heated region can be preferably controlled to a recovered structure or a recrystallized structure. The heating rate is preferably 2000°C / s or more, and more preferably 10000°C / s or more. On the other hand, the upper limit of the heating rate is not particularly limited, and may be, for example, 1000000°C / s.

[0107] Furthermore, it is preferable to control the above heating rate in combination with and inseparably with the heating rate during decarburization annealing, which will be described later. For example, in this embodiment, the aim is to have coarse Goss-oriented grains in the local heat-affected zone after decarburization annealing. However, if the heating rate during decarburization annealing is faster than the heating rate during local rapid heating, it is difficult to achieve the above objective. Therefore, although it depends on the magnitude of the heating rate, it is preferable to set the heating rate during local rapid heating to be equal to or greater than the heating rate during decarburization annealing. Those skilled in the art will be able to preferably control the heating rates during local rapid heating and decarburization annealing if they understand the aim of having coarse Goss-oriented grains in the local heat-affected zone after decarburization annealing.

[0108] The above-mentioned 1 / 5 part of the plate thickness of the steel plate means a depth corresponding to 1 / 5 of the plate thickness of the steel plate from the surface of the steel plate in the plate thickness direction.

[0109] Furthermore, in localized rapid heating, it is sufficient that the maximum temperature reached is 700°C or higher in the center of the locally heated region as viewed from the thickness direction and at 1 / 5 of the thickness of the steel plate. If the maximum temperature reached in the above region is 700°C or higher, the structure of the locally heated region can be preferably controlled to a recovered structure or a recrystallized structure. The above maximum temperature reached is preferably 800°C or higher, and more preferably 900°C or higher. On the other hand, the above maximum temperature reached may be lower than the melting point of the steel plate, for example, 1400°C or lower.

[0110] Furthermore, in the localized rapid heating, the holding time from reaching the maximum temperature to cooling to 700°C at the center of the locally heated region as viewed in the thickness direction and at 1 / 5 of the thickness of the steel plate is 0.1 seconds or more. If the holding time in the above region is 0.1 seconds or more, the structure of the locally heated region can be preferably controlled to a recovered structure or a recrystallized structure. The holding time is preferably 0.2 seconds or more, more preferably 0.3 seconds or more, and even more preferably 0.4 seconds or more. On the other hand, there is no particular limitation on the upper limit of the holding time, and it may be, for example, 10 seconds or less. The holding time from reaching the maximum temperature to cooling to 700°C has a fundamental effect on the formation of coarse Goss-oriented grains close to the ideal Goss orientation.

[0111] In localized rapid heating, it is important to control the heating rate and maximum temperature, as well as the holding time. During this holding time, subgrain structures and recrystallization nuclei that are advantageous for the formation of coarse Goss-oriented grains in the locally heated region can be formed. Controlling the subgrain structure in the locally heated region by the holding time allows for favorable microstructural control in subsequent processes.

[0112] As described above, the method of local rapid heating is not particularly limited. For example, local rapid heating may be performed by spot current heating, laser irradiation, or electron beam irradiation. Regardless of the local rapid heating method, it is sufficient to control the heating rate, maximum temperature, and holding time as described above. A person skilled in the art can combine the conditions of the local rapid heating method to control the desired heating rate, maximum temperature, and holding time.

[0113] For example, a person skilled in the art can perform heat conduction analysis using the finite element method to control the heating rate and the maximum temperature reached at the center of the locally heated region as viewed from the thickness direction and at 1 / 5 of the thickness of the steel plate. Additionally, a person skilled in the art can control the above-mentioned holding time by adjusting the heat removal conditions after the maximum temperature is reached. For example, in the case of spot current heating, this can be achieved by controlling the electrode holding time after current application or by changing the shape of the spot electrode to a shape suitable for heat removal. Furthermore, in the case of laser irradiation or electron beam irradiation, the irradiation speed can be adjusted or the shape of the irradiation region can be changed to an ellipse or the like to gradient the irradiation energy from the center to the outer edge of the irradiation region.

