WO2015129255A1 - 低騒音変圧器用の方向性電磁鋼板およびその製造方法 - Google Patents
低騒音変圧器用の方向性電磁鋼板およびその製造方法 Download PDFInfo
- Publication number
- WO2015129255A1 WO2015129255A1 PCT/JP2015/000934 JP2015000934W WO2015129255A1 WO 2015129255 A1 WO2015129255 A1 WO 2015129255A1 JP 2015000934 W JP2015000934 W JP 2015000934W WO 2015129255 A1 WO2015129255 A1 WO 2015129255A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- region
- irradiation
- steel sheet
- electron beam
- modulated
- Prior art date
Links
Images
Classifications
-
- 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
- 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
-
- 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
-
- 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
- C21D10/00—Modifying the physical properties by methods other than heat treatment or deformation
-
- 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
- C21D8/1216—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
-
- 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
- C21D8/1294—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
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- 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
- H01F1/147—Alloys characterised by their composition
- H01F1/14766—Fe-Si based alloys
- H01F1/14775—Fe-Si based alloys in the form of sheets
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- 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
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F3/00—Cores, Yokes, or armatures
- H01F3/02—Cores, Yokes, or armatures made from sheets
-
- 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
- H01F41/02—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 manufacturing cores, coils, or magnets
-
- 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
- H01F41/02—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 manufacturing cores, coils, or magnets
- H01F41/0206—Manufacturing of magnetic cores by mechanical means
- H01F41/0233—Manufacturing of magnetic circuits made from sheets
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/06—Surface hardening
- C21D1/09—Surface hardening by direct application of electrical or wave energy; by particle radiation
-
- 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
Definitions
- the present invention relates to a grain-oriented electrical steel sheet for a low noise transformer and a method for manufacturing the same.
- a technique for subdividing the magnetic domains of grain-oriented electrical steel sheets there is a technique in which the effect does not disappear even when strain relief annealing is performed, such as forming grooves on the steel sheet surface.
- the present invention is an electron known as one of techniques for subdividing magnetic domains and reducing iron loss by introducing strain into the steel sheet surface layer such as laser irradiation, plasma jet flame irradiation, and marking. It is a technique that uses a beam irradiation method, and is particularly intended to simultaneously achieve low iron loss and low magnetostriction.
- Patent Document 1 discloses a method for manufacturing a grain-oriented electrical steel sheet having a magnetic flux density B 8 exceeding 1.97T.
- the iron loss can be improved by increasing the purity of the material, high orientation, reducing the plate thickness, adding Si, Al, and subdividing the magnetic domain (for example, Non-Patent Document 1).
- the iron loss tends to deteriorate.
- the crystal orientation is highly integrated in the Goss orientation for the purpose of improving B 8
- the magnetostatic energy decreases, the domain width increases, and the eddy current loss increases. Therefore, as a method of reducing such eddy current loss, a technique is used in which the above-described tension coating is applied, or a magnetic domain is subdivided by introducing thermal strain into the steel sheet surface layer to reduce iron loss. .
- Patent Document 3 discloses that laser scanning irradiation is performed under certain conditions to impart thermal strain to the steel sheet
- Patent Document 4 discloses a pulse Q-switched laser having a half width of 10 nsec or more and 1 ⁇ sec or less.
- a technology to reduce iron loss by subdividing magnetic domains by concentrating the light intensity of 1 ⁇ 10 5 to 1 ⁇ 10 8 W / cm 2 and intermittently applying thermal strain to the steel sheet is disclosed. Has been.
- Patent Document 5 describes that a hardened region generated in a steel sheet surface layer by laser irradiation or the like, that is, a plastic strain region obstructs domain wall movement and increases hysteresis loss.
- the strain concentrates locally on a part of the surface layer of the steel sheet, and the effect of reducing iron loss is not sufficient, and the effect of reducing iron loss is insufficient due to the increase in hysteresis loss due to strain.
- magnetostriction due to strain increased.
- Patent Document 5 adjusts the laser output and the spot diameter ratio, reduces the plastic strain region cured by laser irradiation in the direction perpendicular to the laser scanning direction to 0.6 mm or less, and reduces hysteresis loss. By doing so, the iron loss is reduced.
- the plastic strain on the surface of the steel sheet causes an increase in magnetostriction, and as a result, the noise of the transformer increases.
- Patent Document 8 the current value of the electron beam to be irradiated, the traveling speed of the electron beam in the width direction of the steel plate, the irradiation pitch in the rolling direction, and the beam diameter of the electron beam are controlled within a certain range. Discloses a technology for obtaining a grain-oriented electrical steel sheet that is excellent in noise and iron loss by suppressing the occurrence of thermal distortion.
- Non-Patent Document 2 when the magnetic domain of a grain-oriented electrical steel sheet is subdivided by laser light irradiation, the interaction between the laser light and the surface film is strong, which is accompanied by rapid thermal deformation of the steel sheet near the irradiated surface or rapid evaporation of the film. Due to the reaction force on the steel plate, a region with a higher dislocation density is formed on the steel plate near the irradiated portion. As a result, it has been shown that the hardness of the steel sheet increases, and at the same time, the steel sheet is deformed to increase the hysteresis loss (for example, Non-Patent Document 2).
- forming a 90 ° magnetic domain in the steel sheet by forming a region with a higher dislocation density in the vicinity of the irradiated part of the steel sheet surface layer is the basic principle of magnetic domain subdivision by this technology.
- Accompanying the reduction is necessarily accompanied by an increase in hysteresis loss and an increase in magnetostriction. That is, as long as it is a technology for irradiating laser light utilizing thermal distortion as in the prior art, it is not possible to establish all of magnetic domain subdivision, low hysteresis loss, and low magnetostriction.
- the technology that irradiates the electron beam allows electrons to penetrate into the steel sheet rather than the steel sheet surface, so it is considered possible to subdivide the magnetic domain without using plastic strain on the steel sheet surface layer.
- thermal strain is also generated inside the steel sheet, and hysteresis loss and magnetostriction are increased. Therefore, as shown in Patent Document 8, it is necessary to control the surface energy density ⁇ of the electron beam and the energy density ⁇ (energy density on the beam scanning line) of the irradiation part of the electron beam to a certain range.
