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    • 专利摘要:
    UNORIENTED MAGNETIC STEEL SHEET AND METHOD OF PRODUCTION THEREOF. An unoriented magnetic steel sheet includes a specific chemical composition represented, in % by mass, by: Si: 3.0% to 3.6%; Al: 0.50% to 1.25%; Mn: 0.5% to 1.5%; Sb or Sn or both of them: [Sb] + [Sn] / 2 is 0.0025% to 0.05% where [Sb] denotes an Sb content and [Sn] denotes an Sn content; P: 0.010% to 0.150%; Ni: 0.010% to 0.200%; C: 0.0010% to 0.0040%; and others. The thickness of the unoriented magnetic steel sheet is 0.15mm to 0.30mm, the unoriented magnetic steel sheet includes magnetic properties shown, where t denotes the thickness (mm) of the unoriented magnetic steel sheet, per: B50 magnetic flux density: "0.2 xt + 1.52" T or more; a magnetic flux density difference (Delat)B50: 0.08T or less; W10/50 core loss: 0.95 W/kg or less; and W10/400 core loss: "20 x t + 7.5" w/kg or less. The ratio of a number of intergranular grain carbides to the sum of the number of intergranular carbides and the number of grain edge carbides precipitated at the grain edges is 0.50 or less.
    公开号:BR112016028787B1
    申请号:R112016028787-8
    申请日:2015-07-02
    公开日:2021-05-25
    发明作者:Kenichi Murakami；Yoshiaki Natori；Takuya Matsumoto；Hiroki HORI；Takeaki Wakisaka
    申请人:Nippon Steel Corporation；
    IPC主号:
    专利说明:

    technical field
    [0001] The present invention relates to a non-oriented magnetic steel sheet and a method of production thereof. Background
    [0002] Unoriented magnetic steel plates are used for various motors. For example, unoriented magnetic steel sheets are used for compressors in an air conditioner and refrigerator, and motors in an electric vehicle and a hybrid vehicle. The compressors of air conditioners and refrigerators are driven in inverter mode, and therefore reducing the core loss at a commercial frequency (50 Hz and 60 Hz) and reducing the core loss at a high frequency (100 Hz at 1000 Hz) are important to improve efficiency. The rotation speed of an automobile's engine changes according to the automobile's traveling speed. In addition, a high engine torque is required when the car starts.
    [0003] In consideration of the above, a high magnetic flux density, low core loss at commercial frequency, and low core loss at high frequency (hereinafter it is sometimes called "high frequency core loss ") are required for unoriented magnetic steel sheet. Furthermore, a motor core is roughly classified into an integral type and a separate type, and the motor core of the integral type is mainly used, and therefore isotropic magnetic properties are required. However, a conventional unoriented magnetic steel sheet cannot satisfy these requirements. List of quotes Patent Literatures
    [0004] Patent Literature 1: Japanese Patent Publication Open to Public Inspection No. 2010-185119
    [0005] Patent Literature 2: Japanese Patent Publication Open to Public Inspection No. 2003-213385
    [0006] Patent Literature 3: Japanese Patent Publication Open to Public Inspection No. 2013-91837
    [0007] Patent Literature 4: Japanese Patent Publication Open to Public Inspection No. 2007-162096
    [0008] Patent Literature 5: Japanese Patent Publication Open to Public Inspection No. H7-188752
    [0009] Patent Literature 6: Japanese Patent Publication Open to Public Inspection No. 2013-44010 Invention Summary Technical problem
    [00010] An objective of the present invention is to provide an unoriented magnetic steel sheet capable of achieving high magnetic flux density, low core loss at commercial frequency, low core loss at high frequency and isotropic magnetic properties, and a method of producing it. Solution to problem
    [00011] The present inventors have studied hard to solve the problems mentioned above. As a result, it was found that Sb or Sn, or both, are contained in adequate amounts, and P, Ni, and C are contained in adequate amounts, the plate thickness being small, etc., are important points to achieve the high magnetic flux density, low core loss at commercial frequency, and low core loss at high frequency.
    [00012] The present inventors have arrived at the various modes of the invention described below by other serious studies based on the knowledge cited above. (1)
    [00013] An unoriented magnetic steel sheet including: a chemical composition represented, in % by mass, by:
    [00014] Si: 3.0% to 3.6%;
    [00015] Al: 0.50% to 1.25%;
    [00016] Mn: 0.5% to 1.5%;
    [00017] Sb or Sn or both: [Sb] + [Sn] / 2 is 0.0025% to 0.05% where [Sb] denotes the Sb content and [Sn] denotes the Sn content;
    [00018] P: 0.010% to 0.150%;
    [00019] Ni: 0.010% to 0.200%;
    [00020] C: 0.0010% to 0.0040%;
    [00021] N: 0.0030% or less;
    [00022] S: 0.0020% or less;
    [00023] Ti: 0.0030% or less;
    [00024] Cu: 0.0500% or less;
    [00025] Cr: 0.0500% or less;
    [00026] Mo: 0.0500% or less;
    [00027] Bi: 0.0050% or less;
    [00028] Pb: 0.0050% or less;
    [00029] V: 0.0050% or less;
    [00030] B: 0.0050% or less; and
    [00031] balance: Fe and impurities, and
    [00032] magnetic properties represented by, where t denotes the thickness (mm) of the unoriented magnetic steel sheet:
    [00033] a magnetic flux density B50: "0.2 x t + 1.52" T or more;
    [00034] a magnetic flux density difference ΔB50: 0.08T or less;
    [00035] W10/50 core loss: 0.95 W/kg or less; and
    [00036] W10/400 core loss: "20 x t + 7.5" W/kg or less,
    [00037] where and
    [00038] the thickness is 0.15 mm to 0.30 mm, and
    [00039] the ratio of the number of intergranular carbides precipitated in grains in relation to the sum of the number of intergranular carbides and the number of grain edge carbides precipitated in the grain edges is 0.50 or less. (two)
    [00040] The magnetic steel sheet not oriented according to item (1) where, in the chemical composition,
    [00041] P: 0.015% to 0.100%,
    [00042] Ni: 0.020% to 0.100%, or
    [00043] C: 0.0020% to 0.0030%, or
    [00044] any one of their combinations is satisfied. (3)
    [00045] A method of producing an unoriented magnetic steel sheet, including:
    [00046] hot rolling a steel material to obtain a hot rolled steel sheet;
    [00047] cold-rolling the hot-rolled steel sheet to obtain a cold-rolled steel sheet;
    [00048] perform the first annealing of the hot rolled steel sheet before the cold rolling is completed; and
    [00049] perform the second annealing of the cold rolled steel sheet,
    [00050] where the first annealing includes:
    [00051] retain the hot rolled steel sheet in a first temperature range of 850°C to 1100°C for 10 seconds to 120 seconds, and
