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    公开号:BR112013005335B1
    申请号:R112013005335-6
    申请日:2011-09-09
    公开日:2018-10-23
    发明作者:Tatsuhiko Sakai；Hideyuki Hamamura
    申请人:Nippon Steel & Sumitomo Metal Corporation；
    IPC主号:
    专利说明:

    (54) Title: ORIENTED GRAIN ELECTRIC STEEL PLATE AND METHOD FOR MANUFACTURING THE SAME (51) lnt.CI .: C21D 8/12; H01F 1/16 (30) Unionist Priority: 09/09/2010 JP 2010-202394 (73) Holder (s): NIPPON STEEL & SUMITOMO METAL CORPORATION (72) Inventor (s): TATSUHIKO SAKAI; HIDEYUKI HAMAMURA (85) National Phase Start Date: 05/03/2013
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    Descriptive Report of the Invention Patent for ORIENTED GRAIN ELECTRIC STEEL SHEET AND METHOD FOR MANUFACTURING THE SAME.
    FIELD OF TECHNIQUE [001] The present invention relates to a grain-oriented electrical steel plate that is suitable for a transformer iron core or the like and a method for manufacturing the grain-oriented electrical steel plate. Priority is claimed over Patent Application No. 2 JP 2010-202394 filed on September 9, 2010, the contents of which are incorporated by reference.
    BACKGROUND OF THE TECHNIQUE [002] As a technique for reducing iron loss from a grain-oriented electric steel plate, there is a technique for subdividing a magnetic domain by introducing a tension on the surface of a ferrite (Patent Document 3). However, in a coiled iron core, once the annealing for stress relief is performed in the manufacturing process, at the time of annealing, the tension introduced is relaxed and thus, the subdivision of the magnetic domain is not sufficient .
    [003] As a method of supplementing this deficiency, there is a technique for forming a groove on the surface of a ferrite (Patent Documents 1,2, 4 and 5). In addition, there is a technique for forming a groove on the surface of a ferrite and also for forming a crystal grain outline that varies from a bottom portion of the groove to the rear surface of the ferrite in a direction of thickness of the plate (Patent Document 6).
    [004] A method of forming a groove and a grain boundary has a highly improving effect on iron loss. However, in the technique set out in Patent Document 6, productivity is significantly reduced. This fact is due to the groove width being
    Petition 870180063173, of 07/23/2018, p. 10/42
    2/25 set to be in a range of 30 to 300 pm in order to achieve a desired effect and then fixing Sn or similar to the groove and annealing, adding a tension to the groove, or light radiation from laser, plasma or the like for heat treatment for the groove, is required for further formation of a crystal grain contour. That is, due to the fact that it is difficult to carry out the treatment such as the fixation of Sn, the addition of a voltage or the laser light radiation in exact conformity with a narrow groove and it is necessary to slow down the passage speed of the plate extremely, in order to carry them out. In Patent Document 6, an electrolytic grinding method is given as the groove forming method. However, in order to perform electrolytic roughing, it is necessary to apply a protective coating treatment for corrosion using a roughing solution, removing the protective coating and cleaning. For this reason, the number of processes and the treatment time increase significantly.
    CITATION LIST Patent Document [005] [Patent Document 1] Patent Application examined, Second Publication No. 2 JP S62-53,579.
    [006] [Patent Document 2] Patent Application examined, Second Publication No. 2 JP S62-54,873.
    [007] [Patent Document 3] Patent application not examined, First Publication No. 2 JP S56-51,528.
    [008] [Patent Document 4] Patent application not examined, First Publication No. 2 JP H6-57,335.
    [009] [Patent Document 5] Patent application not examined, First Publication No. 2 JP 2003-129.135.
    [0010] [Patent Document 6] Patent Application not examined, First Publication No. 2 JP H7-268,474.
    Petition 870180063173, of 07/23/2018, p. 11/42
    3/25 [0011] [Patent Document 7] Patent application not examined, First Publication No. 2 JP 2,000-109,961.
    [0012] [Patent Document 8] Unexamined Patent Application, First Publication No. 2 JP H9-49,024.
    [0013] [Patent Document 9] Patent Application not examined, First Publication No. 2 JP H9-268,322.
    SUMMARY OF THE INVENTION
    Technical Problem [0014] The present invention has an objective of providing a method of manufacturing a grain-oriented electric steel sheet, in which it is possible to mass-produce a grain-oriented electric steel sheet that has low iron loss and a grain-oriented electric steel plate that has low iron loss.
    Solution to the Problem [0015] In order to solve the problem above and thus achieve this goal, the present invention adopts the following measures.
    (1) That is, in accordance with an aspect of the present invention, a method of fabricating an electric grain-oriented steel sheet is provided which includes: a cold rolling process of performing a cold rolling while moving a sheet of silicon steel containing Si along a direction of passage of the sheet; a first continuous annealing process that causes decarbonisation and primary recrystallization of the silicon steel sheet; a winding process of winding the silicon steel sheet thereby obtaining a steel sheet coil; a process of forming the irradiation groove of a surface of the silicon steel sheet with a laser beam multiple times at predetermined intervals in the direction of passage of the sheet, along an area from one end edge to the other edge end,
    Petition 870180063173, of 07/23/2018, p. 12/42
    4/25 in a direction of the width of the sheet of the silicon steel sheet thus forming a groove along a location of the laser beam, during the period from the cold rolling process to the winding process; a batch annealing process that causes secondary recrystallization in the steel sheet coil; a second process of continuous annealing of unwinding and flattening the steel sheet coil; and a continuous process of voltage transmission coating and electrical insulation properties up to the surface of the silicon steel sheet, and in the batch annealing process, a crystal grain contour that penetrates the silicon steel sheet from from a front surface to the rear surface along the groove is generated and when an average laser beam intensity is set to be P (W), a focus diameter in the direction of passage of the plate from a focused point of the laser beam is set to be Dl (mm), a focus diameter in the direction of the plate width is set to be Dc (mm), a scan speed in the direction of the laser beam plate width is set to be Vc (mm / s), an Up radiation energy density of the laser beam is represented by the following Formula 1 and an instantaneous power density Ip of the laser beam is represented by the following Formula 2, following Formulas 3 and 4 are satisfied.
    Up = (4 / k) xP / (DIxVc) ... (Formula 1)
    Ip = (4 / 7i) xP / (DlxDc) ... (Formula 2) <Up <10 (J / mm2) ... (Formula 3)
    100 (kW / mm 2 ) <Ip <2,000 (kW / mm 2 ) ... (Formula 4) (2) In the aspect set out above (1), in the groove formation process, the gas can be blown into a portion of the silicon steel sheet that is irradiated with the laser beam, at a flow rate greater than or equal to 10 L / minute and less than or equal to 500 L / minute.
