WO2017130980A1 - 方向性電磁鋼板およびその製造方法 - Google Patents
方向性電磁鋼板およびその製造方法 Download PDFInfo
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- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
- H01F1/18—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets with insulating coating
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K15/00—Electron-beam welding or cutting
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D10/00—Modifying the physical properties by methods other than heat treatment or deformation
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1222—Hot rolling
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1233—Cold rolling
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1261—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest following hot rolling
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D8/1294—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a localized treatment
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
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- H—ELECTRICITY
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- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/147—Alloys characterised by their composition
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- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
- H01F41/14—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for applying magnetic films to substrates
- H01F41/22—Heat treatment; Thermal decomposition; Chemical vapour deposition
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2201/00—Treatment for obtaining particular effects
- C21D2201/05—Grain orientation
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1255—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest with diffusion of elements, e.g. decarburising, nitriding
Definitions
- the present invention relates to a grain-oriented electrical steel sheet suitable for an iron core material such as a transformer and a manufacturing method thereof.
- Oriented electrical steel sheets are mainly used as transformer iron cores, and are required to have excellent magnetization characteristics, particularly low iron loss. For that purpose, it is important to highly align the secondary recrystallized grains in the steel sheet in the (110) [001] orientation (Goss orientation) and to reduce impurities in the product.
- Patent Document 1 in introducing thermal strain into a point sequence by electron beam irradiation in a direction intersecting with the rolling direction of the grain-oriented electrical steel sheet, not only the irradiation point interval and irradiation energy are optimized, but also the steel sheet A technique for reducing the iron loss by irradiating the surface of the metal with an electron beam to introduce strain into the steel plate and subdivide the width of the magnetic domain is described.
- thermal strain is introduced, the magnetostriction increases, so that there is a problem that the noise characteristics of the transformer increase.
- Patent Document 2 is excellent in controlling the residence time t per point and the point interval X in accordance with the output of the electron beam when performing the magnetic domain fragmentation process by irradiating the electron beam in a dot shape.
- a technique for providing a grain-oriented electrical steel sheet having iron loss characteristics and noise characteristics is described.
- the forsterite coating increases the tension applied to the steel sheet and controls the diameter A and the irradiation pitch B of the thermal strain introduction region by electron beam irradiation, so that it has excellent low noise and low iron in an actual transformer.
- a technique for providing a grain-oriented electrical steel sheet capable of obtaining loss characteristics is described.
- Patent Document 4 describes a technique for optimizing the rolling direction width, the thickness direction depth, and the rolling direction introduction interval of the reflux magnetic domain by an electron beam method. With these methods, it is possible to obtain good iron loss characteristics while suppressing deterioration of transformer noise to some extent.
- the present invention has been developed in view of the above situation, and proposes a grain-oriented electrical steel sheet capable of obtaining excellent low noise and low iron loss characteristics when assembled in an actual transformer, and a method of manufacturing the same. For the purpose.
- the strain When the strain is introduced by electron beam irradiation, the magnetic domain is subdivided, so the eddy current loss is improved.
- hysteresis loss increases due to strain introduction. Iron loss is improved because the amount of improvement in eddy current loss is greater than the amount of hysteresis loss.
- the cause of the increase in the noise of the actual transformer that occurs when using a material having good iron loss characteristics is a decrease in magnetostriction characteristics due to the introduction of strain.
- the strain distribution to be introduced is kept as it is, the distribution of strain introduction is optimized, the magnetization behavior of the steel sheet is controlled, and the hysteresis loss is reduced. It is one of the effective means to improve.
- the residual flux density Br of the material is controlled by controlling the energy intensity distribution and beam diameter of the electron beam.
- the present invention has been made based on such knowledge, and has the following configuration.
- a grain-oriented electrical steel sheet having subdivided magnetic domains by electron beam irradiation When the maximum magnetic flux density is 1.7T, 0.1 to 0.7 times the residual magnetic flux density before the electron beam irradiation, A grain-oriented electrical steel sheet having a maximum magnetization force of 1.1 to 2.0 times that before the electron beam irradiation.