    [00052] after retention, cool the hot rolled steel sheet at a rate of 5°C/s to 50°C/s in a temperature zone of 850°C to 600°C,
    [00053] where the second annealing includes:
    [00054] retain the cold rolled steel sheet in a second temperature range of 900°C to 1100°C for 10 seconds to 240 seconds, and
    [00055] after holding, cool the cold rolled steel sheet at a rate of 10°C/s to 40°C/s in a temperature zone of 900°C to 300°C, and
    [00056] where the steel material includes a chemical composition represented, in % by mass, by:
    [00057] Si: 3.0% to 3.6%;
    [00058] Al: 0.50% to 1.25%;
    [00059] Mn: 0.5% to 1.5%;
    [00060] Sb or Sn or both of them: [Sb] + [Sn] / 2 is 0.0025% to 0.05% where [Sb] denotes an Sb content and [Sn] denotes an Sn content;
    [00061] P: 0.010% to 0.150%;
    [00062] Ni: 0.010% to 0.200%;
    [00063] C: 0.0010% to 0.0040%;
    [00064] N: 0.0030% or less;
    [00065] S: 0.0020% or less;
    [00066] Ti: 0.0030% or less;
    [00067] Cu: 0.0500% or less;
    [00068] Cr: 0.0500% or less;
    [00069] Mo: 0.0500% or less;
    [00070] Bi: 0.0050% or less;
    [00071] Pb: 0.0050% or less;
    [00072] V: 0.0050% or less;
    [00073] B: 0.0050% or less; and
    [00074] balance: Fe and impurities. (4)
    [00075] The non-oriented magnetic steel sheet production method according to item (3), where the annealing of the hot rolled sheet is performed as the first annealing before the cold rolling. (5)
    [00076] The production method of the unoriented magnetic steel sheet according to item (3), also including annealing the hot rolled sheet before cold rolling, where an intermediate annealing is performed as the first annealing during the rolling to cold. (6)
    [00077] The method of production of magnetic steel sheet not oriented according to any of items (3) to (5) where, in the chemical composition,
    [00078] P: 0.015% to 0.100%,
    [00079] Ni: 0.020% to 0.100%, or
    [00080] C: 0.0020% to 0.0030%, or
    [00081] any one of their combinations is satisfied. (7)
    [00082] The method of producing magnetic steel sheet not oriented according to any of the items (3) to (6), where the thickness of the cold rolled steel sheet is 0.15 mm to 0.30 mm. Advantageous Effects of the Invention
    [00083] According to the present invention, it is possible to obtain excellent magnetic properties because the chemical composition, the ratio of the number of intergranular carbides precipitated in the grains in relation to the sum of the number of intergranular carbides and the number of carbides at the edges of the precipitated grains at the edges of the grains, etc. are adequate. Description of modalities
    [00084] Hereinafter, embodiments of the present invention are described.
    [00085] Initially, the chemical composition of a non-oriented magnetic steel sheet according to an embodiment of the present invention and a steel material used to produce the same is described. The unoriented magnetic steel sheet according to the embodiment of the present invention is produced by hot rolling a steel material, annealing the hot rolled sheet, cold rolling, cold annealing, etc., the details of which will be described later on . Consequently, the chemical compositions of the unoriented magnetic steel sheet and the steel material are suitable for the processes mentioned above in addition to the properties of the unoriented magnetic steel sheet. In the following description, the sign "%" which is the unit of the content of each element contained in the unoriented magnetic steel sheet means "% by mass" unless otherwise specified. Non-mode oriented magnetic steel sheet includes a chemical composition represented by: Si: 3.0% to 3.6%; Al: 0.50% to 1.25%; Mn: 0.5% to 1.5%; Sb or Sn or both of them: [Sb] + [Sn] / 2 is 0.0025% to 0.05% where [Sb] denotes an Sb content and [Sn] denotes an Sn content; P: 0.010% to 0.150%; Ni: 0.010% to 0.200%; C: 0.0010% to 0.0040%; N: 0.0030% or less; S: 0.0020% or less; Ti: 0.0030% or less; Cu: 0.0500% or less; Cr: 0.0500% or less; Mo: 0.0500% or less; Bi: 0.0050% or less; Pb: 0.0050% or less; V: 0.0050% or less; B: 0.0050% or less; and the balance: Fe and impurities. As impurities, those contained in raw materials such as ore and scrap, and those contained during the production process are exemplified. (Si: 3.0% to 3.6%)
    [00086] Si increases specific strength and reduces core loss. When an Si content is less than 3.0%, the core loss cannot be reduced sufficiently. Thus, the Si content is 3.0% or more, and preferably 3.2% or more. On the other hand, when the Si content is above 3.6%, the toughness deteriorates and cold rolling becomes difficult. Thus, the Si content is 3.6% or less. (Al: 0.50% to 1.25%)
    [00087] Al increases specific resistance and reduces core loss, particularly core loss at high frequency. When the Al content is less than 0.50%, the core loss at high frequency cannot be reduced sufficiently. Thus, the Al content is 0.50% or more. On the other hand, when the Al content is above 1.25%, the hysteresis losses increase, and the core loss at a commercial frequency increases. Thus, the Al content is 1.25% or less. (Mn: 0.5% to 1.5%)
    [00088] Mn reduces core loss. When the Mn content is less than 0.5%, the core loss cannot be reduced sufficiently. Fine precipitates are sometimes formed in order to increase core loss. Thus, the Mn content is 0.5% or more, and preferably 0.7% or more. On the other hand, when the Mn content is above 1.5%, many Mn carbides are formed, and core loss increases. Thus, the Mn content is 1.5% or less. (Sb or Sn or both of them: [Sb] + [Sn] / 2 is 0.0025% to 0.05%)
    [00089] Sb and Sn improve the magnetic flux density. Sb is twice as effective as Sn. When [Sb] + [Sn] / 2 is less than 0.0025% where [Sb] denotes the Sb content and [Sn] denotes the Sn content, a sufficient magnetic flux density cannot be obtained. Thus, [Sb] + [Sn] / 2 is 0.0025% or more. On the other hand, when [Sb] + [Sn] / 2 is above 0.05%, the magnetic flux density improvement effect is saturated, and the cost increases in vain. Thus, [Sb] + [Sn] / 2 is 0.05% or less. (P: 0.010% to 0.150%)
    [00090] It has been made clear by the present inventors that P contributes to the improvement of magnetic flux density. When the P content is less than 0.010%, a sufficient magnetic flux density cannot be obtained. Thus, the P content is 0.010% or more, and preferably 0.015% or more. On the other hand, when the P content is above 0.150%, the core loss increases. Thus, the P content is 0.150% or less, and preferably 0.100% or less. (Ni: 0.010% to 0.200%)