- the optimum condition of iron loss shown in FIG. 2 of Patent Document 8 and the optimum condition of low noise shown in FIG. 3 are greatly different, and neither of them can find an optimum condition. It was insufficient as a technique to improve.
- the inventors considered that, in general, when an electron beam is irradiated onto a steel sheet, it is possible to find an optimum condition common to both iron loss and magnetostriction by adjusting the energy density of the irradiated portion. That is, the beam irradiation linear density ⁇ disclosed in Patent Document 8 corresponds to this, and a magnetic domain subdividing effect can be obtained by increasing the value of ⁇ from a predetermined minimum value, and by reducing the value from the maximum value, a steel plate It was thought that the plastic strain of the surface layer could be reduced, and as a result, the increase in hysteresis loss and noise could be suppressed.
- the required electron beam irradiation energy intensity is such that the irradiation is performed at an intensity higher than the level at which the magnetic domains elongated and divided in the direction of the irradiation line exist in the electron beam irradiation line region, and the occurrence of thermal distortion on the steel sheet surface is suppressed. It has been clarified that it is an essential technique to suppress the occurrence of film damage on the irradiation side surface of the steel sheet and to perform irradiation at a strength level that does not form a plastic strain region.
- Table 1 shows that the acceleration voltage Vk is 40 kV to 120 kV and the beam is radiated to the directional electrical steel sheet with a plate thickness of 0.23 mm, B 8 of 1.943 T, and iron loss W 17/50 of 0.85 W / kg.
- the lower limit value of the energy density of the irradiated portion includes a divided magnetic domain elongated in the irradiation direction (Non-Patent Document 3).
- the upper limit value of the energy density is an upper limit value at which damage to the coating does not occur.
- FIG. 2 shows the results of examining the relationship between the distance L in the rolling direction of the irradiated region and the iron loss and magnetostriction when the electron beam irradiation is performed under the above conditions 1 and 2.
- the gist configuration of the present invention is as follows. 1.
- the surface of the steel sheet is irradiated with an electron beam having a beam diameter d of 0.40 mm or less on a line region in a direction intersecting with the rolling direction, and the irradiation line region is a repeating unit composed of two types of regions including a stay region and a traveling region.
- a modulated irradiation region in which the repeating units are connected in the direction of the line region The period in the modulated irradiation region of the repeating unit is 2/3 ⁇ d to 2.5 ⁇ dmm,
- the repetition interval in the rolling direction of the modulated irradiation region is set to 4.0 to 12.5 mm, and the intensity of the electron beam is at least equal to or more than the strength at which the elongated magnetic domains extending in the direction of the modulated irradiation region are formed on the irradiation surface side.
- a grain-oriented electrical steel sheet for a low-noise transformer that has a strength that prevents the occurrence of film damage and the formation of a plastic strain region on the irradiated surface side.
- the surface of the steel sheet is irradiated with an electron beam having a beam diameter d of 0.40 mm or less on a line region in a direction intersecting with the rolling direction, and the irradiation line region is a repeating unit composed of two types of regions including a stay region and a traveling region.
- the present invention it is possible to carry out magnetic domain subdivision processing under conditions that satisfy both the low iron loss and low noise of the transformer, which has been difficult in the past, and the direction of low magnetostriction with low iron loss that has not been achieved conventionally. Since the electromagnetic steel sheet can be obtained, the energy use efficiency in the transformer can be improved and the noise can be suppressed, which is extremely useful industrially.
- the beam diameter and the magnetic domain subdivision when the modulated irradiation region is formed under the condition A (repetition unit period: 0.20 mm). It is a figure which shows the relationship with the iron loss and magnetostriction of the grain-oriented electrical steel sheet after a heat treatment.
- the beam diameter and the magnetic domain subdivision when the modulated irradiation region is formed under the condition B (repetition unit period: 0.50 mm).
- the irradiation object in the present invention is a grain-oriented electrical steel sheet.
- grain-oriented electrical steel sheets are provided with an insulation coating such as a tension coating on the forsterite film on the ground iron, but the present invention provides a forsterite film between the ground iron and the insulation coating. There is no problem even if is not present.
- the magnetic domain refinement process is performed by scanning the surface of the grain-oriented electrical steel sheet with an electron beam in a direction intersecting with the rolling direction and at intervals in the rolling direction.
- the introduction means is limited to electron beam irradiation.
- technologies other than electron beams the interaction with the insulation coating existing on the surface of the steel sheet is large, and damage to the insulation coating and plastic strain consisting of high dislocation density are introduced into the surface layer of the underlying iron rail. Deterioration, that is, deterioration of iron loss is caused, and the best iron loss characteristic cannot be obtained.
- the interaction with the insulating coating is limited to a small size due to the dynamic action of the electron beam, and the interaction with the ground iron inside the steel plate is increased. Therefore, it is possible to impart the magnetic domain refinement effect without damage of the insulating coating, the forsterite film, or the introduction of plastic strain having a high dislocation density in the surface layer of the base iron immediately below the coating.
- the steel plate surface irradiated with the electron beam may be one side of the steel plate or both sides.
- the direction intersecting the rolling direction is a direction perpendicular to the rolling direction, that is, a range of 75 ° to 105 ° when the sheet width direction of the steel sheet is 90 °. It is suitably exhibited.
- reference numeral 1 is a staying region
- 2 is a traveling region
- 3 is a repeating unit (spacing point interval)
- d indicates a beam diameter.
- the beam diameter d of the electron beam in the modulated irradiation region is set to 0.40 mm or less, and the period of the repeating unit in the modulated irradiation region is required to be 2/3 ⁇ d to 2.5 ⁇ dmm.
- the lower limit of the beam diameter d is 0.10 mm
- the beam diameter is the beam irradiation diameter, and is defined by the half width of the energy profile using a known slit method.
- FIG. 4 shows the results of examining the relationship between the beam diameter d, the iron loss W 17/50, and the magnetostriction ⁇ p -p when the electron beam irradiation is performed under the above conditions. As shown in FIG. It can be seen that when the beam diameter d is larger than 0.40 mm, not only the iron loss is deteriorated but also the magnetostriction becomes remarkably large.
- FIGS. 5 and 6 show the results of examining the relationship between the beam diameter, the iron loss, and the magnetostriction when the electron beam irradiation is performed under the two conditions A and B described above.