    Petition 870180063173, of 07/23/2018, p. 13/42
    5/25 (3) In accordance with another aspect of the present invention, a grain-oriented electrical steel plate is provided which includes: a groove formed from a laser beam site that has scanned over an area to from one end edge to the other end edge in a direction the width of the plate; and a crystal grain contour that extends along the groove and penetrates the grain electric steel plate oriented from a front surface to the rear surface.
    (4) In the aspect set out above (3), the grain-oriented electric steel sheet may additionally include a crystal grain, in which a grain diameter thereof in the direction of the width of the grain-oriented electric steel sheet is greater than or equal to 10 mm and less than or equal to a plate width and a grain diameter thereof in a longitudinal direction of the oriented grain electric steel sheet exceeds 0 mm and is 10 mm or less, in which the crystal grain it can be present until it varies from the groove to the rear surface of the grain-oriented electric steel plate.
    (5) In the aspect set out above (3) or (4), a glass coating can be formed in the groove and an X-ray intensity ratio Ir of a characteristic X-ray intensity of Mg in a portion of the groove in one case where an average value of the characteristic X-ray intensity of Mg of different portions that the groove portion of the surface of the grain-oriented electric steel plate is set to 1, in the glass coating, can be in a range of 0 < lr <0.9.
    Advantageous Effects of the Invention [0016] In accordance with the above aspects of the present invention, it is possible to obtain an electrical grain-oriented steel sheet that has low iron loss through a method in which it is possible to mass-produce the steel sheet grain oriented electrical.
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    BRIEF DESCRIPTION OF THE DRAWINGS [0017] Figure 1 is a diagram showing a method of manufacturing an electrical grain-oriented steel sheet related to a modality of the present invention.
    [0018] Figure 2 is a diagram showing a modified example of the embodiment of the present invention.
    [0019] Figure 3A is a diagram showing another example of a method of scanning a laser beam in the embodiment of the present invention.
    [0020] Figure 3B is a diagram showing another example of a method of scanning a laser beam in the embodiment of the present invention.
    [0021] Figure 4A is a diagram showing a focused point of a laser beam in the embodiment of the present invention.
    [0022] Figure 4B is a diagram showing the focused point of the laser beam in the embodiment of the present invention.
    [0023] Figure 5 is a diagram showing a groove and grains of crystal that are formed in the embodiment of the present invention. [0024] Figure 6A is a diagram showing crystal grain limits that are formed in the embodiment of the present invention.
    [0025] Figure 6B is a diagram showing the crystal grain limits that are formed in the embodiment of the present invention.
    [0026] Figure 7A is a diagram showing a photograph of the surface of a silicon steel sheet in the embodiment of the present invention.
    [0027] Figure 7B is a diagram showing a photograph of the surface of a sheet of silicon steel in the form of a comparative example.
    [0028] Figure 8A is a diagram showing another example of the crystal grain outline in the embodiment of the present invention.
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    7/25 [0029] Figure 8B is a diagram showing another example of the crystal grain outline in the embodiment of the present invention.
    DESCRIPTION OF THE MODALITIES [0030] Hereinafter, an embodiment of the present invention will be described with reference to the accompanying drawings. Figure 1 is a diagram showing a method of manufacturing an electrical grain oriented steel plate related to the embodiment of the present invention.
    [0031] In this modality, as shown in Figure 1, cold rolling is performed on a sheet of silicon steel 1 that contains, for example, 2% to 4% Si, in% by mass. The silicon steel sheet 1 is produced, for example, by continuous casting of cast steel, hot rolling of a plate obtained by continuous casting, annealing of a hot rolled steel sheet obtained by hot rolling and the like . The annealing temperature is about 1,100 ° C, for example. The thickness of the silicon steel sheet 1 after cold rolling is in a range of 0.2 mm to 0.3 mm, for example, and, for example, after cold rolling, the silicon steel sheet 1 it is wound in the form of a coil and maintained as a cold rolled coil.
    [0032] Subsequently, the coiled silicon steel sheet 1 is unwound and supplied to a decarburizing annealing furnace 3 and first continuous annealing, so called decarbonizing annealing is carried out in the annealing furnace 3. The temperature of this annealing is at a range of 700 ° C to 900 ° C, for example. At the time of this annealing, decarbonisation and primary recrystallization are caused. As a result, a crystal grain that has a Goss orientation, in which an easily magnetized geometric axis is aligned in a rolling direction, is formed with a certain degree of probability. After that, the steel sheet
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    8/25 silicon 1 discharged from the decarburization annealing furnace 3 is cooled by means of a cooling device 4. Subsequently, the application 5 of an annealing separating agent containing MgO with its main constituent, up to the surface of the silicon steel sheet 1 is made. Then, the silicon steel sheet 1 with the annealing separating agent applied to it is wound in the form of a coil and is thus transformed into a steel sheet coil 31.
    [0033] In this modality, during the period after the wound silicon steel sheet 1 is unrolled until the silicon steel sheet is supplied to the decarburization annealing furnace 3, a groove is formed on the surface of the steel sheet. silicon 1 through the use of a laser beam irradiation device 2. At that time, the irradiation of a laser beam from one end edge towards the other end edge, in a direction the width of the sheet metal plate of silicon steel 1, is performed multiple times at predetermined intervals in relation to a direction of passage of the plate, at the predetermined focus power density Ip and the predetermined focus energy density Up. As shown in Figure 2, a configuration is also possible in which, the laser beam irradiation device 2 is arranged to the side further downstream in the direction of passage of the plate than the cooling device 4 and the surface of the silicon steel sheet 1 is irradiated with a laser beam during the period after cooling through the cooling device 4 which is carried out until the application 5 of the annealing that separates the agent is carried out. A configuration is also possible in which the laser beam irradiation devices are arranged both to the side upstream in the direction of passage of the plate than the annealing furnace 3 and to the side further down in the direction of passage of the plate than the response device 870180063173, of 07/23/2018, p. 17/42
    9/25 cooling 4 and the irradiation of a laser beam is carried out in both locations. The irradiation of a laser beam can be carried out between the annealing furnace 3 and the cooling device 4 and can also be carried out in the annealing furnace 3 or in the cooling device 4. In the formation of the groove by the laser beam, different from a groove formation in machining, a molten layer that will be described later is produced. Since the molten layer does not disappear on decarburization or the like, even though laser irradiation is carried out in any process before secondary recrystallization, the effect of the same is obtained.