    [00091] It has been made clear by the present inventors that Ni contributes to the improvement of magnetic flux density. When the Ni content is less than 0.010%, a sufficient magnetic flux density cannot be obtained. Thus, the Ni content is 0.010% or more, and preferably 0.020% or more. On the other hand, when the Ni content is above 0.200%, the core loss increases. Thus, the Ni content is 0.200% or less, and preferably 0.100% or less. (C: 0.0010% to 0.0040%)
    [00092] It has been made clear by the present inventors that C contributes to the improvement of magnetic flux density. When the C content is less than 0.0010%, sufficient magnetic flux density cannot be obtained. Thus, the C content is 0.0010% or more, and preferably 0.0020% or more. When the C content is above 0.0040% and the Mn content is 0.5% or more, many Mn carbides are formed, and the core loss increases. Thus, the C content is 0.040% or less, and preferably 0.0030% or less. (N: 0.0030% or less)
    [00093] N is not an essential element, and is contained as an impurity in steel, for example. N causes magnetic aging so as to increase core loss. Consequently, the lower the N content, the better. The increase in core loss is notable when the N content is above 0.0030%. Thus, the N content is 0.0030% or less. Considerable cost is required to lower the N content to less than 0.0001%. Therefore, it is not necessary to decrease the N content to less than 0.0001%. (S: 0.0020% or less)
    [00094] S is not an essential element, and is contained as an impurity in steel, for example. S forms fine precipitates in order to increase core loss. Consequently, the lower the S content, the better. The increase in core loss is noticeable when the S content is above 0.0020%. Thus, the S content is 0.0020% or less. Considerable cost is required to lower the S content to less than 0.0001%. Therefore, it is not necessary to lower the S content to less than 0.0001%. (Ti: 0.0030% or less)
    [00095] Ti is not an essential element, and is contained as an impurity in steel, for example. Ti forms fine precipitates in order to increase core loss. Consequently, the lower the Ti content, the better. The increase in core loss is notable when the Ti content is above 0.0030%. Thus, the Ti content is 0.0030% or less. Considerable cost is required to lower the Ti content to less than 0.0001%. Therefore, it is not necessary to lower the Ti content to less than 0.0001%. (Cu: 0.0500% or less)
    [00096] Cu is not an essential element, and is contained as an impurity in steel, for example. There is the possibility that Cu forms fine sulfides in order to deteriorate the magnetic properties. Consequently, the lower the Cu content, the better. The formation of Cu sulphides is notable when the Cu content is above 0.0500%. Thus, the Cu content is 0.0500% or less. It takes considerable cost to lower the Cu content to less than 0.0001%. Therefore, it is not necessary to lower the Cu content to less than 0.0001%. (Cr: 0.0500% or less)
    [00097] Cr is not an essential element, and is contained as an impurity in steel, for example. There is the possibility that Cr forms carbides in order to deteriorate the magnetic properties. Consequently, the lower the Cr content, the better. The formation of Cr carbides is notable when the Cr content is above 0.0500%. Thus, the Cr content is 0.0500% or less. Considerable cost is required to lower the Cr content to less than 0.0001%. Therefore, it is not necessary to decrease the Cr content to less than 0.0001%. (Mo: 0.0050% or less)
    [00098] Mo is not an essential element, and is contained as an impurity in steel, for example. There is the possibility that Mo forms carbide in order to deteriorate the magnetic properties. Consequently, the lower the Mo content, the better. The formation of Mo carbides is notable when the Mo content is above 0.0050%. Thus, the Mo content is 0.0050% or less. Considerable cost is required to lower the Mo content to less than 0.0001%. Therefore, it is not necessary to lower the Mo content to less than 0.0001%. (Bi: 0.0050% or less)
    [00099] Bi is not an essential element, and is contained as an impurity in steel, for example. There is the possibility that Bi facilitates the formation of fine Mn sulphides so as to deteriorate the magnetic properties. Consequently, the lower the Bi content, the better. The facilitation of fine Mn sulphides is notable when the Bi content is above 0.0050%. Thus, the Bi content is 0.0050% or less. Considerable cost is required to lower the Bi content to less than 0.0001%. Therefore, it is not necessary to lower the Bi content to less than 0.0001%. (Pb: 0.0050% or less)
    [000100] Pb is not an essential element, and is contained as an impurity in steel, for example. There is the possibility that Pb facilitates the formation of fine Mn sulphides so as to deteriorate the magnetic properties. Consequently, the lower the Pb content, the better. The facilitation of Mn sulphides is notable when the Pb content is above 0.0050%. Thus, the Pb content is 0.0050% or less. Considerable cost is required to lower the Pb content to less than 0.0001%. Therefore, it is not necessary to lower the Pb content to less than 0.0001%. (V: 0.0050% or less)
    [000101] V is not an essential element, and is contained as an impurity in steel, for example. There is a possibility that V forms carbides or nitrides in order to deteriorate the magnetic properties. Consequently, the lower the V content, the better. The formation of V carbides and V nitrides is notable when the V content is above 0.0050%. Thus, the V content is 0.0050% or less. Considerable cost is required to lower the V content to less than 0.0001%. Therefore, it is not necessary to lower the V content to less than 0.0001%. (B: 0.0050% or less)
    [000102] B is not an essential element, and is contained as an impurity in steel, for example. There is the possibility that B forms nitrides or precipitates containing Fe in order to deteriorate the magnetic properties. Consequently, the lower the B content, the better. The formation of nitrides or precipitates is notable when the B content is above 0.0050%. Thus, the B content is 0.0050% or less. Considerable cost is required to lower the B content to less than 0.0001%. Therefore, it is not necessary to lower the B content to less than 0.0001%.
    [000103] The thickness of the unoriented magnetic steel sheet according to the modality of the present invention will be described below. The thickness of the unoriented magnetic steel sheet depending on the modality is 0.15mm or more and 0.30mm or less. When the thickness is above 0.30 mm, an excellent high frequency core loss cannot be obtained. So the thickness is 0.30mm or less. When the thickness is less than 0.15 mm, passing the sheet through an annealing line in finish annealing is difficult. So the thickness is 0.15mm or more.