- the beam diameter d (mm) of the electron beam is 0.40 mm or less, and the period of the repeating unit is in the range of 2/3 ⁇ d to 2.5 ⁇ dmm in relation to the beam diameter d.
- the lower limit of the beam diameter was set to 0.10 mm because it is disadvantageous for the generation of the divided magnetic domains if the beam diameter is too small compared to the magnetic domain width. Therefore, the lower limit of the beam diameter d is preferably about 0.10 mm.
- the repetition interval in the rolling direction of the above-described modulated irradiation region needs to be 4.0 to 12.5 mm.
- the repetition interval in the rolling direction of the modulated irradiation region is less than 4.0 mm, the iron loss increases as shown in FIG. 2, and the magnetostriction also deteriorates.
- the repeat interval in the rolling direction must be 4.0 to 12.5 mm.
- the range is preferably 5.0 to 10 mm.
- the inventors examined the influence of the acceleration voltage of the electron beam.
- the acceleration voltage of the electron beam is high, electrons penetrate deeper into the steel sheet, and it is considered that the magnetic domain fragmentation of the directional electrical steel sheet having a large thickness is particularly effective. Therefore, the following examination was performed.
- the acceleration voltage of the electron beam is desirably 100 kV or more.
- the upper limit is preferably about 300 kV.
- the outer shape of the transformer is composed of a steel plate having a 500 mm square and a width of 100 mm. Cut the steel plate into a shape as shown in Fig. 8, stack it with a stacking thickness of 100mm, tighten it with a band, and then wind the secondary coil and primary coil around the legs of the steel plate and put it in a tank filled with insulating oil The measurement was carried out by connecting the measuring instrument.
- the three phases are excited by using a primary coil with a 120 ° phase shift, and the cross-sectional area is obtained from the weight of the iron core generated from the induced voltage generated in the secondary coil. It was measured.
- the noise was expressed in dBA units where vibration sound generated around the transformer with a microphone was recorded and A scale correction was performed.
- the iron loss was expressed as a loss per weight of the transformer by subtracting the copper loss from the voltage and current value on the primary coil side in the unloaded state with the secondary coil open.
- Example 1 Has a forsterite film on the steel sheet surface, the sheet thickness was baked tension coating thereon: 0.23 mm, the magnetic flux density B 8: 1.939T, iron loss W 17/50: oriented electrical steel sheet 0.837W / kg 8
- magnetic domain subdivision means electron beam irradiation with acceleration voltage: 150kV, beam current: 5.0mA, beam diameter: 0.18mm is used, and irradiation is continuously performed at a scanning speed of 40m / sec under constant irradiation conditions in the plate width direction. And one was irradiated with an interval in the rolling direction of 5.0 mm (Comparative Example A1) and the other was 7.5 mm (Comparative Example A2). In these comparative examples, a part where the coating partly peeled off was confirmed.
- the other two were irradiated with an electron beam under the same conditions as described above, but the residence time was 0.005 msec, the residence point interval was 0.20 mm, and the residence unit and the running region were repeated units. And a modulated irradiation region was formed at an average scanning speed of 40 m / sec. At this time, one was irradiated with a repetition interval in the rolling direction of 5.0 mm (Invention Example A3), and the other was 7.5 mm (Invention Example A4). In these inventive examples, no damage to the coating was observed, and magnetic domains that were elongated and divided in the plate width direction were observed on the irradiated region by magnetic domain observation by the bitter method.
- the repetition interval in the rolling direction is 5.0 mm and the electron beam is irradiated under the same conditions, but the residence time is 0.0025 msec and the residence point interval is 0.10 mm as the repeating unit of the residence region and the traveling region. Then, repeating units were connected in the plate width direction, and a modulated irradiation region was formed at an average scanning speed of 40 m / sec (Comparative Example A5). Furthermore, the other is that the repetition interval in the rolling direction is 5.0 mm and the electron beam is irradiated under the same conditions, but the residence time is 0.016 msec and the residence point interval is 0.48 mm as the repeating unit of the residence region and the traveling region. Then, repeating units were connected in the plate width direction, and a modulated irradiation region was formed at an average scanning speed of 40 m / sec (Comparative Example A6).
- the remaining two were subjected to discontinuous pulse irradiation in the plate width direction of the steel sheet using an Nd: YAG laser device equipped with a Q switch.
- the irradiation conditions at this time are conventionally known conditions, that is, the laser pulse energy is 3.3 mJ / pulse, the laser spot size is a circle with a diameter of 0.18 mm, the irradiation interval in the plate width direction is 0.3 mm, and the laser wavelength is 1064 nm. It was.
- One irradiation interval in the rolling direction was 5.0 mm (Comparative Example A7) and the other was 7.5 mm (Comparative Example A8).
- a clear circular coating defect and bare iron bareness were observed in the place where the laser beam was received, so the insulating coating was thinly reapplied and baked at a low temperature to improve insulation. .
- the magnetic domain refined grain-oriented electrical steel sheet produced by the method of the present invention is superior in iron loss characteristic and magnetostriction characteristic to the comparative example, and in the iron loss and noise characteristic of the transformer. Is also excellent. Furthermore, it should be noted that when the irradiation interval in the rolling direction is 7.5 mm, unlike the comparative example technique, both the iron loss and noise show the best values, and as a grain oriented electrical steel sheet for transformers It turns out that it has the outstanding effect.
- Example 2 Has a forsterite film on the steel sheet surface, the sheet thickness was baked tension coating thereon: 0.27 mm, the magnetic flux density B 8: 1.941T, iron loss W 17/50: oriented electrical steel sheet 0.918W / kg 8
- magnetic domain subdivision means electron beam irradiation with acceleration voltage: 60kV, beam current: 10mA, beam diameter: 0.30mm is used, and irradiation is continuously performed at a scanning speed of 30m / sec under constant irradiation conditions in the plate width direction. And one was irradiated with an interval in the rolling direction of 5.0 mm (Comparative Example B1) and the other was 7.5 mm (Comparative Example B2). In these comparative examples, a part where the coating partly peeled off was confirmed.