    [0034] For example, as shown in Figure 3A, a scanning device 10 scans a laser beam 9 emitted from a laser device that is a light source, at predetermined intervals PL in a C direction that it is the direction of the sheet width almost perpendicular to an L direction which is the lamination direction of the silicon steel sheet 1, through which the irradiation of the laser beam is carried out. At that time, the assist gas 25 such as air or inert gas is blown into a part that is irradiated with the laser beam 9 of the silicon steel sheet 1. As a result, a groove 23 is formed in an irradiated portion with the laser beam 9, from the surface of the silicon steel sheet 1. The lamination direction corresponds to the direction of passage of the sheet.
    [0035] Scanning the laser beam over the entire width of the silicon steel sheet 1 can also be performed by a single scanning device 10 and can also be performed by a plurality of scanning devices 20, as shown in Figure 3B. In one case, where the plurality of scanning devices 20 is used, only one laser device is a light source from a laser beam 19 that is incident on each scanning device.
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    10/25 scan 20 can also be provided and one can also be provided for each scanning device 20. In a case, where there is a light source, it is preferred that a laser beam emitted from the light source is divided into laser beams 19. Once it becomes possible to divide an irradiated area into a plurality of areas in the direction of the plate width through the use of the plurality of scanning devices 20, the scanning and irradiation times required by the laser beam are decreased. Therefore, it is particularly suitable for high-speed pass-through equipment.
    [0036] The laser beam 9 or 19 is focused by a lens on the scanning device 10 or 20. As shown in Figures 4A and 4B, the shape of a laser beam focused point 24 of the laser beam 9 or 19 on the surface of the silicon steel sheet 1 is, for example, a circular shape or an elliptical shape in which a diameter in the C direction which is the direction of the plate width is Dc and a diameter in the L direction which is the rolling direction is Dl. The scanning of the laser beam 9 or 19 is performed at a speed Vc using, for example, a polygonal mirror or similar on the scanning device 10 or 20. For example, the diameter Dc in the C direction which is the direction of the plate width can be set to be 0.4 mm and the diameter Dl in the L direction which is the lamination direction can be set to be 0.05 mm.
    [0037] As the laser device that is the light source, for example, a CO2 laser can be used. A high-powered laser that is generally used for industrial purposes, such as a YAG laser, a semiconductor laser, or a fiber laser can also be used. The laser that is used can also be any one of a pulsed laser and a continuous wave laser, provided so that the groove 23 and a crystal grain 26 are formed in a stable manner.
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    11/25 [0038] The temperature of the silicon steel sheet 1 when the laser beam is irradiated is not particularly limited. For example, irradiation of the laser beam can be performed in relation to the silicon steel sheet 1 below about room temperature. A scan direction of the laser beam does not have to correspond to the C direction which is the direction of the plate width. However, from the point of view of work efficiency or the like and subdivision of a magnetic domain in the form of long strips in the lamination direction, it is preferred that the angle between the scanning direction and the C direction which is the direction the plate width is 45 °. It is more preferred that the angle is 20 ° and even more preferred that the angle is 10 °. [0039] The instantaneous power density Ip and energy density of irradiation Up of the laser beam that are suitable for the formation of the slot 23 will be described. In this modality, for the reason described below, it is preferred that the peak power density, that is, the instantaneous power density Ip of the laser beam that is defined by Formula 2 satisfies Formula 4 and it is preferred that the density of Up irradiation energy of the laser beam that is defined by Formula 1 meets Formula 3.
    Up = (4 / k) xP / (DIxVc) ... (Formula 1)
    Ip = (4 / 7i) xP / (DlxDc) ... (Formula 2) <Up <10 J / mm 2 ... (Formula 3)
    100 kW / mm 2 <Ip <2,000 kW / mm 2 ... (Formula 4) [0040] Here, P represents the average intensity, that is, the power (W) of the laser beam, Dl represents the diameter (mm ) in the lamination direction of the laser beam's focused point, Dc represents the diameter (mm) in the direction of the laser beam's focused point plate width and Vc represents a sweep speed (mm / s) in the direction of the width of the laser beam. laser beam plate.
    [0041] If the silicon steel sheet 1 is irradiated with the laser beam
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    12/25
    9, an irradiated portion is melted and a portion thereof disperses or evaporates. As a result, groove 23 is formed. A portion of the molten portion that has not dispersed or evaporated remains as it is and is solidified after the end of the laser beam irradiation 9. At the moment of solidification, as shown in Figure 5, a columnar crystal that extends long towards the interior of the silicon steel sheet from the bottom of the groove, and / or a crystal grain that has a larger diameter compared to a non-irradiated laser portion, that is, crystal grain 26 that has a different shape than a grain crystal 27 obtained through primary recrystallization is formed. The crystal grain 26 becomes the starting point for the growth of the crystal grain limit at the time of secondary recrystallization.
    [0042] If the instantaneous power density Ip described above is less than 100 kW / mm 2 , it becomes difficult to sufficiently cause the melting and dispersion or evaporation of the silicon steel sheet 1. That is, it becomes if groove 23 is difficult to form. On the other hand, if the instantaneous power density Ip exceeds 2,000 kW / mm 2 , most of the molten steel disperses or evaporates and thus the crystal grain 26 is not easily formed. If the irradiation energy density Up exceeds 10 J / mm 2 , a molten portion of the silicon steel sheet 1 is increased and thus, the silicon steel sheet 1 is easily deformed. On the other hand, if the irradiation energy density is less than 1 J / mm 2 , the improvement in magnetic characteristics does not appear. For these reasons, it is preferred that Formulas 3 and 4 described above are satisfied.
    [0043] At the moment of irradiation of the laser beam, the assist gas 25 is blown in order to remove the dispersed or evaporated components of the silicon steel sheet 1, from an irradiation path of the laser beam 9. Since the laser beam 9 hits silicon steel sheet 1 steadily due to blowing, the groove 23 is formed
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    13/25 stable mode. In addition, the assist gas 25 is blown, whereby the re-fixing of the components to the silicon steel sheet 1 can be suppressed. In order to sufficiently obtain this effect, it is preferred that the flow rate of the assist gas 25 is greater than or equal to 10 L (liter) / minute. On the other hand, if the flow rate exceeds 500 L / minute, the effect is saturated and the cost also increases. For this reason, it is preferred that the upper limit is set to be 500 L / minute.
    [0044] The preferred conditions described above are also the same in a case where irradiation of the laser beam is performed between decarburization annealing and termination annealing and a case in which the irradiation of the laser beam is performed before and after decarburization annealing.