    [000104] The magnetic properties of the unoriented magnetic steel sheet according to the modality of the present invention will be described below. Non-mode oriented magnetic steel sheet includes magnetic properties represented by, where thickness is represented by t (mm), a magnetic flux density B50: "0.2 x t + 1.52" T or more; a magnetic flux density difference ΔB50: 0.08T or less; W10/50 core loss: 0.95 W/kg or less and W10/400 core loss: "20 x t + 7.5" W/kg or less. (B50 magnetic flux density: "0.2 x t + 1.52" T or more)
    [000105] Magnetic flux density B50 is a magnetic flux density in a magnetic field of 5000 A/m. The average value between the magnetic flux density B50 in the rolling direction (hereafter it is sometimes called the "L direction") and the magnetic flux density B50 in a direction perpendicular to the rolling direction and the thickness direction of the plate (hereafter it is sometimes called the "C direction") and used as the B50 magnetic flux density of an unoriented magnetic steel plate. When the magnetic flux density 50 is less than "0.2 x t + 1.52" T, a motor produced using this unoriented magnetic steel plate cannot guarantee sufficient motor torque. Cars that use such an engine, for example a hybrid vehicle and an electric vehicle, have disadvantages in starting. Thus, the magnetic flux density B50 is "0.2 x t + 1.52" T or more. The higher the magnetic flux density B50, the more preferable it is. (Magnetic flux density difference ΔB50: 0.08T or less)
    [000106] When the difference ΔB50 of the magnetic flux densities B50 in the L direction and the C direction is above 0.08T, the anisotropy is excessive, and excellent properties cannot be obtained in an integral type motor core. Thus, the magnetic flux density difference ΔB50 is 0.08T or less.
    [000107] (W10/50 core loss: 0.95 W/kg or less)
    [000108] W10/50 core loss is the core loss at a magnetic flux density of 1.0 T and a frequency of 50 Hz. An average value between the W10/50 core loss in the L direction and the loss of W10/50 core in the C direction is used as the W10/50 core loss of an unoriented magnetic steel sheet. When the W10/50 core loss is above 0.95 W/kg, the energy loss of a motor core produced using this unoriented magnetic steel sheet becomes excessively large, and the heating value and the power generator size increase. So the W10/50 core loss is 0.95 W/kg or less. The smaller the W10/50 core loss, the more preferable it is. (W10/400 core loss: "20 x t + 7.5" W/kg or less)
    [000109] W10/400 core loss is the core loss at 1.0 T magnetic flux density and a frequency of 400 Hz. The average value between the W10/400 core loss in the L direction and the loss of W10/400 core in C direction is used as W10/400 core loss of an unoriented magnetic steel sheet. When the W10/400 core loss is above "20 xt + 7.5" W/kg, the energy loss of a motor core produced using this unoriented magnetic steel plate becomes excessively large, and the heating value and power generator size increase. Thus, the W10/40 core loss is "20 x t + 7.5" W/kg or less. The smaller the W10/400 core loss, the more preferable it is.
    [000110] Magnetic flux density B50, core loss W10/50, and core loss W10/400 can be measured by an Epstein tester defined in JIS C 2550 or by a single sheet tester (SST) defined in JIS C 2556, for example.
    [000111] Below are described carbides contained in the unoriented magnetic steel sheet according to the modality of the present invention. In non-mode oriented magnetic steel sheet, the ratio of the number of intergranular carbides precipitated in the grains to the sum of the number of intergranular carbides and the number of grain edge carbides precipitated in the grain edges is 0.50 or less. When the ratio is above 0.50, intergranular carbides are excessive, and core loss increases. So the ratio is 0.50 or less. The number of intergranular carbides and the number of carbides at the edges of the grains can be specified by an observation under a scanning microscope.
    [000112] The method of production of the non-oriented magnetic steel sheet according to the modality will be described below. In the production method, hot rolling, hot rolled sheet annealing, cold rolling, finish annealing, etc. are performed.
    [000113] In hot rolling, heating of a steel material such as a plate having the chemical composition shown above is performed (plate heating), and then rough rolling and finishing rolling are performed, by example. The heating temperature of the plate is preferably 1000°C or more and 1250°C or less. The thickness of a hot rolled steel sheet obtained by hot rolling is preferably 1.6 mm or more and 2.6 mm or less. After hot rolling, annealing of the hot rolled steel sheet (annealing of hot rolled sheet) is performed. After annealing the hot rolled sheet, cold rolling of the hot rolled steel sheet is carried out to obtain a cold rolled steel sheet. Cold rolling can be performed once, or two or more times being interspersed with intermediate annealings.
    [000114] The hot rolled steel sheet is held in a first temperature range from 850°C to 1100°C for 10 seconds to 120 seconds and subsequently cooled at a rate of 5°C/s to 50°C/ s in a temperature zone of 850°C to 600°C, in the intermediate annealing if the intermediate annealing is performed, or in the annealing of the hot rolled sheet if the intermediate annealing is not performed. If intermediate annealing is not performed, annealing of hot rolled sheet is an example of first annealing. When the holding temperature (first holding temperature) is less than 850°C, the crystal grains are not sufficiently coarsened, and a sufficient magnetic flux density B50 cannot be obtained. Thus, the first holding temperature is 850°C or more, and preferably 950°C or more. When the first holding temperature is above 1100°C, the toughness is decreased, and fractures easily occur in the subsequent cold rolling. Thus, the first holding temperature is 1100°C or less. When the retention time (first retention time) is less than 10 seconds, the crystal grains are not blunt enough, and a sufficient B50 magnetic flux density cannot be obtained. So the first hold time is 10 seconds or more. When the first retention time is above 120 seconds, the toughness is diminished, and fractures easily occur in the subsequent cold rolling. Thus, the first retention time is 120 seconds or less. When the cooling rate (first cooling rate) after retention is less than 5°C/s, sufficient magnetic flux density B50 cannot be obtained, and core loss W10/50 and core loss W10/ 400 increase. Thus, the first cooling rate is 5°C/s or more, and preferably 20°C/s or more. When the first cooling rate is above 50°C/s, the steel sheet deforms greatly, and fractures easily occur in the subsequent cold rolling. Thus, the first cooling rate is 50°C/s or less.
    [000115] After cold rolling, the finish annealing of the cold rolled steel sheet is performed. Finish annealing is an example of following annealing. In finish annealing, the cold rolled steel sheet is held in a second temperature range of 900°C to 1100°C for 10 seconds to 240 seconds, and then cooled at a rate of 10°C/s to 40°C /s over a temperature zone of 900°C to 300°C. When the holding temperature (second holding temperature) is less than 900°C, the crystal grains are not hardened sufficiently, and excellent magnetic properties cannot be obtained. Thus, the second holding temperature is 900°C or more, and preferably 950°C or more. When the second holding temperature is above 1100°C, the crystal grains are excessively coarsened, and high frequency core loss increases. Thus, the second holding temperature is 1100°C or less, and preferably 1050°C or less. When the retention time (second retention time) is less than 10 seconds, the crystal grains are not sufficiently coarsened, and excellent magnetic properties cannot be obtained. Thus, the second retention time is 10 seconds or more, and preferably 15 seconds or more. When the second retention time is above 240 seconds, the crystal grains are excessively coarsened, and the high frequency core loss increases. Thus, the second retention time is 240 seconds or less, and preferably 200 seconds or less. When the cooling rate (second cooling rate) after retention is above 40°C/s, the ratio of the number of intergranular carbides to the total number of intergranular carbides and carbides at the grain edges above 0. 50, and the core loss increases. Thus, the second cooling rate is 40°C/sec or less, and preferably 30°C/sec or less. When the second cooling rate is less than 10°C/s, the effect of decreasing core loss is saturated, and productivity is decreased. Thus, the second cooling rate is 10°C/s or less.