- the other two were irradiated with an electron beam under the same conditions as above, but the residence time: 0.010 msec and the residence point interval: 0.30 mm was used as the repeat unit for the residence region and travel region, and the repeat unit in the plate width direction. And a modulated irradiation region was formed at an average scanning speed of 30 m / sec. At this time, one was irradiated with a repetition interval in the rolling direction of 5.0 mm (Invention Example B3), and the other was 7.5 mm (Invention Example B4). In these inventive examples, no damage to the coating was observed, and magnetic domains that were elongated and divided in the plate width direction were observed on the irradiated region by magnetic domain observation by the bitter method.
- the repetition interval in the rolling direction is 5.0 mm and the electron beam is irradiated under the same conditions, but the residence time is 0.005 msec and the residence point interval is 0.15 mm as the repeating unit of the residence region and the traveling region. Then, repeating units were connected in the plate width direction, and a modulated irradiation region was formed at an average scanning speed of 30 m / sec (Comparative Example B5). Furthermore, the other is that the repetition interval in the rolling direction is 5.0 mm and the electron beam is irradiated under the same conditions, but the residence time is 0.03 msec and the residence point interval is 0.90 mm as the repeating unit of the residence region and the traveling region. Then, repeating units were connected in the plate width direction, and a modulated irradiation region was formed at an average scanning speed of 30 m / sec (Comparative Example B6).
- the remaining two were subjected to discontinuous pulse irradiation in the plate width direction of the steel sheet using an Nd: YAG laser device equipped with a Q switch.
- the irradiation conditions at this time are conventionally known conditions, that is, the laser pulse energy is 4.5 mJ / pulse, the laser spot size is a circle with a diameter of 0.22 mm, the irradiation interval in the plate width direction is 0.3 mm, and the laser wavelength is 1064 nm. It was.
- One irradiation interval in the rolling direction was 5.0 mm (Comparative Example B7), and the other was 7.5 mm (Comparative Example B8).
- a clear circular coating defect and bare iron bareness were observed in the place where the laser beam was received, so the insulation coating was thinly reapplied and baked at a low temperature to improve insulation. It was.
- the grain-oriented grain-oriented electrical steel sheet produced by the method of the present invention is superior in iron loss characteristics and magnetostriction characteristics as compared with the comparative example, and in the iron loss and noise characteristics of the transformer. Is also excellent. Furthermore, it should be noted that when the irradiation interval in the rolling direction is set to 7.5 mm, the iron loss and the noise both show the best values, unlike the comparative example technique, as a grain-oriented electrical steel sheet for transformers. It turns out that it has the outstanding effect.
Landscapes
- Engineering & Computer Science (AREA)
- Chemical & Material Sciences (AREA)
- Physics & Mathematics (AREA)
- Mechanical Engineering (AREA)
- Power Engineering (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Electromagnetism (AREA)
- Dispersion Chemistry (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
- Soft Magnetic Materials (AREA)
- Manufacturing Cores, Coils, And Magnets (AREA)
Abstract
Description
方向性電磁鋼板の磁区を細分化する技術としては、鋼板表面に溝を形成するなど歪取焼鈍を施した場合でもその効果が消失しない手法がある。これに対し、本発明は、レーザ照射やプラズマジェット炎照射、ケガキなどのように鋼板表層に歪みを導入することで磁区を細分化して鉄損を低減する手法の一つとして知られている電子ビーム照射法を利用した技術で、特に低鉄損と低磁歪とを同時に達成しようとするものである。