    [0045] Returning to the description using Figure 1, after application 5 of the annealing that separates the agent and the winding, as shown in Figure 1, the steel sheet coil 31 is transported to an annealing furnace 6 and placed with the central geometric axis of the sheet steel coil 31 which is almost in the vertical direction. Thereafter, batch annealing, i.e., the final annealing of the steel sheet coil 31, is carried out in a batch treatment. The highest batch annealing temperature to be achieved is set to be about 1,200 ° C, for example and a retention time is set to be about 20 hours, for example. At the time of batch annealing, secondary recrystallization is caused and also a glass coating is formed on the surface of the silicon steel sheet 1. After that, the steel sheet coil 31 is removed from the annealing furnace 6.
    [0046] In the glass coating obtained by the aspect described above, it is desired that an X-ray intensity ratio Ir of the characteristic X-ray intensity of Mg of a groove portion, in a case where
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    14/25 that the mean value of the characteristic X-ray intensity of Mg of different portions that the groove portion of the surface of a grain-oriented electric steel plate is set to be 1, is in a range of 0 <lr <0 , 9. If it is in the range, a favorable iron loss characteristic is obtained.
    [0047] The X-ray intensity ratio is obtained through measurement using a ΕΡΜΑ (microanalyzer with electron probe) or similar.
    [0048] Subsequently, the steel sheet coil 31 is unwound and supplied to an annealing furnace 7 and the second continuous annealing, so-called planar annealing, is carried out in the annealing furnace 7. At the time of the second continuous annealing, the stress deformation and the ripple generated at the time of final annealing are eliminated and thus, the silicon steel sheet 1 becomes flat. As the conditions of annealing, for example, retention of more than or equal to 10 seconds and less than or equal to 120 seconds can be performed at a temperature greater than or equal to 700 ° C and less than or equal to 900 ° C. Subsequently, coating 8 on the surface of the silicon steel sheet 1 is carried out. In coating 8, a material, in which it ensures the properties of electrical insulation and the action of tension to reduce the loss of iron is possible, is coated. A 32 grain oriented electric steel plate is produced through a series of these processes. After a coating is formed by the coating 8, for the convenience of, for example, storage, transportation and the like, the electric grain oriented steel sheet 32 is wound in the form of a coil. [0049] If the electric grain-oriented steel sheet 32 is produced by the method described above, at the time of secondary recrystallization, as shown in Figures 6A and 6B, a crystal grain contour 41 that penetrates the silicon steel sheet 1 from the
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    15/25 front surface to the rear surface along the groove 23 is formed. This is caused by the fact that the crystal grain 26 remains until the terminal phase of secondary recrystallization due to the crystal grain 26 is not easily corroded into a crystal grain that has a Goss orientation and that, despite the crystal grain 26 eventually being absorbed into the crystal grain that has a Goss orientation, at the moment, crystal grains that grow considerably from both sides of the groove 23 cannot corrode each other.
    [0050] In the oriented grain electric steel plate produced according to the modality described above, crystal grain limits shown in Figure 7A were observed. At the crystal grain boundaries, the crystal grain contour 41 formed along the groove has been included. In addition, on a grain-oriented electric steel plate produced according to the modality described above except that the laser beam irradiation is omitted, crystal grain limits shown in Figure 7B were observed.
    [0051] Figures 7A and 7B are photographs taken with etching of the surface of the electric grain-oriented steel sheet executed after the glass coating or similar is removed from the surface of the electric grain-oriented steel sheet and the ferrite is exposed. In these photographs, the crystal grains and the crystal grain limits obtained by secondary recrystallization appear.
    [0052] In the electric grain-oriented steel plate produced by the method described above, the effect of subdividing the magnetic domain is obtained by the grooves 23 formed on the surface of the ferrite. In addition, the magnetic domain subdivision effect is also obtained through the crystal grain boundaries 41 that penetrate the silicon steel sheet 1 from the front surface to the rear surface along the grooves 23. The loss of steel can be additionally reduced 870180063173, of 07/23/2018, p. 24/42
    16/25 due to its synergistic effect.
    [0053] Since the groove 23 is formed by the irradiation of a predetermined laser beam, the formation of the crystal grain contour 41 is very easy. That is, after the formation of the groove 23, it is not necessary to carry out the alignment or the like based on the position of the groove 23 for the formation of the crystal grain contour 41. Therefore, a significant decrease in the passing speed of the plate or similar does not it is necessary and thus, it is possible to mass-produce a grain-oriented electric steel plate.
    [0054] It is possible to perform the irradiation of the laser beam at high speed and the high energy density is obtained from the focus of light in a space of one minute. Therefore, even compared to a case in which the irradiation of a laser beam is not performed, an increase in the time required for treatment is small. That is, regardless of the presence or absence of the irradiation of a laser beam, it is almost not necessary to change a speed of passage of the plate in the treatment that performs decarburization annealing or similar, while a cold rolled coil is unrolled. In addition, since the temperature at which the irradiation of a laser beam is performed is not limited, a heat insulation mechanism or similar to a laser irradiation device is unnecessary. Therefore, compared to a case where treatment in a high temperature oven is necessary, the configuration of an appliance can be simplified.
    [0055] The depth of the slot 23 is not particularly limited. However, it is preferred that the depth is greater than or equal to 1 μηι and less than or equal to 30 μηι. If the depth of the slot 23 is less than 1 μηι, the subdivision of a magnetic domain is sometimes not enough. If the depth of groove 23 exceeds 30 μηι, the
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    17/25 amount of a silicon steel sheet that is a magnetic material, that is, the amount of a ferrite is reduced and the magnetic flux density is reduced. More preferably, the depth of the groove 23 is greater than or equal to 10 μιτι and less than or equal to 20 pm. The groove 23 can also be formed on only one surface of a sheet of silicon steel and can also be formed on both surfaces.
    [0056] The PL interval between slots 23 is not particularly limited. However, it is preferred that the PL interval is greater than or equal to 2 mm and less than or equal to 10 mm. If the PL gap is less than 2 mm, the inhibition of the formation of a magnetic flux through the groove becomes noticeable and it is difficult for the sufficiently high magnetic flux density required for a transformer to be formed. On the other hand, if the PL interval exceeds 10 mm, the effect of improving a magnetic characteristic through a groove and a grain contour is considerably reduced.
