WO2023190963A1 - ナノ結晶合金薄帯の製造方法、及び磁性シートの製造方法 - Google Patents

ナノ結晶合金薄帯の製造方法、及び磁性シートの製造方法 Download PDF

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WO2023190963A1
WO2023190963A1 PCT/JP2023/013352 JP2023013352W WO2023190963A1 WO 2023190963 A1 WO2023190963 A1 WO 2023190963A1 JP 2023013352 W JP2023013352 W JP 2023013352W WO 2023190963 A1 WO2023190963 A1 WO 2023190963A1
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Prior art keywords
alloy ribbon
ribbon
nanocrystalline alloy
adhesive layer
nanocrystalline
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English (en)
French (fr)
Japanese (ja)
Inventor
雄一 小川
詞 豊永
興平 宮野
安男 栗山
建史 福山
純 和田
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Proterial Ltd
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Proterial Ltd
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Priority to JP2024512836A priority Critical patent/JPWO2023190963A1/ja
Priority to US18/852,692 priority patent/US20250129447A1/en
Priority to EP23780971.0A priority patent/EP4491749A4/en
Priority to CN202380031853.9A priority patent/CN118974288A/zh
Publication of WO2023190963A1 publication Critical patent/WO2023190963A1/ja
Anticipated expiration legal-status Critical
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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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C45/00—Amorphous alloys
    • C22C45/02—Amorphous alloys with iron as the major constituent
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/001—Heat treatment of ferrous alloys containing Ni
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/007—Heat treatment of ferrous alloys containing Co
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment
    • C21D8/125—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment with application of tension
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties characterised by the heat treatment
    • C21D8/1272—Final recrystallisation annealing
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1277—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/11—Making amorphous alloys
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • H01F1/153—Amorphous metallic alloys, e.g. glassy metals
    • H01F1/15308—Amorphous metallic alloys, e.g. glassy metals based on Fe/Ni
    • 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
    • H01F1/153—Amorphous metallic alloys, e.g. glassy metals
    • H01F1/15333—Amorphous metallic alloys, e.g. glassy metals containing nanocrystallites, e.g. obtained by annealing
    • 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
    • H01F1/153—Amorphous metallic alloys, e.g. glassy metals
    • H01F1/15383—Applying coatings thereon
    • 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
    • H01F41/0213—Manufacturing of magnetic circuits made from strip(s) or ribbon(s)
    • 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
    • C21D2201/03—Amorphous or microcrystalline structure
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C2200/00—Crystalline structure
    • C22C2200/04—Nanocrystalline
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C2202/00—Physical properties
    • C22C2202/02—Magnetic

Definitions

  • the present disclosure relates to a method of manufacturing a nanocrystalline alloy ribbon having a nanocrystalline structure, and a method of manufacturing a magnetic sheet using the nanocrystalline alloy ribbon.
  • Nanocrystalline alloy ribbons with a nanocrystalline structure are known.
  • Nanocrystalline alloy ribbons have excellent magnetic properties such as high magnetic permeability and low loss, and exhibit these excellent magnetic properties over a wide frequency band.
  • Nanocrystalline alloy ribbons are used in magnetic components such as transformers, motors, choke coils, magnetic shields, and current sensors. Many of these magnetic components have higher operating frequencies as semiconductors and other devices become increasingly high-frequency, and as a result, the soft magnetic material used is increasingly being switched to nanocrystalline alloy ribbons. The reason for this is that nanocrystalline alloy ribbons have a high saturation magnetic flux density of 1.2T or more, which is the saturation magnetic flux density necessary to realize further miniaturization of parts. This is because it has excellent characteristics of low magnetostriction and low loss.
  • non-contact charging has been adopted or considered as a charging method for mobile phones, small electrical appliances, electronic devices, electric vehicles, etc.
  • a nanocrystalline alloy ribbon is sometimes used as a magnetic core of a transmitting/receiving coil or a soft magnetic material for a magnetic shield.
  • the main properties required for soft magnetic materials for non-contact charging are high magnetic permeability, low loss, high saturation magnetic flux density, and thinness.
  • the frequency band mainly used for power transfer in non-contact charging is around 100kHz, and the soft magnetic materials mainly used are limited to ferrite and nanocrystalline alloy ribbons.
  • the nanocrystalline alloy ribbon is very thin, about 20 ⁇ m or less in thickness, and has a saturation magnetic flux density about three times that of ferrite. Therefore, the nanocrystalline alloy ribbon is excellent in making it smaller and thinner, and greatly contributes to making the receiving/transmitting coil set smaller and thinner. For this reason, nanocrystalline alloy ribbons have been adopted or are being considered for use in non-contact charging coils for various products.
  • the charging output tends to be increased in order to shorten the charging time, and in order to cope with this, for example, it is preferable to increase the amount of magnetic flux flowing through the soft magnetic material.
  • As a method of compensating for the increase in the amount of magnetic flux it is possible to increase the amount of soft magnetic material used or to switch to a soft magnetic material with a higher saturation magnetic flux density. In particular, the latter is in demand, and nanocrystalline alloy ribbons are being increasingly adopted.