例えば特許文献1には、1.97Tを超える磁束密度B8を有する方向性電磁鋼板の製造方法が示されている。
しかし、一般に磁束密度B8が高くなると鉄損は劣化する傾向にある。例えば、B8の向上を目的に、結晶方位をGoss方位へ高度に集積させると、静磁エネルギーが下がり、磁区幅が広がって、渦電流損が高くなる。そこで、かような渦電流損を低減する方法として、前述したような張力コーティングを付与したり、鋼板表層に熱歪みを導入して磁区を細分化し、鉄損を低減する技術が利用されている。
例えば、特許文献3には、一定の条件下でレーザスキャニング照射を行うことで鋼板に熱歪みを付与することにより、また特許文献4には、半価幅10nsec以上、1μsec以下のパルスQスイッチレーザを用い、光強度を1×105~1×108 W/cm2として集光し、間欠的に鋼板に熱歪みを付与することにより、磁区を細分化して鉄損を低減する技術が開示されている。
つまり、鋼板表層の照射部近傍に、より転位密度の高い領域を形成させて鋼板に90°磁区を発生させることがこの技術による磁区細分化の基本原理であるので、磁区細分化による渦流損の低減に付随して、必然的にヒステリシス損の増加と磁歪の増大を伴う。すなわち、従来技術のような熱歪みを活用するレーザ光を照射する技術である限り、磁区細分化、低ヒステリシス損化および低磁歪化の全てを鼎立させることはできない。
すなわち、特許文献8に開示されるビーム照射線密度βがこれに相当し、βの値を所定の最小値より大きくすることで磁区細分化効果が得られ、また最大値より小さくすることで鋼板表層の塑性歪みを低減でき、その結果、ヒステリシス損と騒音の増大を抑制することができると考えた。
すなわち、これは特許文献8の図2におけるβ≧10-α/0.06(J/cm2)の領域で優れた鉄損が得られ、特許文献8の図3におけるβ≦11.25-α/0.08(J/cm2)で低騒音が得られることに相当する。
そこで、βの値の本質的な物理作用を求めて鋭意研究を進めた結果、βの値が大きい場合の磁歪劣化については、鋼板表面での熱歪みによる被膜損傷の発生が関与していること、一方βの値が小さい場合には、照射線領域で照射線方向に細長く伸びた分割磁区の消失が磁区細分化の有無の本質であることが判明した。すなわち、必要な電子ビーム照射エネルギー強度としては、電子ビーム照射線領域で照射線方向に細長く伸び分割された磁区が存在するレベル以上の強度で照射すること、かつ鋼板表面の熱歪みの発生を抑え、鋼板の照射側表面の被膜損傷の発生を抑制し、さらに塑性歪領域を形成しない強度レベルで照射することが、本質的な技術であることが解明された。
板厚が0.23mmで、B8が1.943T、鉄損W17/50が0.85W/kgである方向性電磁鋼板に、加速電圧Vk:60kV、ビーム電流I:8.5mA、ビーム径d:0.30mm、走査速度V:30m/secで、圧延方向の照射線間隔Lを2.5~30mmに変更して電子ビームを照射した。その際、一方は一定照射条件(条件1)で連続照射を行って比較例とした。他方は、図1に示すようにビームの滞留領域:1と走行領域:2の合計領域0.45mmを繰返し単位:3(繰返し単位の周期でもある)として鋼板板幅方向へ繰返し照射する変調照射線領域を形成する照射条件(条件2)で照射した。なお、この時、滞留点での滞留時間を0.015msecとし、平均走査速度が30m/secとなるように走行領域:2での走行速度を調節した。
上記の条件1、2で電子ビーム照射を行ったときの、照射線領域の圧延方向の間隔Lと鉄損および磁歪との関係について調べた結果を、図2に示す。
この結果は、磁区細分化処理を施した方向性電磁鋼板を使用して、低鉄損でかつ低騒音な変圧器を同一の材料で得られることを意味しており、今までにない工業的な意味の大きい優れた技術であることが分かる。
本発明は、上記の知見を基にさらに研究を重ねた末に完成されたものである。
1.鋼板表面に対し、圧延方向と交差する方向の線領域にビーム径dが0.40mm以下の電子ビームを照射し、該照射線領域を滞留領域と走行領域からなる2種類の領域を繰返し単位とする変調照射線領域とし、かつ該変調照射線領域を圧延方向に間隔を設けて繰返すことによる磁区細分化処理を施した方向性電磁鋼板において、
該繰返し単位を線領域方向に連結させた変調照射線領域とし、
該繰返し単位の該変調照射線領域における周期を2/3×d~2.5×dmmとし、
該変調照射線領域の圧延方向の繰返し間隔を4.0~12.5mmとし、さらに
電子ビームの強度を、少なくとも照射面側に該変調照射線領域方向に細長く伸びた分割磁区が形成される強度以上で、かつ照射面側に被膜損傷の発生および塑性歪み領域の形成が生じない強度までとした
低騒音変圧器用の方向性電磁鋼板。
該繰返し単位を線領域方向に連結させた変調照射線領域とし、
該繰返し単位の該変調照射線領域における周期を2/3×d~2.5×dmmとし、
該変調照射線領域の圧延方向の繰返し間隔を4.0~12.5mmとし、さらに
電子ビームの強度を、少なくとも照射面側に該変調照射線領域方向に細長く伸びた分割磁区が形成される強度以上で、かつ照射面側に被膜損傷の発生および塑性歪み領域の形成が生じない強度までとする
低騒音変圧器用の方向性電磁鋼板の製造方法。
〔被照射材〕
本発明における照射対象は方向性電磁鋼板である。通常、方向性電磁鋼板には、地鉄の上にあるフォルステライト被膜の上から張力コーティングなどの絶縁コーティングが施されているが、本発明は、地鉄と絶縁コーティングとの間にフォルステライト被膜が存在していなくても問題はない。
本発明では、上記した方向性電磁鋼板の表面に、圧延方向に交差する方向に、かつ圧延方向に間隔を設けて、電子ビームを走査することによって、磁区細分化処理を施すが、鋼板に対する歪み導入手段としては電子ビーム照射に限られる。電子ビーム以外の技術では、鋼板表面に存在する絶縁コーティングとの相互作用が大きく、絶縁コーティングの損傷やその直下の地鉄表層部に高転位密度からなる塑性歪みが導入されるため、ヒステリシス損の劣化、すなわち鉄損の劣化を招き、最良の鉄損特性を得ることができない。
これに対し、電子ビームを使用した場合、電子ビームの動的作用によって絶縁コーティングとの相互作用が小さく限定され、鋼板内部の地鉄との相互作用が大きくなる。したがって、絶縁コーティングの損傷やフォルステライト被膜あるいはコーティング直下の地鉄表層部に高転位密度からなる塑性歪みの導入がない状態で磁区細分化効果を付与することが可能となる。
圧延方向に交差する方向に電子ビームを走査して、電子ビームの照射線領域を形成するが、この照射線領域は、一定の照射条件で照射するいわゆる図3に示すような連続照射ではなく、図1に示したような滞留領域1と走行領域2からなる2種類の領域を繰返し単位として、この繰返し単位を照射線領域方向に連結させて繰返すことにより形成される変調照射線領域とすることが、本発明の最も肝要な技術である。
交差する方向に照射する電子ビームの照射が一定の照射条件で施されるいわゆる連続照射の場合には、図2において条件1として示したように、ほぼ同一の照射条件で最良の鉄損値と最良の磁歪特性を得ることができず、その結果、同一の変圧器で低鉄損と低騒音を満足するものを得ることはできなかった。
ここに、変調照射線領域における電子ビームのビーム径dは0.40mm以下とし、またこの変調照射線領域における繰返し単位の周期は2/3×d~2.5×dmmとする必要がある。但し、ビーム径dの下限は0.10mmで、ビーム径はビーム照射径であり、公知のスリット法を用い、エネルギープロファイルの半値幅で規定したものとする。
〔実験1〕
板厚が0.23mmで、B8が1.937T、鉄損W17/50が0.86W/kgの方向性電磁鋼板に、加速電圧:60kV、ビーム電流:9mAの電子ビームを、試料と電子ビーム間の距離を変えることでビーム径を0.20mm~0.60mmと変化させて、圧延方向の間隔:6mmで、板幅方向に、滞留時間0.010msecで滞留点間隔0.45mmを滞留領域および走行領域の繰返し単位とし、板幅方向に繰返し単位を連結させて変調照射線領域を形成した(平均走査速度は30m/s)。
図4に示したとおり。ビーム径dが0.40mmより大きい条件では、鉄損が劣化するだけでなく、磁歪が著しく大きくなることが分かる。
板厚が0.23mmで、B8が1.942T、鉄損W17/50が0.85W/kgの方向性電磁鋼板に、加速電圧:60kV、ビーム電流:9mAの電子ビームを、試料と電子ビーム間の距離を変えることでビーム径を0.10mm~0.40mmと変化させて、圧延方向の間隔:6mmで、板幅方向に、滞留時間0.008msecで滞留点間隔0.20mmを滞留領域および走行領域の繰返し単位とする条件A(平均走査速度は25m/s)、および滞留時間0.02msecで滞留点間隔0.50mmを滞留領域および走行領域の繰返し単位とする条件B(平均走査速度は25m/s)で、板幅方向に繰返し単位を連結させて変調照射線領域を形成した。