    [0057] In the embodiment described above, a crystal grain contour 41 is formed along a groove 23. However, for example, in a case where the width of the groove 23 is wide and the crystal grains 26 are removed along a wide strip in the lamination direction, at the time of secondary recrystallization, some of the crystal grains 26 sometimes grow before other crystal grains 26. In this case, as shown in Figures 8A and 8B, a plurality of crystal grains 53 each having a certain degree of width and along the groove 23 is formed below the grooves 23 in a direction of the thickness of the plate. It is acceptable if a grain diameter Wc1 in the lamination direction of crystal grain 53 exceeds 0 mm and the diameter of grain Wc1 becomes greater than or equal to, for example, 1 mm. However, the diameter of the Wc1 grain tends to become less than or equal to 10 mm. The reason that the grain diameter Wc1 tends to become
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    18/25 less than or equal to 10 mm is because a crystal grain that grows with the highest priority at the time of secondary recrystallization is a crystal grain 54 that has a Goss orientation and growth is impeded by the crystal grain 54. One crystal grain contour 51 approximately parallel to groove 23 is present between crystal grain 53 and crystal grain 54. crystal grain contour 52 is present between adjacent crystal grains 53. grain diameter Wcc in the direction of crystal grain plate width 53 tends to become greater than or equal to, for example, 10 mm. The crystal grain 53 can also be present as a single crystal grain in a wide direction along the width of the entire plate, in which case the crystal grain outline 52 must not be present. Regarding the grain diameter, for example, it can be measured using the following method. After the glass coating is removed and stripping is carried out to expose the ferrite, a field of view of 300 mm in the direction of lamination and 100 mm in the direction of the width of the plate is observed, the dimensions in the direction of lamination and the direction of the width of the crystal grain plate are measured by vision and image processing and the average value of the same is obtained. [0058] The crystal grain 53 that extends along the groove 23 is not necessarily a crystal grain that has a Goss orientation. However, since its size is limited, its influence on a magnetic characteristic is very small.
    [0059] In Patent Documents 1 to 9, a feature that a groove is formed through the irradiation of a laser beam is not established and additionally, a crystal grain boundary that extends along the groove is created at the moment secondary recrystallization, as described above. That is, even if the irradiation of a laser beam is established, since timing or similar irradiation is not appropriate, it is not
    Petition 870180063173, of 07/23/2018, p. 27/42
    19/25 possible to obtain the effects that are obtained in the modality described above.
    [Examples] (First Experiment) [0060] In a first experiment, hot rolling, annealing and cold rolling of a steel material for electrical oriented steel were performed, the thickness of the silicon steel sheet was set to be 0.23 mm and the silicon steel sheet has been rolled up and thus transformed into a cold rolled coil. Five cold rolled coils were produced. Subsequently, in relation to the three cold-rolled coils related to Examples N 22 1, 2 and 3, the groove formation through the laser beam irradiation was performed and after that, a decarburization annealing was performed, thus causing the primary recrystallization. The laser beam irradiation was performed using a fiber laser. In all examples, the power P was 2,000 W and in relation to a focused format, in Examples N 22 1 and 2, the diameter Dl in the L direction was 0.05 mm and the diameter Dc in the C direction was 0.4 mm . In relation to Example n 2 3, the diameter Dl in the L direction was 0.04 mm and the diameter Dc in the C direction was 0.04 mm. The sweep speed Vc was set to be 10 m / s in Examples N 22 1 and 3 and 50 m / s in Example n 2 2. Therefore, the instantaneous power density Ip was 127 kW / mm 2 in Examples N 22 1 and 2 and 1,600 kW / mm 2 in Example n 2 3. The irradiation energy density Up was 5.1 J / mm 2 in Example n 2 1, 1.0 J / mm 2 in Example n 2 2 and 6, 4 J / mm 2 in Example n 2 3. The irradiation step PL was set to be 4 mm and the air was blown at a flow rate of 15 L / minute as the assist gas. As a result, the width of the groove formed was about 0.06 mm, that is, 60 pm in Examples N 22 1 and 3 and 0.05 mm, that is, 50 pm in Example n 2 2. The depth of the groove was about 0.02 mm, that is, 20 pm in Example n 2 1, 3 pm in Example n 2 2 and 30 pm in
    Petition 870180063173, of 07/23/2018, p. 28/42
    20/25
    Example η 2 3. The variation in width was ± 5 pm and the variation in depth was ± 2 pm.
    [0061] In relation to another cold rolled coil related to Comparative Example No. 2 1, the formation of a groove through roughing was performed and after that, decarburization annealing was performed thereby causing primary recrystallization. The shape of this groove was made to have the same shape as the groove in Example No. 2 formed by the irradiation of the laser beam described above. Regarding the permanence of a cold rolled coil related to Comparative Example n 2 2, the formation of a groove was not performed and after that, decarburization annealing was performed, thus causing primary recrystallization.
    [0062] In all Examples N 22 1 to 3 and in Comparative Example Nos. 1 and 2, after decarburizing annealing, the application of an annealing separating agent, final annealing, planar annealing and coating are carried out on the silicon steel sheets. In this way, five types of grain-oriented electric steel sheets were produced.
    [0063] When the structures of these electric oriented steel sheets were observed, in all Examples N 22 1 to 3 and Comparative Example Nos. 1 and 2, the secondary recrystallized grains formed by the secondary recrystallization were present. In Examples N 22 1 to 3, similarly to the crystal grain outline 41 shown in Figure 6A or 6B, the crystal grain outline along the groove was present. However, in Comparative Example Nos. 1 and 2, such a crystal grain contour was not present.
    [0064] Thirty single sheets, each having a length in the rolling direction of 300 mm and a length in the direction of the width of the sheet of 60 mm were sampled from each of the grain-oriented electric steel sheets respectively and O
    Petition 870180063173, of 07/23/2018, p. 29/42
    21/25 the mean value of the magnetic characteristics was measured by a single method of plate magnetometry (SST: Single Plate Test). The measurement method was carried out in accordance with IEC60404-3: 1982. As the magnetic characteristics, the magnetic flux density Be (T) and loss of iron W17 / 50 (W / kg) were measured. The magnetic flux density Be is the magnetic flux density that is generated in an electric grain steel sheet oriented at a magnetizing force of 800 A / m. Since the higher the value of the magnetic flux density Be of an electrical grain-oriented steel plate, the greater the magnetic flux density that is generated in a given magnetizing force, the electrical grain-oriented steel plate in which the value of the Beé large magnetic flux density, it is suitable for a small efficient transformer. The loss of iron W17 / 50 is loss of iron when an electrical grain-oriented steel plate is subjected to alternating current energization under conditions where the maximum magnetic flux density is 1.7 T and the frequency is 50 Hz. The lower the value of the W17 / 50 iron loss of a grain-oriented electric steel plate, the greater the energy loss and thus, the grain-oriented electric steel plate in which the value of the W17 / 50 iron loss is small , is suitable for a transformer. The average value of each of the magnetic flux density Be (T) and the loss of iron W17 / 50 (W / kg) is shown in Table 1 below. Additionally, in relation to the single plate samples described above, the measurement of the X-ray intensity ratio Ir was performed using uso. Each average value is shown together in Table 1 below.