[0114] In general, heating by laser irradiation preferentially heats only the vicinity of the irradiated steel sheet surface, and the interior of the steel sheet is less likely to be heated. Furthermore, since heating by laser irradiation is non-contact heating, heat is removed quickly after heating and the temperature is difficult to maintain. Therefore, when laser irradiation heating is performed as localized rapid heating, in order to recover or recrystallize the cold-worked structure in the laser-irradiated area, it is necessary to control the conditions so that not only the surface of the steel sheet but also the interior of the steel sheet is heated, and the cooling rate is slowed to relatively coarsen the subgrain structure in the laser-irradiated area. The laser irradiation conditions for localized rapid heating are completely different from the laser irradiation conditions for magnetic domain refinement. For example, the laser irradiation conditions for magnetic domain refinement (usually 0.5 to 50 mJ / mm ２ ) is applied to this embodiment, the structure of the locally heated region is not controlled favorably, and coarse Goss-oriented grains close to the ideal Goss orientation are not formed in the steel sheet after the decarburization annealing process. The same applies to electron beam irradiation as to laser irradiation. Even if the electron beam irradiation conditions for magnetic domain refinement are applied to this embodiment, the structure of the locally heated region is not controlled favorably, and coarse Goss-oriented grains close to the ideal Goss orientation are not formed in the steel sheet after the decarburization annealing process.

[0115] However, simply increasing the input power of laser or electron beam irradiation makes it difficult to form coarse Goss-oriented grains close to the ideal Goss orientation. For example, when rapid heating is performed by laser or electron beam irradiation, it is preferable to make the beam shape elliptical or adjust the scan speed, etc., so as to ensure a temperature range in which the crystal grains in that region can grow after rapid heating.

[0116] Conventionally, laser irradiation or electron beam irradiation has been performed on electrical steel sheets to control magnetic domains after secondary recrystallization and reduce iron loss. Under these laser or electron beam irradiation conditions, the steel sheet is heated to a depth of approximately 20 μm from the surface, resulting in rapid heat dissipation after heating. Therefore, under conventional conditions, it is difficult to ensure the required holding time from reaching the maximum temperature to cooling to 700°C. In other words, under conventional laser or electron beam irradiation conditions, although the irradiated area may be able to act as a barrier to the growth of secondary recrystallized grains, it is difficult to form coarse Goss-oriented grains with an orientation close to the ideal Goss orientation, as in the present embodiment. To form coarse Goss-oriented grains close to the ideal Goss orientation by laser or electron beam irradiation, the conditions for laser or electron beam irradiation must be considered as described above.

[0117] (Decarburization Annealing Process) In the decarburization annealing process, the cold-rolled steel sheet after the local rapid heating process is subjected to decarburization annealing (primary annealing). This decarburization annealing increases the frequency of Goss-oriented grains formed in the local heat-affected zone, increases the grain size of the Goss-oriented grains, and preferably forms coarse Goss-oriented grains with an orientation close to the ideal Goss orientation. The decarburization annealing conditions may be a heating rate of 10 to 10,000°C / s, an annealing temperature of 700 to 900°C, and an annealing time of 10 to 600 seconds. Furthermore, by subjecting the cold-rolled steel sheet to decarburization annealing, C contained in the cold-rolled steel sheet is removed. Decarburization annealing is preferably performed in a humid atmosphere to remove "C" contained in the cold-rolled steel sheet.

[0118] It is also effective to reduce the primary recrystallized grain size by controlling the conditions of the hot rolling and hot-rolled sheet annealing described above, or by lowering the decarburization annealing temperature as necessary. The primary recrystallized grain size is not particularly limited, but is preferably 8 to 30 μm.

[0119] Furthermore, in this embodiment, many coarse Goss-oriented grains with orientations close to the ideal Goss orientation are formed in the local heat-affected zone. Therefore, there is no need to form Goss-oriented grains by decarburization annealing. As described above, the heating rate for decarburization annealing may be 10,000°C / s or less. However, it is preferable to use a slower heating rate for decarburization annealing to form {111}<112>-oriented grains and {411}<148>-oriented grains that are easily eroded into the matrix portion (local heat-unaffected zone). For example, the heating rate for decarburization annealing is preferably 300°C / s or less, more preferably 200°C / s or less, and even more preferably 100°C / s or less.