- the steel slab is hot rolled into a hot rolled steel sheet, Subjecting the hot-rolled steel sheet to hot-rolled sheet annealing, The hot-rolled steel sheet after the hot-rolled sheet annealing is cold-rolled steel sheet having a final sheet thickness by performing cold rolling twice or more sandwiching one time or intermediate annealing, Subjecting the cold-rolled steel sheet to decarburization annealing, A method for producing a grain-oriented electrical steel sheet that is subjected to finish annealing after applying an annealing separator containing MgO to the surface of the cold rolled steel sheet after the decarburization annealing, The steel plate after the finish annealing is subjected to magnetic domain subdivision treatment by electron beam irradiation, The magnetic domain segmentation process is performed with a beam diameter in a direction orthogonal to the scanning direction of the electron beam being 220 ⁇ m or less and a maximum beam intensity ratio in a direction orthogonal to the maximum beam intensity in the scanning direction being 0.7 to 1.3.
- the present invention it is possible to further reduce the iron loss of the grain-oriented electrical steel sheet without deteriorating the noise characteristics in the transformer in which the grain-oriented electrical steel sheet reduced in iron loss by applying strain by the electron beam is laminated. Can be realized.
- the type (component composition, structure, etc.) of the grain-oriented electrical steel sheet used as the ground iron is not particularly limited, and any kind of grain-oriented electrical steel sheet can be used.
- the grain-oriented electrical steel sheet of the present embodiment may have a tension coating on the surface of the ground iron.
- the type of the tension coating is not particularly limited. For example, two layers comprising a forsterite coating mainly composed of Mg 2 SiO 4 formed in finish annealing and a phosphate-based tension coating formed thereon. It can be a film.
- a phosphate-based tension-imparting insulating coating can be directly formed on the surface of the base iron having no forsterite coating.
- the phosphate-based tension-imparting insulating coating can be formed, for example, by applying an aqueous solution containing metal phosphate and silica as main components to the surface of the base iron and baking it.
- the surface layer portion of the ground iron is locally distorted by performing electron beam irradiation in the direction across the rolling direction on the surface at intervals in the rolling direction.
- strain regions extending in the direction crossing the rolling direction are formed at periodic intervals in the rolling direction.
- the feature of this embodiment is that the residual magnetic flux density level and the maximum magnetizing force level after irradiation with an electron beam can be further improved by improving hysteresis loss without deteriorating transformer noise. It was clarified and clarified the electron beam irradiation conditions to achieve it. Details will be described below.
- the present inventors investigated material parameters highly correlated with the amount of distortion introduced by electron beam irradiation.
- the magnetostrictive harmonic level (noise level estimated from the measured magnetostrictive vibration harmonic level (dB)) is highly correlated with transformer noise, and among them, from the magnetostrictive waveform of the steel plate excited under the conditions of 1.5T and 50Hz. It was found that the derived magnetostrictive harmonic level changes with high sensitivity according to the amount of strain introduced.
- the magnetostrictive harmonic level of 1.5T, 50Hz has a reflector on the surface of the steel plate, frequency analysis of the expansion and contraction motion (magnetostrictive waveform) of the steel plate measured by the laser Doppler vibrometer, and the speed every 100Hz.
- the value obtained by decomposing into frequency components and correcting the A scale for each frequency component is a value obtained by integrating in the range of 100 to 1000 Hz according to the following equation.
- ⁇ n a vibration harmonic component
- f n a frequency
- ⁇ n a hearing correction coefficient.
- Figure 1 shows the magnetostrictive harmonic level of each sample by changing the beam current value under the conditions of an acceleration voltage of 60 kV, a dot pitch of 0.32 mm, an irradiation line interval of 5.5 mm, and a scanning speed of 32 m / s. The result of deriving is shown.
- An increase in the beam current value indicates an increase in the amount of strain introduced into the steel sheet, and it can be said that there is a very good correlation between the amount of strain introduced and the magnetostrictive harmonic level.
- Fig. 2 shows the residual magnetic flux density Br and the maximum magnetizing force Hmax as important parameters for improving the hysteresis loss, and the hysteresis loop when the maximum magnetic flux density (Bm) is 1.7T.
- the hysteresis loss is proportional to the area of the portion surrounded by the hysteresis loop shown in FIG.
- the maximum magnetizing force Hmax and the residual magnetic flux density Br have a great influence on the area of the loop, and the smaller the both factors, the smaller the loop of the hysteresis loop. Therefore, it can be said that it is very important to control the rate of change of the residual magnetic flux density Br and the maximum magnetization force before and after irradiation.