    Table 1
    Average value of B 8 (T) Average value ofWi7 / 5o (W / kg) Average Ir value Example n 2 1 1.89 0.74 0.5 Example n 2 2 1.90 0.76 0.9
    Petition 870180063173, of 07/23/2018, p. 30/42
    22/25
    Example n 2 3 1.87 0.75 0.1 Comparative Example n 2 1 1.88 0.77 1.0 Comparative Example n 2 2 1.91 0.83 1.0
    [0065] As shown in Table 1, in Examples N 22 1 to 3, compared to Comparative Example n 2 2, the magnetic flux density Be was low with the formation of the groove. However, once the groove and the crystal grain outline along the groove were present, the iron loss was significantly low. In Examples No. 22 1 to 3, even compared to Comparative Example No. 2 1, since the crystal grain contour along the groove was present, the loss of iron was low.
    (Second Experiment) [0066] In a second experiment, the verification in relation to the irradiation conditions of the laser beam was performed. Here, laser beam irradiation was performed under four types of conditions described below.
    [0067] In a first condition among the four types of conditions, a continuous wave fiber laser was used. The power P was set to be 2,000 W, the diameter Dl in the L direction was set to be 0.05 mm, the diameter Dc in the C direction was set to be 0.4 mm and the sweep speed Vc was set to be 5 m / s. Therefore, the instantaneous power density Ip was 127 kW / mm 2 and the irradiation energy density Up was 10.2 J / mm 2 . That is, compared to the conditions of the first experiment, the scanning speed was reduced by half and thus, the energy density of irradiation Up was doubled. Therefore, the first condition does not satisfy Formula 3. As a result, the warping deformation of the steel sheet was generated with an irradiated portion as the starting point. Once a warping angle reached a range of 3 ° to 10 °, winding in the form of a coil was difficult.
    Petition 870180063173, of 07/23/2018, p. 31/42
    23/25 [0068] In addition, in a second condition, a continuous wave fiber laser was used. In addition, the power P was set to be 2,000 W, the diameter Dl in the L direction was set to be 0.10 mm, the diameter Dc in the C direction was set to be 0.3 mm and the sweep speed Vc was set to be 10 m / s. Therefore, the instantaneous power density Ip was 85 kW / mm 2 and the irradiation energy density Up was 2.5 J / mm 2 . That is, compared to the conditions of the first experiment, the diameter Dl in the L direction and the diameter Dc in the C direction were changed and thus, the instantaneous power density Ip was defined to be small. The second condition does not satisfy Formula 4. As a result, it was difficult to form a grain boundary that could penetrate.
    [0069] In addition, in a third condition, a continuous wave fiber laser was used. The power P was set to be 2,000 W, the diameter Dl in the L direction was set to be 0.03 mm, the diameter Dc in the C direction was set to be 0.03 mm and the sweep speed Vc was set to be 10 m / s. Therefore, the instantaneous power density Ip was 2800 kW / mm 2 and the irradiation energy density Up was 8.5 J / mm 2 . That is, the diameter Dl in the L direction was defined to be smaller than in the condition of the first experiment and thus, the instantaneous power density Ip was defined to be large. Therefore, the third condition also does not satisfy Formula 4. As a result, it was difficult to sufficiently form a crystal grain contour along the groove.
    [0070] In addition, in a fourth condition, a continuous wave fiber laser was used. The power P was set to be 2,000 W, the diameter Dl in the L direction was set to be 0.05 mm, the diameter Dc in the C direction was set to be 0.4 mm and the sweep speed Vc was set to be 60 m / s. Therefore, the instantaneous power density Ip was 127 kW / mm 2 and the irradiation energy density Up
    Petition 870180063173, of 07/23/2018, p. 32/42
    24/25 was 0.8 J / mm 2 . That is, the sweep speed was set to be higher than in the condition of the first experiment and thus, the radiation energy density Up was set to be small. The fourth condition does not satisfy Formula 3. As a result, in the fourth condition, it was difficult to form a groove that has a depth greater than or equal to 1 pm.
    (Third Experiment) [0071] In a third experiment, the laser beam irradiation was performed under two sets of conditions, a condition in which the flow rate of the assist gas was set to be less than 10 L / minute and a condition where the assist gas is not supplied. As a result, it was difficult to stabilize the groove depth, the variation in the groove width was greater than or equal to the range of ± 10 pm and the variation in depth was greater than or equal to a range of ± 5 pm. For this reason, the variation in magnetic characteristics was large compared to the examples.
    Industrial Applicability [0072] In accordance with an aspect of the present invention, a grain-oriented electric steel sheet that has low iron loss can be obtained by a method in which it is possible to mass-produce the grain-oriented electric steel sheet .
    REFERENCE LISTING
    1: silicon steel sheet
    2: laser beam irradiation device
    3, 6, 7: annealing furnace
    31: steel sheet coil
    32: grain-oriented electric steel sheet
    9.19: let laser
    10, 20: scanning device
    23: slot
    Petition 870180063173, of 07/23/2018, p. 33/42
    25/25
    24: laser beam focused point 25: service gas 26, 27, 53, 54: crystal grain 41,51, 52: crystal grain outline
    Petition 870180063173, of 07/23/2018, p. 34/42
    1/3
    权利要求:
    Claims (5)
    [1]
    1. Method of manufacturing a grain-oriented electric steel plate, characterized by the fact that it comprises:
    a cold rolling process to perform a cold rolling while moving a silicon steel sheet containing Si along a direction of passage of the sheet;
    a first continuous annealing process that causes decarbonisation and primary recrystallization of the silicon steel sheet;
    a winding process of winding the silicon steel sheet thereby obtaining a steel sheet coil;
    a process of forming the irradiation groove of a surface of the silicon steel sheet with a laser beam multiple times at predetermined intervals in the direction of passage of the sheet, along an area from one end edge to the other edge end, in a direction of the width of the sheet of the silicon steel sheet thereby forming a groove along a location of the laser beam, during the period from the cold rolling process to the winding process;
    a batch annealing process that causes secondary recrystallization in the steel sheet coil;
    a second process of continuous annealing of unwinding and flattening the steel sheet coil; and a continuous process of coating a transmission of voltage and electrical insulating properties to the surface of the silicon steel sheet, in which in the batch annealing process, a crystal grain contour that penetrates the silicon steel sheet from a front surface to a rear surface along the groove is generated, and
    Petition 870180063173, of 07/23/2018, p. 35/42
    [2]
    2/3 when an average laser beam intensity is set to be P (W), a focus diameter in the direction of passage of the plate from a focused point of the laser beam is set to be Dl (mm), a diameter of focus in the direction of the plate width is set to be Dc (mm), a sweep speed in the direction of the laser beam plate width is set to be Vc (mm / s), an irradiation energy density Up of the beam of laser is represented by the following Formula 1 and an instantaneous power density Ip of the laser beam is represented by the following Formula 2, following Formulas 3 and 4 are satisfied
    Up = (4 / k) xP / (DIxVc) ... (Formula 1)
    Ip = (4 / k) xP / (DIxDc) ... (Formula 2)
    1 <Up <10 (J / mm 2 ) ... (Formula 3)
    100 (kW / mm 2 ) <Ip <2,000 (kW / mm 2 ) ... (Formula 4).