[0120] The amount of decarbonation and the state of the surface oxide layer affect the formation of the glass film. Therefore, in decarburization annealing, the degree of oxidation (PH) in the annealing atmosphere (furnace atmosphere) is important. ２ O / PH ２ ) may be set to 0.01 to 0.15. ２ O / PH ２ is the partial pressure of water vapor in the atmosphere, PH ２ O and hydrogen partial pressure PH ２ It can be defined as the ratio of

[0121] (Nitriding) Nitriding is an effective treatment in low-temperature slab heating processes where the slab heating temperature is 1280°C or less, and is an important step for adjusting the strength of the inhibitor in secondary recrystallization. Nitriding increases the nitrogen content of the steel sheet by approximately 40 to 200 ppm between the start of decarburization and the start of secondary recrystallization in finish annealing. Examples of nitriding include annealing in an atmosphere containing a nitriding gas such as ammonia, and finish annealing of a decarburized annealed steel sheet coated with an annealing separator containing a nitriding powder such as MnN. The amount of nitride after nitriding is preferably 130 to 350 ppm, and more preferably 150 to 250 ppm.

[0122] (Annealing separator application step) The annealing separator application step is a step of applying an annealing separator to a decarburized annealed steel sheet. Examples of the annealing separator include an annealing separator containing MgO as a main component and an annealing separator containing Al. ２ O ３ The decarburized annealed steel sheet after being coated with the annealing separator is wound into a coil and then finish-annealed in the subsequent finish-annealing step.

[0123] (Finish annealing process) The finish annealing process is a process in which the decarburized annealed steel sheet coated with the annealing separator is subjected to finish annealing (secondary annealing) to cause secondary recrystallization. In this process, the growth of primary recrystallized grains is suppressed by an inhibitor, and secondary recrystallization is allowed to proceed, thereby preferentially growing {100}<001> oriented grains and dramatically improving magnetic flux density.

[0124] In the final annealing, the decarburized annealed steel sheet that has been coated with an annealing separator and dried may be held for 10 hours to 60 hours in a temperature range of 1000° C. to 1300° C. The atmosphere during the final annealing may be, for example, a nitrogen atmosphere or a mixed atmosphere of nitrogen and hydrogen.

[0125] In this embodiment, secondary recrystallization may be induced by applying a temperature gradient of more than 0.5°C / cm, preferably 1.0°C / cm or more, to the boundary between the primary recrystallized region and the secondary recrystallized region in the steel sheet during the heating process of finish annealing. For example, the above temperature gradient may be applied to the steel sheet during the growth of secondary recrystallized grains in a temperature range of 800°C or higher during the heating process of finish annealing. The direction in which the temperature gradient is applied may be the direction perpendicular to the rolling direction C. The temperature gradient may be appropriately changed depending on the chemical composition of the steel. For example, if the chemical composition favors preferential growth of secondary recrystallized grains, the temperature gradient may be more than 0.5°C / cm (preferably 1.0°C / cm or more). On the other hand, if the chemical composition favors preferential growth of secondary recrystallized grains, the temperature gradient is preferably more than 1.0°C / cm.

[0126] The method for providing a temperature gradient is not particularly limited, and any known method may be applied. For example, when a box-type annealing furnace is used and a coiled steel sheet is placed in the furnace and heated, the position and arrangement of the heating device and the temperature distribution in the annealing furnace may be controlled so that a sufficient temperature difference is generated from the top to the bottom of the coil or from the outside to the inside. Alternatively, a temperature distribution may be formed in the coil to be annealed by actively heating only a portion of the coil using an induction heating, high-frequency heating, or electric current heating device.

[0127] If a temperature gradient is applied to the steel sheet during the heating process of the finish annealing, secondary recrystallized grains with sharp orientations are generated from the portion of the coil that has reached the secondary recrystallization initiation state early, and these secondary recrystallized grains grow preferentially due to the temperature gradient. For example, the secondary recrystallized grains can be grown throughout the entire coil.

[0128] (Insulating Coating Forming Step) A coating solution containing phosphoric acid or a phosphate, chromic anhydride or a chromate, and colloidal silica is applied to the steel sheet after the final annealing and baked (for example, at 350°C to 1150°C for 5 to 300 seconds) to form an insulating coating.

[0129] (Magnetic Domain Control Step) After the insulating coating step, a localized micro-distortion region or a localized groove is formed in the steel sheet by a known method such as laser, plasma, mechanical method, or etching.

[0130] The method for imparting localized microstrain to the steel sheet is not particularly limited. For example, strain may be imparted to the steel sheet by irradiating it with a laser or an electron beam. The steel sheet may not melt or may be partially melted by the irradiation with the laser or electron beam.