- the ratio before and after irradiation is derived from these measured values by measuring the residual magnetic flux density before irradiation and the maximum magnetization force when excited to 1.7 T, and then measuring the sample after electron beam irradiation in the same manner. Is suitable, but for the sample after electron beam irradiation, the maximum magnetic force when the residual magnetic flux density and the maximum magnetic flux density Bm are 1.7 T is measured, and then the strain relief annealing is performed in a nitrogen atmosphere at 800 ° C. for 3 hours.
- the residual magnetic flux density and the maximum magnetization force of the sample after annealing may be used as values before electron beam irradiation. This is because the strain introduced by the electron beam irradiation is released by the strain relief annealing.
- Electron beam irradiation is performed on 0.27 mm-thick grain-oriented electrical steel sheets with varying acceleration voltage, convergence current, and beam current, and hysteresis loss before and after electron beam irradiation is measured.
- Fig. 3 shows the results arranged in relation to the maximum magnetization force.
- the irradiation conditions were adjusted so that the magnetostrictive harmonic level was constant, and the amount of distortion to be introduced was the same. Since it was thought that the residual magnetic flux density and the maximum magnetizing force had a great influence on the increase / decrease in hysteresis loss, the analysis was conducted by paying attention to the residual magnetic flux density and the maximum magnetizing force.
- a preferable range of the change rate of the residual magnetic flux density before and after irradiation is 0.1 or more and 0.5 or less.
- the preferable range of the change ratio of the maximum magnetization force before and after irradiation is 1.1 or more and 1.5 or less.
- FIG. 4 shows the amount of improvement in hysteresis loss of a steel sheet irradiated under irradiation conditions in which the beam diameter in the direction orthogonal to the scanning direction is 120 to 160 ⁇ m, the maximum beam intensity in the direction orthogonal to the scanning direction, and the maximum beam intensity in the scanning direction. The relationship of the ratio is shown.
- Hysteresis loss is improved when the maximum beam intensity ratio is 0.7 or more and 1.3 or less, the energy intensity distribution in the rolling direction and the direction perpendicular to the rolling direction is made the same as much as possible, and uniform distortion is introduced by the beam having a uniform energy intensity distribution. It turns out that is important. More preferably, the hysteresis loss is improved more favorably at 0.8 or more and 1.1 or less. Since Hmax and Br are parameters that are sensitive to strain, Hmax and Br can be adjusted by controlling the energy intensity distribution ratio that can change the introduced strain distribution.
- Figure 5 shows the relationship between the Hmax ratio (white circles) and Br ratio (black squares) and the energy intensity distribution ratio. By making the energy intensity distribution ratio close to 1 and making the strain distribution as uniform as possible, Hmax and Br It can be seen that both ratios are controlled within the preferred range described above.
- FIG. 6 shows the relationship between the amount of improvement in hysteresis loss of the sample irradiated under the irradiation condition with the maximum beam intensity ratio of 1.0 and the beam diameter in the direction orthogonal to the scanning direction. It was found that the hysteresis loss was improved when the electron beam diameter was 220 ⁇ m or less, and no change or deterioration was observed when the electron beam diameter was more than 220 ⁇ m. As the beam diameter is increased, the effect of improving the hysteresis loss is lost. Therefore, it is understood that it is important to irradiate the beam as narrow as possible in order to improve the hysteresis loss.
- the acceleration voltage is preferably 90 kV or more. More preferably, it is 150 kV or more.
- the upper limit is about 300 kV in practice.
- a method of converging the beam with a converging coil (beam control coil) is useful.
- beam control coil By devising the arrangement of the converging coil and performing current control with high accuracy, it is possible to control the beam diameter and energy intensity distribution within a favorable range even for electrons with low acceleration voltage and poor straightness. .
- the converging ability of the coil is sufficient, the preferred irradiation range is expanded and production stability is improved.
- the beam cannot be controlled as expected. In this case, it is possible to secure stable convergence capability by using two or more convergence coils.
- This stigmeter is generally composed of a coil, and adjusts the beam shape by correcting the amount of current in the x-axis direction and the y-axis direction orthogonal to each other.