    2. Method of manufacturing a grain-oriented electric steel sheet according to claim 1, characterized by the fact that in the groove formation process, the gas is blown into a portion of the silicon steel sheet, which is irradiated with the laser beam, at a flow rate greater than or equal to 10 L / minute and less than or equal to 500 L / minute.
    [3]
    3. Electric grain-oriented steel plate, characterized by the fact that it comprises:
    a groove formed from a location on a laser beam that scanned over an area from one end edge to the other end edge in a direction the width of the plate; and a crystal grain contour that extends along the groove and penetrates the electrical grain steel sheet oriented from a front surface to a rear surface.
    [4]
    4. Oriented grain electric steel plate, according to
    Petition 870180063173, of 07/23/2018, p. 36/42
    3/3 to claim 3, characterized by the fact that it additionally comprises a crystal grain in which a grain diameter of the same in the direction of the width of the sheet of the oriented grain electric steel plate is greater than or equal to 10 mm and smaller or equal to a plate width and a grain diameter thereof in a longitudinal direction of the oriented grain electric steel sheet exceeds 0 mm and is 10 mm or less, in which the crystal grain is present up to a range from the groove to the rear surface of the grain-oriented electric steel plate.
    [5]
    5. Electric grain-oriented steel sheet according to claim 3 or 4, characterized by the fact that a glass coating is formed in the groove and an X-ray intensity ratio Ir of a characteristic X-ray intensity of Mg in a portion of the groove in a case where an average value of the characteristic X-ray intensity of Mg from different portions of the groove portion of the surface of the grain-oriented electric steel plate is set to 1, in the glass coating, is in a range of 0 <lr <0.9.
    Petition 870180063173, of 07/23/2018, p. 37/42
    1/8
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    引用文献:
    公开号 | 申请日 | 公开日 | 申请人 | 专利标题
    JPS5826406B2|1979-10-03|1983-06-02|Nippon Steel Corp|
    US4645547A|1982-10-20|1987-02-24|Westinghouse Electric Corp.|Loss ferromagnetic materials and methods of improvement|
    JPS6253579B2|1984-11-10|1987-11-11|Nippon Steel Corp|
    SE465129B|1984-11-10|1991-07-29|Nippon Steel Corp|CORN-ORIENTED STEEL TUNNER PLATE FOR LOW WATER LOSS ELECTRICITY AFTER RELAXATION GLOVES AND PROCEDURE FOR PREPARATION OF THE PLATE|
    JPS6253579A|1985-09-03|1987-03-09|Seiko Epson Corp|Portable receiver|
    JPS6254873A|1985-09-03|1987-03-10|Sanyo Electric Co Ltd|Fixed-head type digital magnetic reproducing device|
    JPS6396216A|1986-10-11|1988-04-27|Nippon Steel Corp|Production of grain oriented electrical steel sheet having high adhesiveness of glass film and excellent iron loss characteristic|
    JPH0379722A|1989-08-21|1991-04-04|Kawasaki Steel Corp|Manufacture of grain oriented silicon steel sheet having excellent magnetic characteristics|
    JP2563729B2|1992-08-07|1996-12-18|新日本製鐵株式会社|Method and apparatus for improving iron loss of grain-oriented electrical steel sheet using pulsed CO2 laser|
    KR960010595B1|1992-09-21|1996-08-06|신니뽄세이데스 가부시끼가이샤|Production of grain-oriented silicon steel sheet having no glass coating and excellent in iron loss|
    JP3726289B2|1994-03-31|2005-12-14|Ｊｆｅスチール株式会社|Oriented electrical steel sheet with low iron loss|
    JP3369724B2|1994-05-27|2003-01-20|川崎製鉄株式会社|Grain-oriented electrical steel sheet with low iron loss|
    JP3393218B2|1995-08-08|2003-04-07|新日本製鐵株式会社|Manufacturing method of low iron loss unidirectional electrical steel sheet|
    JP3470475B2|1995-11-27|2003-11-25|Ｊｆｅスチール株式会社|Grain-oriented electrical steel sheet with extremely low iron loss and its manufacturing method|
    JPH09268322A|1996-02-02|1997-10-14|Nippon Steel Corp|Production of grain oriented silicon steel sheet with ultralow iron loss|
    EP0837148B1|1996-10-21|2001-08-29|Kawasaki Steel Corporation|Grain-oriented electromagnetic steel sheet|
    JP4319715B2|1998-10-06|2009-08-26|新日本製鐵株式会社|Unidirectional electrical steel sheet with excellent magnetic properties and manufacturing method thereof|
    IT1306157B1|1999-05-26|2001-05-30|Acciai Speciali Terni Spa|PROCEDURE FOR THE IMPROVEMENT OF MAGNETIC CHARACTERISTICS OF SILICON STEEL GRAIN STEEL ORIENTED BY TREATMENT|
    JP4331900B2|2001-03-30|2009-09-16|新日本製鐵株式会社|Oriented electrical steel sheet and method and apparatus for manufacturing the same|
    JP4189143B2|2001-10-22|2008-12-03|新日本製鐵株式会社|Low iron loss unidirectional electrical steel sheet manufacturing method|
    RU2298592C2|2002-03-28|2007-05-10|Ниппон Стил Корпорейшн|Electrical-sheet steel with oriented grains possessing high adhesion of film and method of making such steel|
    EP1607487B1|2003-03-19|2016-12-21|Nippon Steel & Sumitomo Metal Corporation|Manufacturing method of a grain-oriented magnetic steel sheet excellent in magnetic characteristics|
    TWI305548B|2005-05-09|2009-01-21|Nippon Steel Corp|Low core loss grain-oriented electrical steel sheet and method for producing the same|
    CN101946017B|2008-02-19|2013-06-05|新日铁住金株式会社|Method of manufacturing low core loss grain-oriented electrical steel plate|