上記のA,B2つの条件で電子ビーム照射を行ったときの、ビーム径と鉄損および磁歪との関係について調べた結果を、図5,6に示す。
すなわち、ビームの滞留領域が重なりすぎた場合には、鉄損低減効果に比して、局所的な歪増大による磁歪増大の影響が大きすぎ、一方、磁区幅に比してビームの滞留領域が離れすぎた場合には、十分な磁区細分化効果が得られないと考えられる。
この変調照射線領域の圧延方向の繰返し間隔が4.0mm未満の場合、図2に示したように鉄損が増大し、かつ磁歪も劣化する。逆に12.5mmを超える場合も、鉄損が増大し、かつ磁歪も劣化するので、圧延方向繰返し間隔を4.0~12.5mmとする必要がある。好ましくは5.0~10mmの範囲である。
そこで以下の検討を行った。
板厚が0.27mmで、B8が1.945T、鉄損W17/50が0.93W/kgの方向性電磁鋼板に、表2に示す加速電圧とビーム電流の電子ビーム(ビーム出力は一定)を、条件ごとに試料と電子ビーム間の距離を変えることでビーム径を0.20mmと一定にし、圧延方向の間隔:8mmで、板幅方向に、滞留時間0.0075msecで滞留点間隔0.30mmを滞留領域および走行領域の繰返し単位とし、板幅方向に繰返し単位を連結させて変調照射線領域を形成した(平均走査速度は40m/s)。
表2に示す条件で電子ビーム照射を行ったときの、鉄損および磁歪について調べた結果を、表2に併記する。
次に、電子ビームの強度については、特許文献8に開示されるビーム照射線密度βの値により定めるよりも、少なくとも照射面側にこの変調照射線領域方向に細長く伸びた分割磁区が形成される強度をもって下限値とし、照射面側に被膜損傷が発生しない強度をもって上限値とする技術を用いる方が簡便、かつ実用的である。
そこで、本発明では、この技術を採用するものとした。
変圧器の鉄損および騒音は、図7に示すような三相三脚の積み鉄心型の変圧器を用いて評価した。図7に示したように、変圧器の外形は500mm角、幅100mmの鋼板で構成される。鋼板を図8に示すような形状に斜角切断し、積み厚を100mmとして積層し、バンドで締付け、その後2次コイルおよび1次コイルを鋼板の脚部に巻き、絶縁油を入れたタンクに装入して測定器具を接続し、測定を行った。
三相は120°位相をずらして1次コイルを用いて励磁を行い、2次コイルに発生する誘導電圧値から鉄心重量より断面積を求めて、鉄心の磁束密度1.7Tにおける鉄損および騒音を測定した。騒音は、マイクで変圧器の周囲で発生する振動音を収録し、Aスケール補正を行ったdBA単位で表した。また、鉄損は、2次コイルを開放状態とした無負荷状態の1次コイル側の電圧と電流値より銅損分を差し引いて変圧器の重量当たりの損失で表した。
鋼板表面にフォルステライト被膜を有し、その上に張力コーティングを焼付けた板厚:0.23mm、磁束密度B8:1.939T、鉄損W17/50:0.837W/kgの方向性電磁鋼板を8分割し、それぞれに次の条件で磁区細分化処理を施した。
磁区細分化手段としては、加速電圧:150kVでビーム電流:5.0mA、ビーム径:0.18mmの電子ビーム照射を用い、板幅方向に一定の照射条件で連続的に40m/secの走査速度で照射し、かつ一つは圧延方向における間隔を5.0mm(比較例A1)、他の一つは7.5mm(比較例A2)として照射し、比較例とした。これらの比較例においては、一部コーティングが剥落した箇所が確認された。
さらに、他の一つは、圧延方向の繰り返し間隔を5.0mmとし、同じ条件の電子ビームを照射したが、滞留時間:0.016msecで滞留点間隔:0.48mmを滞留領域および走行領域の繰返し単位とし、板幅方向に繰返し単位を連結させ、平均走査速度:40m/secで変調照射線領域を形成した(比較例A6)。
鋼板表面にフォルステライト被膜を有し、その上に張力コーティングを焼付けた板厚:0.27mm、磁束密度B8:1.941T、鉄損W17/50:0.918W/kgの方向性電磁鋼板を8分割し、それぞれに次の条件で磁区細分化処理を施した。
磁区細分化手段としては、加速電圧:60kVで、ビーム電流:10mA、ビーム径:0.30mmの電子ビーム照射を用い、板幅方向に一定の照射条件で連続的に30m/secの走査速度で照射し、かつ一つは圧延方向における間隔を5.0mm(比較例B1)、他の一つは7.5mm(比較例B2)として照射し、比較例とした。これらの比較例においては、一部コーティングが剥落した箇所が確認された。
さらに、他の一つは、圧延方向の繰り返し間隔を5.0mmとし、同じ条件の電子ビームを照射したが、滞留時間:0.03msecで滞留点間隔:0.90mmを滞留領域および走行領域の繰返し単位とし、板幅方向に繰返し単位を連結させ、平均走査速度:30m/secで変調照射線領域を形成した(比較例B6)。
2 走行領域
3 繰返し単位(滞留点間隔)
Claims (6)
- 鋼板表面に対し、圧延方向と交差する方向の線領域にビーム径dが0.40mm以下の電子ビームを照射し、該照射線領域を滞留領域と走行領域からなる2種類の領域を繰返し単位とする変調照射線領域とし、かつ該変調照射線領域を圧延方向に間隔を設けて繰返すことによる磁区細分化処理を施した方向性電磁鋼板において、
該繰返し単位を線領域方向に連結させた変調照射線領域とし、
該繰返し単位の該変調照射線領域における周期を2/3×d~2.5×dmmとし、
該変調照射線領域の圧延方向の繰返し間隔を4.0~12.5mmとし、さらに
電子ビームの強度を、少なくとも照射面側に該変調照射線領域方向に細長く伸びた分割磁区が形成される強度以上で、かつ照射面側に被膜損傷の発生および塑性歪み領域の形成が生じない強度までとした
低騒音変圧器用の方向性電磁鋼板。 - 前記電子ビームの加速電圧を100kV以上とした請求項1に記載の低騒音変圧器用の方向性電磁鋼板。
- 前記変調照射線領域の圧延方向の繰返し間隔を5.0~10mmとした請求項1または2に記載の低騒音変圧器用の方向性電磁鋼板。
- 鋼板表面に対し、圧延方向と交差する方向の線領域にビーム径dが0.40mm以下の電子ビームを照射し、該照射線領域を滞留領域と走行領域からなる2種類の領域を繰返し単位とする変調照射線領域とし、かつ該変調照射線領域を圧延方向に間隔を設けて繰返すことからなる磁区細分化処理を施して方向性電磁鋼板を製造するに際し、
該繰返し単位を線領域方向に連結させた変調照射線領域とし、
該繰返し単位の該変調照射線領域における周期を2/3×d~2.5×dmmとし、
該変調照射線領域の圧延方向の繰返し間隔を4.0~12.5mmとし、さらに
電子ビームの強度を、少なくとも照射面側に該変調照射線領域方向に細長く伸びた分割磁区が形成される強度以上で、かつ照射面側に被膜損傷の発生および塑性歪み領域の形成が生じない強度までとする
低騒音変圧器用の方向性電磁鋼板の製造方法。 - 前記電子ビームの加速電圧を100kV以上とする請求項4に記載の低騒音変圧器用の方向性電磁鋼板の製造方法。
- 前記変調照射線領域の圧延方向の繰返し間隔を5.0~10mmとする請求項4または5に記載の低騒音変圧器用の方向性電磁鋼板の製造方法。
Priority Applications (6)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
KR1020167026091A KR20160126015A (ko) | 2014-02-28 | 2015-02-24 | 저소음 변압기용의 방향성 전자 강판 및 그 제조 방법 |
US15/121,791 US20170016085A1 (en) | 2014-02-28 | 2015-02-24 | Grain-oriented electrical steel sheet for low-noise transformer, and method of manufacturing said sheet |
CN201580010242.1A CN106029917A (zh) | 2014-02-28 | 2015-02-24 | 低噪声变压器用取向性电磁钢板及其制造方法 |
EP15754530.2A EP3112480A4 (en) | 2014-02-28 | 2015-02-24 | Grain-oriented electrical steel sheet for low-noise transformer, and method for manufacturing said sheet |