[0131] Similarly, the method for forming localized grooves in a steel sheet is not particularly limited. For example, grooves can be formed by irradiating the steel sheet with a laser or electron beam and melting and evaporating the steel in the irradiated area. Alternatively, grooves can be formed mechanically by pressing a gear against the surface of the steel sheet. Alternatively, grooves can be formed by printing a resist film with predetermined holes on the surface of the steel sheet and then electrolytic etching. Furthermore, groove formation can be performed at any known time point after the cold rolling process.

[0132] In order to subdivide the magnetic domains, the above-mentioned distortions and grooves are arranged in a line or dot shape on the rolled surface of the steel sheet so as to extend in a direction intersecting the rolling direction, and at intervals of 2 mm to 10 mm in the rolling direction. For example, the above-mentioned distortions are arranged when the energy density Ua is 0.1 to 10 mJ / mm ２ The grooves may be locally formed on the steel sheet so that the irradiation diameter is 10 to 500 μm. The grooves may be locally formed on the steel sheet so that the groove depth is 10 to 50 μm.

[0133] In the grain-oriented electrical steel sheet according to the present embodiment, for example, the energy density of the laser irradiation can be lowered or the depth of the grooves formed can be made shallower compared to the conventional technology. ８ By understanding the objective of "improving iron loss characteristics while preferably suppressing a decrease in magnetic field strength," it is possible to preferably control the magnetic domain control conditions within the above-mentioned numerical ranges depending on the target secondary recrystallized structure.

[0134] In the grain-oriented electrical steel sheet according to this embodiment, whether magnetic domains are controlled, i.e., whether the steel sheet has local strain or local grooves, can be determined by the following method. First, if the grain-oriented electrical steel sheet has an insulating coating or the like on its surface, this coating is removed. The coating can be removed by the method described above. The surface of the electrical steel sheet from which the coating has been removed is observed visually or under a microscope. If linear or dotted grooves are found on the steel sheet surface at intervals of 2 mm to 10 mm, the steel sheet is determined to have local grooves. Furthermore, if linear or dotted laser or electron beam irradiation marks are found on the steel sheet surface at intervals of 2 mm to 10 mm, the steel sheet is determined to have local strain. Those skilled in the art can determine whether linear or dotted grooves or laser or electron beam irradiation marks are local strain or local grooves due to magnetic domain refining.

[0135] It may be difficult to observe the irradiation marks of the laser or electron beam. In such cases, the sample may be heat-treated at 800°C for 120 minutes and the iron loss values ​​before and after the heat treatment may be compared.１７／５０ When the value of increases by 0.02 W / kg or more, it can be determined that the steel sheet before heat treatment has localized distortion.

[0136] The grain-oriented electrical steel sheet according to this embodiment can be manufactured by the above-mentioned steps. The grain-oriented electrical steel sheet according to this embodiment, which is manufactured by controlling the conditions of each step in a composite and inseparable manner, has an extremely small deviation between the crystal orientation of the secondary recrystallized grains and the ideal Goss orientation, and the crystal grains do not grow coarsely. Therefore, even if magnetic domain control technology is applied, the grain-oriented electrical steel sheet is excellent in all of magnetic flux density, iron loss, and noise characteristics.

[0137] For example, when manufacturing the grain-oriented electrical steel sheet according to this embodiment, it is assumed that local rapid heating is performed on the cold-rolled steel sheet, but other manufacturing conditions may be optimized depending on the purpose. For example, if the distance between the rolling direction L and the transverse direction C of the local rapid heating is narrowed, manufacturing conditions other than the local rapid heating can be relaxed, and the grain-oriented electrical steel sheet according to this embodiment can be manufactured without controlling the temperature gradient during the heating process of the finish annealing. On the other hand, if the distance between the rolling direction L and the transverse direction C of the local rapid heating is widened, the grain-oriented electrical steel sheet according to this embodiment can be manufactured by controlling the temperature gradient during the heating process of the finish annealing or by controlling the steel composition to a chemical composition that facilitates preferential growth of secondary recrystallized grains. Those skilled in the art, once they understand the characteristics of the grain-oriented electrical steel sheet according to this embodiment described above, will be able to preferably optimize the local rapid heating conditions and other manufacturing conditions.

[0138] Next, the effects of the present invention will be specifically described in detail using examples. The conditions in the examples are one example of conditions adopted to confirm the feasibility and effects of the present invention, and the present invention is not limited to this one example of conditions. The present invention can adopt various conditions as long as they do not deviate from the gist of the present invention and the object of the present invention is achieved.