    [000116] Magnetic steel sheet not oriented according to modality can thus be produced. After the finish annealing, an insulating coating film can be formed by coating and baking.
    [000117] Non-modally oriented magnetic steel sheet as stated above is used, for example, for an iron core of a motor and it is possible to greatly contribute to the reduction of energy consumption of an air conditioner, of a refrigerator, electric vehicle, hybrid vehicle, etc.
    [000118] Hereinafter, preferred embodiments of the present invention are described in detail, but the present invention is not limited to these examples. It is apparent to a person skilled in the art to which the present invention belongs that several examples of modifications or several revised examples can be conceived within the scope of the technical ideas described in the claims, and it is logically understood that these also fall within the technical scope. of the present invention. Examples
    [000119] In the following, the unoriented magnetic steel sheet according to the embodiment of the present invention is described concretely while being illustrated with examples. The examples illustrated below are only examples of the unoriented magnetic steel sheet in accordance with the embodiment of the present invention, and the grain oriented magnetic steel sheet of the present invention is not limited to the following examples. (first experience)
    [000120] In a first experiment, a steel ingot containing, in % by mass, C: 0.0022%, S: 0.0012%, Ti: 0.0015%, N: 0.0018%, Sn: 0.022 %, P: 0.016%, Ni: 0.031%, Cu: 0.024%, and the balance of Si, Al, Mn, Fe and impurities was produced using a vacuum melting furnace. Contents of Si, Al and Mn in each steel ingot are listed in Table 1. Then the steel ingot was heated to 1150°C for one hour in a heating furnace, taken out of the heating furnace, and then run in total. six hot rolling passes to obtain a hot rolled steel sheet with a thickness of 2.0 mm. Subsequently, the hot rolled steel sheet was held at 1000°C for 60 seconds in the annealing of the hot rolled sheet. The cooling rate on cooling after holding from 850°C to 600°C was 25°C/s. Subsequently, cold rolling of the hot rolled steel sheet was carried out to obtain a cold rolled steel sheet with a thickness of 0.30 mm. Then, the cold rolled steel sheet was held at 1000°C for 20 seconds in the finish annealing. The cooling rate on cooling after retention from 900°C to 300°C was 15°C/s. Subsequently, an insulating coating film was formed by coating and baking. A non-magnetic oriented steel sheet was thus produced. [00150] Six pieces of square 55 mm samples were made of each magnetic steel sheet with grain oriented, then the core losses W10/400, the core losses W10/50, and the magnetic flux densities B50 in the L direction and in the C direction of each sample were measured by the SST method. An average value between the W10/400 core loss in the L direction and the W10/400 core loss in the C direction, an average value between the W10/50 core loss in the L direction and the W10/50 core loss in the C direction C, an average value between the magnetic flux density B50 in the L direction and the magnetic flux density in the C direction, and the difference ΔB50 between the magnetic flux density B50 in the L direction and the magnetic flux density B50 in the C direction were calculated for each sample. The mean value between the W10/400 core losses of the six pieces of the samples, and the mean value between the magnetic flux densities B50 of the six pieces of the samples were calculated for each of the unoriented magnetic steel sheets using the values established above. An average value between the magnetic flux density B50 in the C direction of the six pieces of samples, and an average value between the magnetic flux density differences ΔB50 of the six pieces of samples were calculated for each of the unoriented magnetic steel sheets. These results are also listed in Table 1. Underlined values in Table 1 indicate that the numerical values are outside the range of the present invention.
    [000121] Scanning microscope observation was performed within a visual field with an area of 0.25 mm2 for each unoriented magnetic steel plate, and it was found that the ratio of the number of intergranular carbides precipitated in grains to the sum the number of intergranular carbides and the number of grain edge carbides at grain edges was 0.50 or less on any unoriented magnetic steel plate. Table 1

    [000122] As listed in Table 1, in each of the samples No. 12, No. 1-4, No. 1-5, No. 1-6 No. 1-9, No. 1-11, No. 1 -12, No. 1-14, and No. 1-15, the chemical composition was within the range of the present invention, and excellent magnetic properties could be obtained. In each of samples #1-7, #1-9, #1-11, #1-14, and #1-15, the Si content and the Mn content were within the preferable range, and particularly excellent magnetic properties could be obtained.
    [000123] In a No. 1-1 sample, the Si content was less than the lower limit of the range of the present invention, and therefore the core loss was high. In sample #1-3, the Al content was less than the lower end of the range of the present invention, and therefore the core loss was high. In a No. I-5 sample, the Mn content was less than the lower end of the range of the present invention, and therefore the core loss was high. In sample #1-10, the Mn content was above the upper limit of the range of the present invention, and therefore the core loss was high. In a sample 1-13, the Al content was above the upper limit of the range of the present invention, and therefore the core loss at the commercial frequency was high, and the magnetic flux density difference was large. In a sample 1-16, the Si content was above the upper limit of the range of the present invention, and therefore fractures occurred during cold rolling, and the magnetic properties could not be measured. (second experience)
    [000124] In a second experiment, a steel ingot containing, in % by mass, Si: 3.2%, Al: 0.80%, Mn: 0.9%, C: 0.0029%, S: 0 .0019%, Ti: 0.0012%, N: 0.0024%, Sb: 0.010%, Sn: 0.042%, P: 0.025%, Ni: 0.024%, Cr: 0.02%, the balance of Fe and impurities was produced using a vacuum melting furnace.
    [000125] Then, the steel ingot was heated to 1100°C for one hour in a heating furnace, taken out of the heating furnace, and then six hot rolling passes were performed in total to obtain a rolled steel plate. hot with a thickness of 2.0 mm. Subsequently, the annealing of the hot rolled sheet was performed. A first holding temperature T1, a first holding time t1, and a first cooling rate R1 in the re-baking of the hot rolled sheet were listed in Table 2. Subsequently, the cold rolling of the hot rolled steel sheet was performed. hot to obtain a cold-rolled steel sheet with a thickness of 0.25 mm. Then, the cold rolled steel sheet was held at 980°C for 25 seconds in the finish annealing. The cooling rate on cooling after retention from 900°C to 300°C was 20°C/s. Subsequently, an insulation coating film was formed by coating and baking. An unoriented magnetic steel sheet was thus produced.