- the beam shape control method using the acceleration voltage, converging coil, and stigmator described above it is not impossible to control the beam diameter and energy intensity distribution to a suitable range even if any one of them is applied, but a plurality of combinations are combined.
- the control range of the electron beam irradiation conditions that can be irradiated with an appropriate beam diameter and energy intensity distribution is expanded and the stability is remarkably improved. Therefore, it is preferable to combine a plurality of the above.
- irradiation conditions of the electron beam are not particularly limited, but suitable irradiation conditions are described below.
- the linear scanning direction of the electron beam is a direction that forms an angle of 60 ° or more and 120 ° or less from the rolling direction. If the angle is deviated from 90 °, the irradiation area of the strained portion increases, and it becomes a factor that restricts suitable irradiation conditions, so 90 ° is desirable.
- the irradiation of the electron beam onto the steel plate is preferably dot-shaped irradiation in which the beam is stopped and moved repeatedly.
- the dot interval (distance between centers of adjacent dots) at this time is preferably set to an average beam diameter in the scanning direction ⁇ 2.5 or less. An increase in the interval means that a region where no distortion is introduced increases in the meantime. Therefore, if the interval is wider than the above range, a sufficient magnetic domain refinement effect cannot be obtained.
- the average scanning speed is preferably 30 m / s or more. If the average scanning speed is less than 30 m / s, high productivity cannot be realized. Preferably, it is 75 m / s or more, more preferably 100 m / s or more. As the scanning speed increases, it becomes difficult to control dot irradiation that repeatedly stops and moves the beam, so the upper limit is preferably set to 300 m / s.
- the irradiation line interval is 15 mm or less. This is because when the irradiation line interval is widened, the magnetic domain fragmentation effect is poor and the iron loss is difficult to improve. There is no particular lower limit for the line spacing, but if the line spacing is narrow, the production capacity is impaired, so the preferred spacing is 5 mm or more.
- the beam current is preferably small from the viewpoint of controlling the beam shape. This is because when the charged particles repel each other, the beam becomes difficult to converge. Therefore, the upper limit of the beam current is 30 mA, more preferably 20 mA. On the other hand, if the beam current becomes too low, the magnetic domain refinement effect cannot be obtained. From the viewpoint of the magnetic domain refinement effect, the lower limit of the beam current is preferably 0.5 mA.
- the pressure in the processing chamber is preferably 3 Pa or less.
- the pressure in the processing chamber is preferably 3 Pa or less.
- the lower limit is about 10 ⁇ 5 Pa in practical use because excessively low costs increase the cost of vacuum control such as a vacuum pump.
- Example C 0.055 mass%, Si: 3.05 mass%, Mn: 0.08 mass%, Ni: 0.02 mass%, Al: 190 mass ppm, N: 65 mass ppm, Se: 150 mass ppm, S: 10 mass ppm and O: A steel slab containing 15 ppm by mass and the balance being substantially Fe composition was manufactured by continuous casting, heated to 1450 ° C, and hot rolled to a hot rolled sheet with a thickness of 2.4 mm And hot-rolled sheet annealing at 1025 ° C. for 300 seconds.
- an annealing separator containing 2 parts by weight of TiO 2 per 100 parts by weight of MgO. And final finish annealing for the purpose of secondary recrystallization, forsterite film formation and purification was performed at 1200 ° C. for 30 hours. Then, an insulating coat composed of 60% colloidal silica and aluminum phosphate was applied and baked at 800 ° C. This coating application treatment also serves as flattening annealing. Then, the electron beam was irradiated at right angles to the rolling direction.
- the accelerating voltage, the focusing coil, and the use conditions of the stigmator were changed.
- Other irradiation conditions were a dot interval of 0.20 mm, an irradiation line interval of 6.0 mm, a scanning speed of 60 m / s, and a processing chamber pressure of 0.01 Pa.
- the magnetic properties were evaluated using a product obtained by performing magnetic domain fragmentation treatment on one side as described above. Changes in the residual magnetic flux density and the maximum magnetization force before and after irradiation were derived using the magnetic characteristics of the sample after irradiation and the magnetic characteristics after annealing at 800 ° C. ⁇ 3 h in an N 2 atmosphere. Next, each product was sheared at an oblique angle, a 500 kVA three-phase transformer was assembled, and iron loss and noise were measured in an excited state at 50 Hz and 1.7 T.