CA2939336A CA2939336C (en) | 2014-02-28 | 2015-02-24 | Grain-oriented electrical steel sheet for low-noise transformer, and method for manufacturing said sheet |
MX2016010883A MX2016010883A (es) | 2014-02-28 | 2015-02-24 | Lamina de acero electrico de grano orientado para transformador de bajo nivel de ruido, y metodo para la fabricacion de dicha lamina. |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2014-039169 | 2014-02-28 | ||
JP2014039169A JP2015161024A (ja) | 2014-02-28 | 2014-02-28 | 低騒音変圧器用の方向性電磁鋼板およびその製造方法 |
Publications (2)
Publication Number | Publication Date |
---|---|
WO2015129255A1 true WO2015129255A1 (ja) | 2015-09-03 |
WO2015129255A8 WO2015129255A8 (ja) | 2016-08-11 |
Family
ID=54008589
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2015/000934 WO2015129255A1 (ja) | 2014-02-28 | 2015-02-24 | 低騒音変圧器用の方向性電磁鋼板およびその製造方法 |
Country Status (8)
Country | Link |
---|---|
US (1) | US20170016085A1 (ja) |
EP (1) | EP3112480A4 (ja) |
JP (1) | JP2015161024A (ja) |
KR (1) | KR20160126015A (ja) |
CN (1) | CN106029917A (ja) |
CA (1) | CA2939336C (ja) |
MX (1) | MX2016010883A (ja) |
WO (1) | WO2015129255A1 (ja) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2019182154A1 (ja) | 2018-03-22 | 2019-09-26 | 日本製鉄株式会社 | 方向性電磁鋼板及び方向性電磁鋼板の製造方法 |
Families Citing this family (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN108474056A (zh) * | 2016-01-25 | 2018-08-31 | 杰富意钢铁株式会社 | 方向性电磁钢板以及其制造方法 |
WO2019189857A1 (ja) * | 2018-03-30 | 2019-10-03 | Jfeスチール株式会社 | 変圧器用鉄心 |
WO2020255552A1 (ja) | 2019-06-17 | 2020-12-24 | 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 |
KR102276850B1 (ko) * | 2019-12-19 | 2021-07-12 | 주식회사 포스코 | 방향성 전기강판 및 그 자구미세화 방법 |
CN114762911B (zh) | 2021-01-11 | 2023-05-09 | 宝山钢铁股份有限公司 | 一种低磁致伸缩取向硅钢及其制造方法 |
Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2012036450A (ja) * | 2010-08-06 | 2012-02-23 | Jfe Steel Corp | 方向性電磁鋼板およびその製造方法 |
JP2012036445A (ja) * | 2010-08-06 | 2012-02-23 | Jfe Steel Corp | 方向性電磁鋼板およびその製造方法 |
JP2012172191A (ja) * | 2011-02-21 | 2012-09-10 | Jfe Steel Corp | 方向性電磁鋼板の製造方法 |
WO2013046716A1 (ja) * | 2011-09-28 | 2013-04-04 | 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 |
JP2013072116A (ja) * | 2011-09-28 | 2013-04-22 | Jfe Steel Corp | 方向性電磁鋼板およびその製造方法 |
WO2013100200A1 (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 |
Family Cites Families (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4195750A (en) | 1977-09-29 | 1980-04-01 | Rieke Corporation | Molded flange for drums or other containers |
GB2012481B (en) | 1978-01-09 | 1982-04-07 | Rca Corp | Egfet mirrors |
JP2719832B2 (ja) | 1989-06-09 | 1998-02-25 | ユーホーケミカル株式会社 | はんだペースト |
JP3023242B2 (ja) | 1992-05-29 | 2000-03-21 | 川崎製鉄株式会社 | 騒音特性の優れた低鉄損一方向性珪素鋼板の製造方法 |
JP2563730B2 (ja) | 1992-08-07 | 1996-12-18 | 新日本製鐵株式会社 | パルスco2レーザを用いた方向性電磁鋼板の鉄損改善方法 |
US5296051A (en) * | 1993-02-11 | 1994-03-22 | Kawasaki Steel Corporation | Method of producing low iron loss grain-oriented silicon steel sheet having low-noise and superior shape characteristics |
JP4123679B2 (ja) | 2000-04-25 | 2008-07-23 | Jfeスチール株式会社 | 方向性電磁鋼板の製造方法 |
JP4344264B2 (ja) | 2004-03-08 | 2009-10-14 | 新日本製鐵株式会社 | 低鉄損一方向性電磁鋼板 |
JP5845848B2 (ja) * | 2010-11-26 | 2016-01-20 | Jfeスチール株式会社 | 方向性電磁鋼板の製造方法 |
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 |
-
2014
- 2014-02-28 JP JP2014039169A patent/JP2015161024A/ja active Pending
-
2015
- 2015-02-24 WO PCT/JP2015/000934 patent/WO2015129255A1/ja active Application Filing
- 2015-02-24 KR KR1020167026091A patent/KR20160126015A/ko active Search and Examination
- 2015-02-24 EP EP15754530.2A patent/EP3112480A4/en not_active Withdrawn
- 2015-02-24 US US15/121,791 patent/US20170016085A1/en not_active Abandoned
- 2015-02-24 MX MX2016010883A patent/MX2016010883A/es unknown