  • the magnetic flux flows from the coil in the thickness direction of the alloy ribbon, and then flows outward in the plane from the center, so it is preferable that the nanocrystalline alloy ribbon has isotropic magnetic properties. .
  • an amorphous alloy ribbon for the nanocrystalline alloy ribbon is produced by casting, and then wound up. Then, a certain amount of amorphous alloy ribbon is unwound from the rolled ribbon, re-wound into a ring-shaped core, and put into a heat treatment furnace as many pieces as the heat treatment furnace allows. Heat treatment at a temperature of 580°C to 580°C. In this way, nanocrystalline alloy ribbons were produced. The heat treatment process using this heat treatment furnace took 5 to 8 hours, including cooling. Nanocrystalline alloy ribbons that have been nanocrystallized through heat treatment are unwound from a ring-shaped core and then laminated or stacked to form a magnetic sheet.
  • the above process adds lamination and layering processes to the conventional manufacturing process of core products using nanocrystalline alloy ribbons.
  • the core is made to match the dimensions of the final product, heat treated, and sent to the subsequent process, so the above manufacturing process is required. There are no unnecessary steps.
  • the thin ribbon is re-wound to create a ring-shaped core for heat treatment, but this step is not always essential.
  • the ring-shaped core made by rewinding a thin ribbon is not used as is, so it is an extra step to re-wind the thin ribbon that has been cast and wound to create a ring-shaped core.
  • the magnetic sheet is preferably manufactured by a process in which a thin ribbon after casting is unwound as it is, continuously heat-treated, and then wound or laminated or laminated as it is.
  • Japanese Patent Publication No. 2014-516386 discloses a process of heat treating an amorphous alloy ribbon under tensile stress in a continuous furnace at a temperature Ta where 450°C ⁇ Ta ⁇ 750°C.
  • the composition of the amorphous alloy ribbon is Fe 100-a-b-c-d-x-y-z Cu a Nb b M c T d Si x B y Z z and impurities of up to 1 at%.
  • M is one or more of the elements Mo
  • T is one or more of the elements V, Mn, Cr, Co or Ni
  • Z is one of the elements C, P or Ge.
  • Patent Document 2 discloses a method for manufacturing a soft magnetic material that achieves both high saturation magnetization and low coercive force.
  • This soft magnetic material has a composition formula Fe 100-ab-c B a Cu b M' c , where M' is at least one element selected from Nb, Mo, Ta, W, Ni, and Co. It has a composition satisfying 10 ⁇ a ⁇ 16, 0 ⁇ b ⁇ 2, and 0 ⁇ c ⁇ 8. Then, this soft magnetic material is produced by heating an alloy having an amorphous phase at a heating rate of 10°C/second or more, and at a temperature of 0 to 80°C at a temperature higher than the crystallization start temperature and lower than the Fe-B compound formation start temperature. Produced by holding for seconds.
  • Patent Document 3 discloses a nanocrystalline alloy ribbon.
  • the nanocrystalline alloy ribbon is represented by the composition formula Fe 100-ab-c-d B a Si b Cu c M d , where a, b, c, and d are all atomic %, and each is 0. ⁇ a, 0 ⁇ b, 0 ⁇ c, 0 ⁇ d, and 78 ⁇ 100-a-b-c-d, and M is Ti, Zr, Hf, V, Nb, Ta, Cr, Mo , and represents at least one element selected from the group consisting of W.
  • the nanocrystalline alloy ribbon is produced by continuously running the amorphous alloy ribbon under a tension F applied to the amorphous alloy ribbon, and bringing a part of the amorphous alloy ribbon into contact with a heat transfer medium maintained at a temperature of 450°C or higher. Manufactured. At this time, the temperature of the amorphous alloy ribbon is raised to a final temperature of 450° C. or higher so that the average temperature increase rate in the temperature range from 350° C. to 450° C. is 10° C./sec or higher.
  • Patent Document 4 discloses a method for processing an amorphous alloy ribbon.
  • the amorphous alloy ribbon is fed forward along a running path at a set feed rate and guided so as not to slacken.
  • the amorphous alloy ribbon is then heated to a temperature for starting the heat treatment at a rate greater than 10 3 C/sec, and the amorphous alloy ribbon is cooled at a rate greater than 10 3 C/sec until the heat treatment is completed.
  • mechanical restraint is applied to the ribbon until the amorphous alloy ribbon assumes a specific shape in a resting state after the heat treatment, and after the heat treatment, the amorphous alloy ribbon is cooled at a rate that preserves the specific shape. do.
  • nanocrystalline alloy ribbons In order to continuously heat-treat nanocrystalline alloy ribbons, it is necessary to heat-treat the ribbons wound after casting at high temperatures continuously after unwinding, and at the same time as possible to increase productivity. It is also required that no breakage occurs. Further, in order for the nanocrystalline alloy ribbon to have excellent magnetic properties, it is necessary to have a fine nanocrystalline structure with an average grain size of 50 nm or less and low magnetostriction. In order to maintain low magnetostriction, it is necessary to add a certain amount of Si.