    [000126] Measurements of magnetic properties were performed similarly to the first experiment. These results are also listed in Table 2. Values underlined in Table 2 indicate that the numerical values are outside the range of the present invention. It was found that the ratio of the number of intergranular carbides precipitated in the grains to the sum of the number of intergranular carbides and the number of grain edge carbides precipitated at the grain edges was 0.50 or less in any magnetic steel plate. not oriented similarly to the first experience. Table 2


    [000127] As listed in Table 2, in each of samples No. 2-3, No. 2-5, No. 2-9, and No. 2-11, the conditions of the first annealing were within the range of the present invention, and excellent magnetic properties were obtained. In each of samples no. 2-7 a no. 2-9 and no. 2-11, the first holding temperature and the first cooling rate were each within the preferable range, and particularly excellent magnetic properties could be obtained .
    [000128] In a 2-1 sample, the first holding temperature T1 was less than the lower limit of the range of the present invention, and therefore the core loss was high, and the magnetic flux density was low. In sample #2-2, the first retention time t1 was less than the lower limit of the range of the present invention, and therefore the core loss was high, and the magnetic flux density was low. In sample #2-4, the first cooling rate R1 was less than the lower end of the range of the present invention, and therefore the core loss was high, and the magnetic flux density was low. In sample No. 2-10, the first cooling rate R1 was above the upper limit of the range of the present invention, and therefore the steel sheet deformed greatly, fractures occurred during cold rolling, and magnetic properties could not be measured. In sample #2-12, the first retention time t1 was above the upper limit of the range of the present invention, and therefore the toughness was decreased, fractures occurred during cold rolling, and the magnetic properties could not be measures. In sample #2-13, the first retention temperature T1 was above the upper limit of the range of the present invention, and therefore the toughness was decreased, fractures occurred during cold rolling, and the magnetic properties did not could be measured. (Third experience)
    [000129] In a third experiment, a steel ingot containing, in % by mass, Si: 3.4%, Al: 0.80%, Mn: 0.9%, C: 0.0010%, S: 0 .0014%, Ti: 0.0018%, N: 0.0022%, Sb: 0.022%, Sn: 0.051%, P: 0.018%, Ni: 0.034%, Cr: 0.03%, Cu: 0.04 %, Mo: 0.01%, B: 0.0009%, and the balance of Fe and impurities were produced using a vacuum melting furnace.
    [000130] Then, the steel ingot was heated to 1170°C for one hour in a heating oven, and then six hot rolling passes were performed in total to obtain a hot rolled steel sheet with a thickness of 2 .1 mm. Subsequently, the hot-rolled steel sheet was held at 980°C for 50 seconds in the hot-rolled sheet annealing. The cooling rate on cooling after holding from 850°C to 500°C was 29°C/s. Subsequently, cold rolling of the hot rolled steel sheet was carried out to obtain a cold rolled steel sheet with a thickness of 0.25 mm. Then the finish annealing was performed. A second holding temperature T2, a second holding time t2, and a second cooling rate R2 in the finish annealing are listed in Table 3. Thereafter an insulating coating film was formed by coating and baking. An unoriented magnetic steel sheet was thus produced.
    [000131] Measurements of magnetic properties were performed, and the ratio of the number of intergranular carbides precipitated in the grains to the sum of the number of intergranular carbides and the number of grain edge carbides precipitated in the grain edges was measured, similarly to the first experience. These results are also listed in Table 3. Values underlined in Table 3 indicate that the numerical values are outside the range of the present invention. Table 3

    [000132] As listed in Table 3, in each of samples no. 32, no. 3-4 to no. 3-7, and no. 3-10 to no. 3-16, the conditions of the second annealing were within the range of the present invention, and excellent magnetic properties were obtained. In each of samples no. 3-5 to 3-7 and no. 3-11 to 3-13, the second hold temperature, the second hold time, and the second cooling rate were within the preferable range, and particularly excellent magnetic properties were obtained.
    [000133] In a No. 3-1 sample, the second retention temperature T2 was lower than the lower limit of the range of the present invention, and therefore the core loss was high. In sample #3-3, the second retention time t2 was less than the lower limit of the range of the present invention, and therefore the core loss was high. In sample #3-8, the second retention time t2 was above the upper limit of the range of the present invention, and therefore the core loss at high frequency was high. In sample #3-9, the second cooling rate R2 was above the upper limit R2 was above the upper limit of the range of the present invention, and therefore the intergranular carbide ratio was high, and the core loss was high. In sample #3-17, the second holding temperature T2 was above the upper limit of the range of the present invention, and therefore the core loss at high frequency was high. (Fourth experience)
    [000134] In a fourth experiment, a steel ingot containing in % by mass. Si: 3.2%, Al: 0.80%, Mn: 1.0%, S: 0.0010%, Ti: 0.0012%, N: 0.0020%, Sn: 0.041%, Cu: 0.022 %, and the balance of P, Ni, C, Fe and impurities was produced using a vacuum melting furnace. The P, Ni, and C contents of each steel ingot are listed in table 4.
    [000135] Then the steel ingot was heated to 1140°C for one hour in a heating furnace, removed from the heating furnace, and then six hot rolling passes were performed in total to obtain a hot rolled steel sheet with a thickness of 2.0 mm. Subsequently, the hot rolled steel sheet was held at 880C for 40 seconds in the annealing of the hot rolled sheet. The cooling rate on cooling after holding from 850°C to 600°C was 29°C/s. Subsequently, cold rolling of the hot rolled steel sheet was carried out to obtain a cold rolled steel sheet with a thickness of 0.30 mm. Then, the cold rolled steel sheet was held at 1000°C for 12 seconds in the finish annealing. The cooling rate on cooling after retention from 900°C to 300°C was 25°C/s. Subsequently, an insulating coating film was formed by coating and baking. An unoriented magnetic steel sheet was thus produced.
    [000136] Measurements of magnetic properties were performed similarly to the first experiment. These results are also listed in Table 4. Values underlined in Table 4 indicate that the numerical values are outside the range of the present invention. It was found that the ratio of the number of intergranular carbides precipitated in the grains to the sum of the number of intergranular carbides and the number of grain edge carbides precipitated at the grain edges was 0.50 or less in any magnetic steel plate. not oriented similarly to the first experience Table 4

    [000137] As illustrated in Table 4, in each of samples No. 4-2 to No. 4-9, the chemical composition was within the range of the present invention, and excellent magnetic properties could be obtained. In each of samples No. 4-6 to No. 4-8, the P content, Ni content and C content were within the preferable range, and particularly excellent magnetic properties could be obtained.