    JP4782248B1|2010-07-28|2011-09-28|新日本製鐵株式会社|Oriented electrical steel sheet and manufacturing method thereof|JP4660402B2|2006-03-16|2011-03-30|株式会社リコー|Non-magnetic toner for electrostatic image development|
    DE102011000712A1|2011-02-14|2012-08-16|Thyssenkrupp Electrical Steel Gmbh|Method for producing a grain-oriented flat steel product|
    US8900688B2|2011-05-27|2014-12-02|Nippon Steel & Sumitomo Metal Corporation|Grain oriented electrical steel sheet and method of producing grain oriented electrical steel sheet|
    BR112014025281B1|2012-04-27|2019-06-18|Nippon Steel & Sumitomo Metal Corporation|MAGNETIC STEEL SHEET WITH ORIENTED GRAIN AND METHOD FOR PRODUCING THE SAME|
    RU2604550C1|2012-11-26|2016-12-10|Ниппон Стил Энд Сумитомо Метал Корпорейшн|Oriented-grain electric steel sheet and method of producing oriented-grain electrical steel sheet|
    CN105451902B|2013-07-24|2018-08-24|Posco公司|Oriented electrical steel and its manufacturing method|
    TWI499776B|2014-05-23|2015-09-11|China Steel Corp|Method for measuring deterioration of an electromagnetic steel sheet and measure machine using the same|
    CN106471141B|2014-07-03|2019-02-01|新日铁住金株式会社|Laser processing device|
    KR101562962B1|2014-08-28|2015-10-23|주식회사 포스코|Method and appratus for refining magnetic domains in grain-oriented electrical steel sheet and grain-oriented electrical steel manufactured using the same|
    KR101676628B1|2014-12-24|2016-11-16|주식회사 포스코|Grain-orientied electrical steel sheet and method for manufacturing the same|
    KR101650400B1|2014-12-24|2016-08-23|주식회사 포스코|Method for refining magnetic domain of oriented electrical steel, amd the device|
    US10434606B2|2015-04-20|2019-10-08|Nippon Steel Corporation|Grain-oriented electrical steel sheet|
    KR102008600B1|2015-04-20|2019-08-07|닛폰세이테츠 가부시키가이샤|Directional electronic steel sheet|
    RU2682363C1|2015-04-20|2019-03-19|Ниппон Стил Энд Сумитомо Метал Корпорейшн|Electrical steel sheet with oriented grain structure|
    JP6455593B2|2015-04-20|2019-01-23|新日鐵住金株式会社|Oriented electrical steel sheet|
    WO2017017908A1|2015-07-28|2017-02-02|Ｊｆｅスチール株式会社|Linear groove forming method and linear grooves forming apparatus|
    CN105185503B|2015-09-24|2018-01-19|国网智能电网研究院|A kind of electrical sheet sheet material and preparation method thereof|
    CN106944743B|2015-10-08|2020-01-03|诺威科技集团有限公司|Method and apparatus for forming fine permanent magnetic regions of electric steel sheet by laser beam|
    CN105463172A|2015-12-14|2016-04-06|武汉钢铁公司|Method for improving magnetic performance of silicon steel sheet through laser indented oriented silicon steel cold-rolled sheet|
    DE102016208131B4|2015-12-18|2021-10-07|Fraunhofer-Gesellschaft zur Förderung der angewandten Forschung e.V.|Method and device for machining a workpiece|
    KR101751525B1|2015-12-24|2017-07-11|주식회사 포스코|Grain oriented electrical steel sheet and method for manufacturing the same|
    CN108699616A|2015-12-30|2018-10-23|Posco公司|The magnetic domain thinning method and its device of oriented electrical steel sheets|
    KR101739868B1|2016-01-22|2017-05-25|주식회사 포스코|Method and apparatus for refining magnetic domains grain-oriented electrical steel|
    KR101739865B1|2016-01-22|2017-05-25|주식회사 포스코|Method and apparatus for refining magnetic domains grain-oriented electrical steel|
    KR101739866B1|2016-01-22|2017-05-25|주식회사 포스코|Method and apparatus for refining magnetic domains grain-oriented electrical steel|
    JP6569803B2|2016-03-31|2019-09-04|日本製鉄株式会社|Oriented electrical steel sheet|
    CN108660303B|2017-03-27|2020-03-27|宝山钢铁股份有限公司|Stress-relief-annealing-resistant laser-scored oriented silicon steel and manufacturing method thereof|
    CN108660295A|2017-03-27|2018-10-16|宝山钢铁股份有限公司|A kind of low iron loss orientation silicon steel and its manufacturing method|
    US20210082606A1|2018-01-31|2021-03-18|Nippon Steel Corporation|Grain-oriented electrical steel sheet|
    CN110093486B|2018-01-31|2021-08-17|宝山钢铁股份有限公司|Manufacturing method of low-iron-loss oriented silicon steel resistant to stress relief annealing|
    CN110323044B|2018-03-30|2021-02-19|宝山钢铁股份有限公司|Heat-resistant magnetic domain refining type oriented silicon steel and manufacturing method thereof|
    KR20210080085A|2019-12-20|2021-06-30|주식회사 포스코|Grain oriented electrical steel sheet and method for refining magnetic domains therein|
    法律状态:
    2018-04-24| B07A| Application suspended after technical examination (opinion) [chapter 7.1 patent gazette]|
    2018-08-28| B09A| Decision: intention to grant [chapter 9.1 patent gazette]|
    2018-10-23| B16A| Patent or certificate of addition of invention granted [chapter 16.1 patent gazette]|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 09/09/2011, OBSERVADAS AS CONDICOES LEGAIS. |
    2019-11-26| B25D| Requested change of name of applicant approved|Owner name: NIPPON STEEL CORPORATION (JP) |
    优先权:
    申请号 | 申请日 | 专利标题
    JP2010202394|2010-09-09|
    JP2010-202394|2010-09-09|
    PCT/JP2011/070607|WO2012033197A1|2010-09-09|2011-09-09|Oriented electromagnetic steel sheet and process for production thereof|
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