[0139] Using the slabs with adjusted chemical compositions as raw materials, decarburized annealed steel sheets having the chemical compositions shown in Table 2 were manufactured. These chemical compositions were measured based on the above-mentioned method. In Table 2, "-" indicates that the content was not measured, and that control and manufacturing were not carried out with the content in mind.

[0140] When producing the above-mentioned decarburized annealed steel sheet, a slab was heated to 1150°C and subjected to hot rolling to obtain a hot-rolled steel sheet having a thickness of 2.6 mm. This hot-rolled steel sheet was then subjected to hot-rolled sheet annealing by heating to 1100°C and subsequently annealing at 900°C, and then subjected to pickling to remove scale formed on the surface. These steel sheets were subjected to a single cold rolling or multiple cold rollings with intermediate annealing in between to obtain a cold-rolled steel sheet having a final thickness of 0.22 mm.

[0141] The above cold-rolled steel sheets were subjected to localized rapid heating under the conditions shown in Tables 3 to 10. In spot current heating, a copper electrode with a diameter of 1 mm was used in contact with the steel sheet. The electrode shape, electrode pressure, current, current application time, and electrode holding time after current application were varied in a composite manner to control the heating rate, maximum temperature, and holding time from reaching the maximum temperature until cooling to 700°C (holding time at 700°C or higher). In laser heating, a fiber laser was used, and the focused spot diameter of the laser beam in the rolling direction (i.e., the diameter containing 86% of the laser output) was set to 30 μm (except for Tests No. 130 and 131). The laser irradiation energy density, laser scanning speed, and shape of the laser irradiation region were varied in a composite manner to control the heating rate, maximum temperature, and holding time at 700°C or higher. Those skilled in the art can combine the conditions of the localized rapid heating method to control the desired heating rate, maximum temperature, and holding time at 700°C or higher.

[0142] In Test No. 128, the laser beam was elongated in the scanning direction, and the holding time from reaching the maximum temperature until cooling to 700°C during local rapid heating was controlled to 0.2 seconds, so that coarse Goss-oriented grains with an orientation close to the ideal Goss orientation were formed in the locally heated region. In Test No. 129, general laser irradiation conditions for magnetic domain refinement were applied. In Test No. 130, the focused spot diameter was set to 0.5 mm, and the laser irradiation energy density was set to 2.0 J / mm. ２ In Test No. 131, the laser beam was focused at a spot diameter of 0.5 mm and a laser irradiation energy density of 30.0 J / mm.２ The laser beam was controlled so that the laser beam irradiated area would ultimately be the grain boundary of the secondary recrystallized grains.

[0143] In the table, "No treatment" for the localized rapid heating method indicates that localized rapid heating was not performed. The localized heating conditions "Linear or spotted" represent the shape of the localized heated area on the surface of the cold-rolled steel sheet, and the localized heating conditions "Rolling direction spacing" and "Width direction spacing" represent the spacing in the rolling direction and transverse direction at which the localized heated areas are arranged on the surface of the cold-rolled steel sheet. The localized heated areas are evenly spaced at equal intervals in the rolling direction and transverse direction. When providing localized heated areas on the surface of the cold-rolled steel sheet, they are arranged so that the distribution of the localized heated areas is not uneven.

[0144] In the table, the widthwise spacing "End 10" in the local heating conditions of localized rapid heating indicates that a localized heating region was formed only at a position 10 mm from the end of the steel sheet in the direction perpendicular to the rolling direction.

[0145] The cold-rolled steel sheets after localized rapid heating were subjected to decarburization annealing under the conditions shown in Tables 3 to 10. In the decarburization annealing, the degree of oxidation (PH) in the annealing atmosphere (furnace atmosphere) was measured. ２ O / PH ２ ) was set to 0.13.

[0146] The produced decarburized annealed steel sheets were subjected to nitriding treatment at 750°C in a nitrogen-hydrogen-ammonia atmosphere to adjust the nitrogen content of the steel sheets to 220 ppm. Furthermore, an annealing separator containing MgO as the main component was applied, and finish annealing was performed.