- 2015-02-24 CN CN201580010242.1A patent/CN106029917A/zh active Pending
- 2015-02-24 CA CA2939336A patent/CA2939336C/en active Active
Patent Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2012036450A (ja) * | 2010-08-06 | 2012-02-23 | Jfe Steel Corp | 方向性電磁鋼板およびその製造方法 |
JP2012036445A (ja) * | 2010-08-06 | 2012-02-23 | Jfe Steel Corp | 方向性電磁鋼板およびその製造方法 |
JP2012172191A (ja) * | 2011-02-21 | 2012-09-10 | Jfe Steel Corp | 方向性電磁鋼板の製造方法 |
WO2013046716A1 (ja) * | 2011-09-28 | 2013-04-04 | 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 |
JP2013072116A (ja) * | 2011-09-28 | 2013-04-22 | Jfe Steel Corp | 方向性電磁鋼板およびその製造方法 |
WO2013100200A1 (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 |
Non-Patent Citations (1)
Title |
---|
See also references of EP3112480A4 * |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2019182154A1 (ja) | 2018-03-22 | 2019-09-26 | 日本製鉄株式会社 | 方向性電磁鋼板及び方向性電磁鋼板の製造方法 |
KR20200121873A (ko) | 2018-03-22 | 2020-10-26 | 닛폰세이테츠 가부시키가이샤 | 방향성 전자 강판 및 방향성 전자 강판의 제조 방법 |
US11562840B2 (en) | 2018-03-22 | 2023-01-24 | Nippon Steel Corporation | Grain-oriented electrical steel sheet and method for producing grain-oriented electrical steel sheet |
Also Published As
Publication number | Publication date |
---|---|
CA2939336A1 (en) | 2015-09-03 |
US20170016085A1 (en) | 2017-01-19 |
EP3112480A4 (en) | 2017-03-29 |
MX2016010883A (es) | 2016-10-26 |
JP2015161024A (ja) | 2015-09-07 |
KR20160126015A (ko) | 2016-11-01 |
CA2939336C (en) | 2018-09-04 |
CN106029917A (zh) | 2016-10-12 |
EP3112480A1 (en) | 2017-01-04 |
WO2015129255A8 (ja) | 2016-08-11 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
WO2015129255A1 (ja) | 低騒音変圧器用の方向性電磁鋼板およびその製造方法 | |
US11772199B2 (en) | Grain-oriented electrical steel sheet and magnetic domain refinement method therefor | |
JP6200908B2 (ja) | 方向性電磁鋼板の製造方法 | |
KR101421391B1 (ko) | 방향성 전기 강판 | |
US10465259B2 (en) | Grain-oriented electrical steel sheet and production method therefor | |
WO2012017654A1 (ja) | 方向性電磁鋼板およびその製造方法 | |
US20220127692A1 (en) | Grain-oriented electrical steel sheet, and method of manufacturing same | |
JPWO2016063317A1 (ja) | 方向性電磁鋼板 | |
WO2015129253A1 (ja) | 低騒音変圧器用の方向性電磁鋼板およびその製造方法 | |
JP2014512453A (ja) | 方向性平鋼製品の製造方法 | |
JPH01281709A (ja) | コアロス減少のため電気用鋼において耐熱性の細分化磁区を得る方法 | |
JP6015723B2 (ja) | 低騒音変圧器鉄心用方向性電磁鋼板の製造方法 | |
US20230060105A1 (en) | Grain-oriented electrical steel sheet and magnetic domain refinement method thereof | |
JP7180763B2 (ja) | 方向性電磁鋼板およびその製造方法 | |
JP2013159850A (ja) | 方向性電磁鋼板およびその製造方法 | |
JP7287506B2 (ja) | 方向性電磁鋼板 | |
JP7459955B2 (ja) | 方向性電磁鋼板 | |
JP5867126B2 (ja) | 方向性電磁鋼板の鉄損改善方法およびその装置 | |
JP2013072094A (ja) | 方向性電磁鋼板の製造方法及び製造装置 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 15754530 Country of ref document: EP Kind code of ref document: A1 |
|
REEP | Request for entry into the european phase |
Ref document number: 2015754530 Country of ref document: EP |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2015754530 Country of ref document: EP |
|
ENP | Entry into the national phase |
Ref document number: 2939336 Country of ref document: CA |
|
WWE | Wipo information: entry into national phase |
Ref document number: MX/A/2016/010883 Country of ref document: MX |
|
WWE | Wipo information: entry into national phase |
Ref document number: 15121791 Country of ref document: US |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
REG | Reference to national code |
Ref country code: BR Ref legal event code: B01A Ref document number: 112016019615 Country of ref document: BR |
|
ENP | Entry into the national phase |
Ref document number: 20167026091 Country of ref document: KR Kind code of ref document: A |
|
ENP | Entry into the national phase |
Ref document number: 112016019615 Country of ref document: BR Kind code of ref document: A2 Effective date: 20160824 |