- Table 1 shows the measurement conditions and measurement results. Since all the samples had the same magnetostrictive harmonic level, the total amount of distortion introduced can be considered to be the same.
- accelerating voltage 60kV
- items that can change the electron beam shape are not used, such as using multiple converging coils or using a stigmator, the optimal iron loss is reduced as shown in Nos. 1 to 4.
- Condition No. 3 exists, but the optimum condition disappears when the convergence current value deviates by 2 mA, indicating that the stability is low. It can be seen that the optimum condition range can be expanded by applying the beam control items (Nos. 5 to 8) even when the acceleration voltage is low.
- the optimum irradiation condition range is expanded by applying the beam control item, and not only the optimum irradiation range is expanded by applying the two-stage converging coil and stigmator, but also iron. It can be seen that the amount of loss improvement has also increased.
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Abstract
Description
1.電子ビーム照射による細分化磁区を有する方向性電磁鋼板であって、
最大磁束密度が1.7Tである場合に、
前記電子ビーム照射前の0.1から0.7倍の残留磁束密度と、
前記電子ビーム照射前の1.1から2.0倍の最大磁化力とを有する、方向性電磁鋼板。
該熱延鋼板に熱延板焼鈍を施し、
該熱延板焼鈍後の熱延鋼板に、1回または中間焼鈍をはさむ2回以上の冷間圧延を施して最終板厚を有する冷延鋼板とし、
該冷延鋼板に脱炭焼鈍を施し、
該脱炭焼鈍後の冷延鋼板表面にMgOを含む焼鈍分離剤を塗布した後に仕上焼鈍を施す方向性電磁鋼板の製造方法であって、
前記仕上げ焼鈍後の鋼板に、電子ビームの照射による磁区細分化処理を施し、
前記磁区細分化処理は、前記電子ビームの走査方向と直交する方向のビーム径が220μm以下、かつ走査方向のビーム最大強度に対して直交する方向のビーム最大強度比が0.7以上1.3以下にて行う、方向性電磁鋼板の製造方法。
C:0.055質量%、Si:3.05質量%、Mn:0.08質量%、Ni:0.02質量%、Al:190質量ppm、N:65質量ppm、Se:150質量ppm、S:10質量ppmおよびO:15質量ppmを含有し、残部は実質的にFeの組成となる鋼スラブを、連続鋳造にて製造し、1450℃に加熱後、熱間圧延により板厚:2.4 mmの熱延板としたのち、1025℃で300秒の熱延板焼鈍を施した。ついで、冷間圧延により中間板厚:0.60mmとし、酸化度PH2O/PH2=0.35、温度:950℃、時間:100秒の条件で中間焼鈍を実施した。その後、塩酸酸洗により表面のサブスケールを除去したのち、再度、冷間圧延を実施して、板厚:0.30mmの冷延板とした。
Claims (5)
- 電子ビーム照射による細分化磁区を有する方向性電磁鋼板であって、
最大磁束密度が1.7Tである場合に、前記電子ビーム照射前の0.1から0.7倍の残留磁束密度と、前記電子ビーム照射前の1.1から2.0倍の最大磁化力とを有する、方向性電磁鋼板。 - 鋼スラブに熱間圧延を施して熱延鋼板とし、
該熱延鋼板に熱延板焼鈍を施し、
該熱延板焼鈍後の熱延鋼板に、1回または中間焼鈍をはさむ2回以上の冷間圧延を施して最終板厚を有する冷延鋼板とし、
該冷延鋼板に脱炭焼鈍を施し、
該脱炭焼鈍後の冷延鋼板表面にMgOを含む焼鈍分離剤を塗布した後に仕上焼鈍を施す方向性電磁鋼板の製造方法であって、
前記仕上げ焼鈍後の鋼板に、電子ビームの照射による磁区細分化処理を施し、
前記磁区細分化処理は、前記電子ビームの走査方向と直交する方向のビーム径が220μm以下、かつ走査方向のビーム最大強度に対して直交する方向のビーム最大強度比が0.7以上1.3以下にて行う、方向性電磁鋼板の製造方法。 - 前記電子ビームの照射は、1以上のビーム制御コイルを使用して行うことを特徴とする、請求項2に記載の方向性電磁鋼板の製造方法。
- 前記電子ビームを加速電圧90kV以上で照射する、請求項2または3に記載の方向性電磁鋼板の製造方法。
- 前記電子ビームの照射は、スティグメーターを使用して行う、請求項3または4に記載の方向性電磁鋼板の製造方法。
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WO2024070074A1 (ja) * | 2022-09-28 | 2024-04-04 | Jfeスチール株式会社 | 方向性電磁鋼板およびその製造方法並びに変圧器用鉄心 |
Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS60136142A (ja) * | 1983-12-26 | 1985-07-19 | Hitachi Ltd | 電子ビ−ム真円度調整装置 |
WO2013099272A1 (ja) * | 2011-12-28 | 2013-07-04 | Jfeスチール株式会社 | 方向性電磁鋼板およびその製造方法 |
JP2013159850A (ja) * | 2012-02-08 | 2013-08-19 | Jfe Steel Corp | 方向性電磁鋼板およびその製造方法 |
WO2014068962A1 (ja) * | 2012-10-31 | 2014-05-08 | Jfeスチール株式会社 | 方向性電磁鋼板とその製造方法 |
JP2015161024A (ja) * | 2014-02-28 | 2015-09-07 | Jfeスチール株式会社 | 低騒音変圧器用の方向性電磁鋼板およびその製造方法 |
Family Cites Families (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4567369A (en) * | 1982-06-18 | 1986-01-28 | National Research Development Corporation | Correction of astigmatism in electron beam instruments |
EP1279747B1 (en) * | 2001-07-24 | 2013-11-27 | JFE Steel Corporation | A method of manufacturing grain-oriented electrical steel sheets |
TWI305548B (en) | 2005-05-09 | 2009-01-21 | Nippon Steel Corp | Low core loss grain-oriented electrical steel sheet and method for producing the same |
JP5919617B2 (ja) | 2010-08-06 | 2016-05-18 | Jfeスチール株式会社 | 方向性電磁鋼板およびその製造方法 |
JP5593942B2 (ja) | 2010-08-06 | 2014-09-24 | Jfeスチール株式会社 | 方向性電磁鋼板およびその製造方法 |
JP5712667B2 (ja) | 2011-02-21 | 2015-05-07 | Jfeスチール株式会社 | 方向性電磁鋼板の製造方法 |
IN2014MN01092A (ja) * | 2011-12-22 | 2015-07-03 | Jfe Steel Corp | |
JP6010907B2 (ja) | 2011-12-28 | 2016-10-19 | Jfeスチール株式会社 | 方向性電磁鋼板およびその製造方法 |
JP5954421B2 (ja) | 2012-08-30 | 2016-07-20 | Jfeスチール株式会社 | 鉄心用方向性電磁鋼板およびその製造方法 |
RU2613818C1 (ru) | 2013-02-28 | 2017-03-21 | ДжФЕ СТИЛ КОРПОРЕЙШН | Способ изготовления листа из текстурированной электротехнической стали |
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Patent Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS60136142A (ja) * | 1983-12-26 | 1985-07-19 | Hitachi Ltd | 電子ビ−ム真円度調整装置 |
WO2013099272A1 (ja) * | 2011-12-28 | 2013-07-04 | Jfeスチール株式会社 | 方向性電磁鋼板およびその製造方法 |
JP2013159850A (ja) * | 2012-02-08 | 2013-08-19 | Jfe Steel Corp | 方向性電磁鋼板およびその製造方法 |
WO2014068962A1 (ja) * | 2012-10-31 | 2014-05-08 | Jfeスチール株式会社 | 方向性電磁鋼板とその製造方法 |
JP2015161024A (ja) * | 2014-02-28 | 2015-09-07 | Jfeスチール株式会社 | 低騒音変圧器用の方向性電磁鋼板およびその製造方法 |
Non-Patent Citations (1)
Title |
---|
See also references of EP3409796A4 * |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP7420326B1 (ja) | 2022-09-28 | 2024-01-23 | Jfeスチール株式会社 | 方向性電磁鋼板およびその製造方法並びに変圧器用鉄心 |
WO2024070074A1 (ja) * | 2022-09-28 | 2024-04-04 | Jfeスチール株式会社 | 方向性電磁鋼板およびその製造方法並びに変圧器用鉄心 |
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