    [000138] In a No. 4-1 sample, the P content, the Ni content and the C content were each less than the lower limit of the range of the present invention, and therefore the magnetic flux density was low. In each of samples No. 4-10 and No. 4-11, the P content, Ni content and C content were each above the upper limit of the range of the present invention, and therefore the core loss was high. (Fifth experience)
    [000139] In a fifth experiment, a steel ingot containing, in % by mass, Si: 3.3%, Al: 0.80%, Mn: 1.1%, C: 0.0012%, S: 0 .0018%, Ti: 0.0015%, N: 0.0024%, Sb: 0.004%, Sn: 0.058%, P: 0.015%, Ni: 0.018%, Cr: 0.005%, Cu: 0.010%, and the Fe balance and impurities were produced using a vacuum melting furnace.
    [000140] Then the steel ingot was heated to 1160°C for one hour in a heating furnace, taken out of the heating furnace, then six hot rolling passes were performed in total to obtain a hot rolled steel sheet with a thickness of 2.0 mm. Subsequently, the hot rolled steel sheet was held at 1000°C for 60 seconds in the annealing of the hot rolled sheet. The cooling rate on cooling after holding from 850°C to 600°C was 28°C/s. Subsequently, cold rolling of the hot rolled steel sheet was carried out to obtain a cold rolled sheet with a thickness of 0.15 mm. Then the finish annealing was performed. The second holding temperature T2, the second holding time t2, and the second cooling rate R2 in the finish annealing are listed in Table 5. Subsequently, an insulating coating film was formed by coating and baking. An unoriented magnetic steel sheet was thus produced.
    [000141] Measurements of magnetic properties were performed similarly to the first experiment. These results are also listed in Table 5. Values underlined in Table 5 indicate that the numerical values are outside the range of the present invention. It was found that the ratio of the number of intergranular carbides precipitated in the grains to the sum of the number of intergranular carbides and the number of grain edge carbides precipitated at the grain edges was 0.50 or less in any magnetic steel plate. not oriented similarly to the first experience. Table 5

    [000142] As listed in Table 5, in each of samples no. 52, no. 5-4 no. 5-7, and no. 5-9 no. of the range of the present invention, and excellent magnetic properties could be obtained. In each of Samples #5-4 thru 5-7, #5-9, and #5-10, the second hold temperature, the second hold time, and the second cooling rate were within the preferred range. , and particularly excellent magnetic properties could be obtained. [00173] In a No. 5-1 sample, the second holding temperature T2 was lower than the lower limit of the range of the present invention, and therefore the core loss was high, and the magnetic flux density was low. In sample #5-3, the second retention time t2 was less than the lower limit of the range of the present invention, and therefore the core loss was high. In sample #5-8, the second retention time was above the upper limit of the range of the present invention, and therefore the core loss was low and the magnetic flux density was high. In sample No. 5-12, the second holding temperature T2 was above the upper limit of the range of the present invention, and therefore the core loss was high, and the magnetic flux density was low. INDUSTRIAL APPLICABILITY
    [000143] The present invention can be used, for example, for industries producing unoriented magnetic steel sheets and industries that use the unoriented magnetic steel sheet.
    权利要求:
    Claims (7)
    [0001]
    1. Unoriented magnetic steel sheet, characterized by the fact that it comprises: a chemical composition represented, in % by mass, by: Si: 3.0% to 3.6%; Al: 0.50% to 1.25%; Mn: 0.5% to 1.5%; Sb or Sn or both of them: [Sb] + [Sn] / 2 is 0.0025% to 0.05% where [Sb] denotes an Sb content and [Sn] denotes an Sn content; P: 0.010% to 0.150%; Ni: 0.010% to 0.200%; C: 0.0010% to 0.0040%; N: 0.0030% or less; S: 0.0020% or less; Ti: 0.0030% or less; Cu: 0.0500% or less; Cr: 0.0500% or less; Mo: 0.0500% or less; Bi: 0.0050% or less; Pb: 0.0050% or less; V: 0.0050% or less; B: 0.0050% or less; and balance: Fe and impurities, and magnetic properties represented, where t denotes the thickness (mm) of the unoriented magnetic steel sheet, by: magnetic flux density B50: "0.2 x t + 1.52" T or more; ΔB50 magnetic flux density difference: 0.08T or less; W10/50 core loss: 0.95 W/kg or less; and W10/400 core loss: "20 xt + 7.5" W/kg or less, where the thickness is 0.15 mm to 0.30 mm, and the ratio of the number of intragranular carbides precipitated in the grains to the sum of the number of intergranular carbides and the number of grain edge carbides precipitated at the grain edges is 0.50 or less.
    [0002]
    2. Unoriented magnetic steel sheet according to claim 1, characterized in that, in the chemical composition, P: 0.015% to 0.100%, Ni: 0.020% to 0.100%, or C: 0.0020% to 0 .0030%, or any combination thereof is satisfied.
    [0003]
    3. Non-oriented magnetic steel sheet production method, characterized in that it comprises: hot rolling a steel material to obtain a hot rolled steel sheet; cold rolling of hot rolled steel sheet to obtain a cold rolled steel sheet; performing the first annealing of the hot rolled steel sheet before the cold rolling is completed; and performing the second annealing of the cold rolled steel sheet, where the first annealing includes: holding the hot rolled steel sheet in a first temperature range of 850°C to 1100°C for 10 seconds to 120 seconds, and after hold, cool the hot rolled steel sheet at a rate of 5°C/s to 50°C/s in a temperature zone of 850°C to 600°C, where the second annealing includes: holding the steel sheet cold rolled in a second temperature range from 900°C to 1100°C for 10 seconds to 240 seconds, and after retention, cool the cold rolled steel sheet at a rate of 10°C/s to 40°C/ s in a temperature zone of 900°C to 300°C, and where the steel material comprises a chemical composition represented, in % by mass, by: Si: 3.0% to 3.6%; Al: 0.50% to 1.25%; Mn: 0.5% to 1.5%; Sb or Sn or both of them: [Sb] + [Sn] / 2 is 0.0025% to 0.05% where [Sb] denotes an Sb content and [Sn] denotes an Sn content; P: 0.010% to 0.150%; Ni: 0.010% to 0.200%; C: 0.0010% to 0.0040%; N: 0.0030% or less; S: 0.0020% or less; Ti: 0.0030% or less; Cu: 0.0500% or less; Cr: 0.0500% or less; Mo: 0.0500% or less; Bi: 0.0050% or less; Pb: 0.0050% or less; V: 0.0050% or less; B: 0.0050% or less; and balance: Fe and impurities.
    [0004]
    4. Non-oriented magnetic steel sheet production method according to claim 3, characterized in that the annealing of the hot rolled sheet is performed as the first annealing before the cold rolling.