[0147] In the heating process of the finish annealing, the steel sheet was heated to 1000°C at a rate of 15°C / hr (°C / hr) in a mixed atmosphere of hydrogen and nitrogen, and then heated to 1200°C at the heating rate shown in Tables 11 to 18. In addition, in the heating process of the finish annealing, a temperature gradient shown in Tables 11 to 18 was applied in the direction perpendicular to the rolling direction C to the boundary region between the primary recrystallization region and the secondary recrystallization region in the steel sheet in a temperature range of 800°C or higher. In Tables 11 to 18, a temperature gradient of "<1.0" in the heating process of the finish annealing indicates that the temperature gradient in the heating process was not substantially controlled. After the heating process of the finish annealing, the steel sheet was held at 1200°C for 20 hours in a hydrogen atmosphere.

[0148] After the finish annealing, the steel sheet was coated with a coating solution for an insulating film, which was mainly composed of colloidal silica and phosphate, with chromic anhydride added as needed, and baked to form an insulating film.

[0149] To refine the magnetic domains, laser irradiation or groove formation was performed. For laser irradiation, a steel sheet having an insulating coating formed thereon was irradiated with a laser in a linear pattern extending in a direction intersecting the rolling direction on the rolled surface of the steel sheet, at intervals of 10 mm in the rolling direction, with an irradiation diameter of 300 μm, and at an energy density Ua shown in Tables 11 to 18. In Tables 11 to 18, an energy density Ua of "untreated" indicates that laser irradiation for magnetic domain refinement was not performed. For groove formation, grooves were formed in a linear pattern extending in a direction intersecting the rolling direction on the rolled surface of the steel sheet, at intervals of 5 mm in the rolling direction, with an average groove width of 100 μm and an average groove depth shown in Tables 11 to 18, and then an insulating coating was formed. In Tables 11 to 18, a groove depth of "-" indicates that groove formation for magnetic domain refinement was not performed.

[0150] The chemical composition of the base steel sheet, magnetic flux density B ８ , iron loss W １７／５０ The magnetostriction rate level Lva200@1.7T was measured based on the above-mentioned method. The results are shown in Tables 11 to 19. In Table 19, "-" indicates that the content was not controlled or manufactured with consideration given to the content, and the content was not measured. In addition, various properties were evaluated for the manufactured grain-oriented electrical steel sheets. The evaluation results are shown in Tables 11 to 19.

[0151] Among Nos. 1 to 159, the grain-oriented electrical steel sheets according to the present invention have a magnetic flux density B ８ , iron loss W １７／５０ , and the magnetostriction rate level Lva200@1.7T were favorably controlled.

[0152] On the other hand, among Nos. 1 to 159, the grain-oriented electrical steel sheets used as comparative examples have a magnetic flux density B ８ , iron loss W １７／５０ , or the magnetostriction rate level Lva200@1.7T was not controlled favorably.

[0153]

[0154]

[0155]

[0156]

[0157]

[0158]

[0159]

[0160]

[0161]

[0162]

[0163]

[0164]

[0165]

[0166]

[0167]

[0168]

[0169]

[0170]

[0171] According to the above-described aspects of the present invention, it is possible to provide a grain-oriented electrical steel sheet that is excellent in all of magnetic flux density, iron loss, and noise characteristics, even when magnetic domain control technology is applied, and therefore the present invention has high industrial applicability.

[0172] REFERENCE SIGNS LIST 1 Decarburization annealed steel sheet 2 Local heat affected zone 3 Local heat unaffected zone (matrix part) 4 Local heat affected zone boundary 5 Local heat affected zone boundary 14 Goss oriented grain 15 Coarse Goss oriented grain 21 Rolling direction 22 Width direction (direction perpendicular to rolling)

Claims

1. A grain-oriented electrical steel sheet having a base steel sheet and an insulating coating and having magnetic domain control. The magnetic flux density in the rolling direction when excited at 800 A / m is expressed in units of T and B. ８ The iron loss when excited to a magnetic flux density of 1.7 T at a frequency of 50 Hz is expressed in units of W / kg. １７／５０ When the magnetostriction rate level calculated from the magnetostriction amount of the 200 Hz component of the magnetostriction waveform when excited to a magnetic flux density of 1.7 T at a frequency of 50 Hz is defined as Lva200@1.7 T in dB units, ８ But, B ８ ≧1.940, １７／５０ But, W １７／５０ ≦0.670, and the Lva200@1.7T satisfies Lva200@1.7T≦46.0.