    [0005]
    5. Method of production of unoriented magnetic steel sheet characterized by the fact that claim 3, further comprising the annealing of the hot rolled sheet before cold rolling, where an intermediate annealing is performed as the first annealing during the rolling to cold.
    [0006]
    6. Method of production of unoriented magnetic steel sheet according to any one of claims 3 to 5, characterized in that, in the chemical composition, P: 0.015% to 0.100%, Ni: 0.020% to 0.100%, or C: 0.0020% to 0.0030%, or any combination thereof is satisfied.
    [0007]
    7. Method of production of unoriented magnetic steel sheet according to any one of claims 3 to 6, characterized in that the thickness of the cold rolled steel sheet is 0.15 mm to 0.30 mm.
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    CN106661686A|2017-05-10|
    EP3165624B1|2019-05-01|
    JP6341281B2|2018-06-13|
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    US20170194082A1|2017-07-06|
    EP3165624A1|2017-05-10|
    JPWO2016002904A1|2017-04-27|
    TW201606093A|2016-02-16|
    MX2016015754A|2017-04-10|
    引用文献:
    公开号 | 申请日 | 公开日 | 申请人 | 专利标题
    KR100316896B1|1993-09-29|2002-02-19|에모또 간지|Non-oriented silicon steel sheet having low iron loss and method for manufacturing the same|
    JP2744581B2|1993-12-28|1998-04-28|川崎製鉄株式会社|Method for manufacturing non-oriented silicon steel sheet with extremely low iron loss and excellent low magnetic field characteristics|
    JP3307872B2|1998-02-06|2002-07-24|新日本製鐵株式会社|Motor for electric vehicle using non-oriented electrical steel sheet and method of manufacturing the electrical steel sheet|
    JP3815336B2|2002-01-23|2006-08-30|住友金属工業株式会社|Non-oriented electrical steel sheet|
    JP4506664B2|2005-12-15|2010-07-21|住友金属工業株式会社|Non-oriented electrical steel sheet for rotor and manufacturing method thereof|
    JP4855220B2|2006-11-17|2012-01-18|新日本製鐵株式会社|Non-oriented electrical steel sheet for split core|
    KR20100122116A|2008-04-14|2010-11-19|신닛뽄세이테쯔 카부시키카이샤|High-strength non-oriented magnetic steel sheet and process for producing the high-strength non-oriented magnetic steel sheet|
    EP2316980B1|2008-07-22|2018-11-14|Nippon Steel & Sumitomo Metal Corporation|Non-oriented electrical steel sheet and method for manufacturing the same|
    JP2010185119A|2009-02-13|2010-08-26|Sumitomo Metal Ind Ltd|Non-oriented electromagnetic steel sheet|
    KR101457755B1|2009-03-13|2014-11-03|신닛테츠스미킨 카부시키카이샤|Non－oriented magnetic steel sheet and method for producing the same|
    BRPI1013018B1|2009-06-03|2018-07-10|Nippon Steel & Sumitomo Metal Corporation|ELECTRICALLY ORIENTED STEEL SHEET|
    US9051815B2|2009-09-28|2015-06-09|Baker Hughes Incorporated|Apparatus and method for predicting vertical stress fields|
    CN103052722B|2010-08-04|2015-04-22|新日铁住金株式会社|Process for producing non-oriented electromagnetic steel sheet|
    JP2012036459A|2010-08-09|2012-02-23|Sumitomo Metal Ind Ltd|Non-oriented magnetic steel sheet and production method therefor|
    CN102453838A|2010-10-25|2012-05-16|宝山钢铁股份有限公司|High-strength non-oriented electrical steel with high magnetic induction and manufacturing method thereof|
    JP5712863B2|2011-08-23|2015-05-07|新日鐵住金株式会社|Method for producing non-oriented electrical steel sheet|
    JP5724824B2|2011-10-27|2015-05-27|新日鐵住金株式会社|Method for producing non-oriented electrical steel sheet with good magnetic properties in rolling direction|
    CN102367547B|2011-10-31|2013-03-13|山西太钢不锈钢股份有限公司|Manufacture method of high-silicon aluminum content non-oriented silicon steel strip|
    KR102012610B1|2012-03-29|2019-08-20|닛폰세이테츠 가부시키가이샤|Non-oriented electromagnetic steel sheet and method for producing same|
    TWI468533B|2012-05-31|2015-01-11|Nippon Steel & Sumitomo Metal Corp|Non - directional electromagnetic steel plate|
    WO2013179438A1|2012-05-31|2013-12-05|新日鐵住金株式会社|Nonoriented electromagnetic steel sheet|
    CN103543297B|2012-07-17|2016-09-21|冯金泉|Turntable|
    JP6127408B2|2012-08-17|2017-05-17|Ｊｆｅスチール株式会社|Method for producing non-oriented electrical steel sheet|RU2696887C1|2016-01-15|2019-08-08|ДжФЕ СТИЛ КОРПОРЕЙШН|Sheet from non-textured electrical steel and method of manufacturing thereof|
    KR101901313B1|2016-12-19|2018-09-21|주식회사 포스코|Non-oriented electrical steel sheet and method for manufacturing the same|
    JP6624393B2|2016-12-28|2019-12-25|Ｊｆｅスチール株式会社|Non-oriented electrical steel sheet with excellent recyclability|
    DE102017208146B4|2017-05-15|2019-06-19|Thyssenkrupp Ag|NO electrical steel for electric motors|
    JP6738047B2|2017-05-31|2020-08-12|Ｊｆｅスチール株式会社|Non-oriented electrical steel sheet and its manufacturing method|
    CN110212712B|2017-07-15|2021-09-07|芜湖乾凯材料科技有限公司|Low-stress motor iron core and preparation method thereof|
    KR102009392B1|2017-12-26|2019-08-09|주식회사 포스코|Non-oriented electrical steel sheet and method for manufacturing the same|
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    法律状态:
    2019-08-27| B06U| Preliminary requirement: requests with searches performed by other patent offices: procedure suspended [chapter 6.21 patent gazette]|
    2019-09-10| B25D| Requested change of name of applicant approved|Owner name: NIPPON STEEL CORPORATION (JP) |
    2021-03-09| B09A| Decision: intention to grant [chapter 9.1 patent gazette]|
    2021-05-25| B16A| Patent or certificate of addition of invention granted|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 02/07/2015, OBSERVADAS AS CONDICOES LEGAIS. |
    优先权:
    申请号 | 申请日 | 专利标题
    JP2014-136949|2014-07-02|
    JP2014136949|2014-07-02|
    PCT/JP2015/069197|WO2016002904A1|2014-07-02|2015-07-02|Non-oriented magnetic steel sheet, and manufacturing method for same|
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