  • magnetic sheets for non-contact charging are required to have isotropic magnetic properties, to have as few wrinkles and streaks as possible that tend to occur during nanocrystallization during heat treatment, and to have a high space factor.
  • Patent Document 1 discloses a nanocrystalline alloy ribbon of 1.4T or more, but since it is heat-treated by applying tension, anisotropy may be imparted to it. Furthermore, the magnetic permeability is also 3000 or less, and the remanence Jr/Js (Br/Bs) is as low as 0.1 or less. Therefore, it is difficult to use the alloy of Patent Document 1 in products other than some products that require low magnetic permeability. In addition, since the alloy ribbon is not restrained during heat treatment, wrinkles and streaks are likely to occur in the ribbon when nanocrystals are formed, which may result in poor plate thickness deviation, space factor, etc. In addition, areas with wrinkles, streaks, etc. become extremely brittle and may break due to tension.
  • Patent Document 2 discloses a method of heating an amorphous alloy by sandwiching the amorphous alloy between heated blocks.
  • the series of heat treatment operations in which the amorphous ribbon is sandwiched between blocks, heated, and then the amorphous alloy is taken out, takes time. Since the amount that can be processed at one time is limited, this method is not suitable for heat treating a large amount of ribbon during mass production. Furthermore, since it is not possible to heat-treat the ribbon continuously, this method is not suitable as a method for heat-treating magnetic sheets.
  • the soft magnetic material described in Patent Document 2 does not contain Si, an SiO 2 film that contributes to the corrosion resistance of the soft magnetic material is not formed on the material surface. Therefore, it may be difficult to prevent rust and the like.
  • Patent Document 4 a method is disclosed in which a thin ribbon is brought into contact with a heated roller. Mass productivity is high because the ribbon can be heat-treated while being transported. However, since stable heat treatment is achieved by pressing the ribbon against a roller with a large tension of 25 MPa or more, anisotropy may be imparted during heat treatment as in Patent Document 1. Therefore, it is not suitable for applications requiring isotropy. In addition, since only one side of the ribbon is conveyed in contact with the heating roller, and the opposite side of the ribbon is not constrained, wrinkles and streaks may occur due to crystallization when it comes into contact with the heating roller. It is not possible to suppress the occurrence of the phenomenon or the possibility that the ribbon may partially lift. Additionally, there is a problem in that the tension causes breaks.
  • nanocrystalline alloy ribbons are produced by jetting molten alloy adjusted to a predetermined alloy composition onto a rotating cooling roller, rapidly solidifying it to produce an alloy ribbon, and then heat-treating the alloy ribbon. be done.
  • the nanocrystalline alloy ribbon has a thin thickness and a predetermined width, and is manufactured as a long ribbon. According to this manufacturing method, anisotropy is likely to be introduced in the casting direction (longitudinal direction), and even after heat treatment, the magnetic properties of the elongate shape are unchanged in the longitudinal direction and the width direction perpendicular to the longitudinal direction. There are different trends.
  • nanocrystalline alloy ribbons used for motor stators, magnetic sheets for non-contact charging coils, etc. are required to have as isotropic properties as possible.
  • nanocrystalline alloy ribbons that have excellent magnetic properties (high saturation magnetic flux density, low core loss) and isotropy are continuously heat-treated. It was difficult to obtain it in a method and in a highly productive manner.
  • the present disclosure provides a manufacturing method for obtaining a nanocrystalline alloy ribbon using a method of continuously heat-treating a ribbon, and a manufacturing method for a magnetic sheet using the manufacturing method.
  • the manufacturing method for obtaining a nanocrystalline alloy ribbon includes a manufacturing method that can obtain a nanocrystalline alloy ribbon with high saturation magnetic flux density, high magnetic permeability, and excellent magnetic properties, low magnetostriction, and low loss. It includes a manufacturing method that can obtain a nanocrystalline alloy ribbon with isotropy, or a manufacturing method of a nanocrystalline alloy ribbon that can suppress wrinkles, streaks, etc. and achieve a high space factor.
  • a method for producing a nanocrystalline alloy ribbon according to the first aspect of the present disclosure includes heating an amorphous alloy ribbon by bringing it into contact with a heating body, so that crystal grains having an average crystal grain size of 50 nm or less are formed in an amorphous phase.
  • a method for producing a nanocrystalline alloy ribbon having an existing structure The nanocrystalline alloy ribbon is represented by the composition formula a Si b B c Cu d Me , where A is at least one of Ni and Co, and M is selected from Nb, Mo, V, Zr, Hf, and W.
  • the amorphous alloy ribbon comes into contact with the heating body and is heated, the amorphous alloy ribbon is conveyed and the opposite side of the amorphous alloy ribbon contacts the heating body.
  • a ribbon pressing member contacts the surface, and the amorphous alloy ribbon is heated while being pressed against the heating body;
  • the heating body is heated to a heating temperature Ta of Tx1+80°C or more and Tx1+230°C or less.
  • a method for manufacturing a magnetic sheet according to a second aspect of the present disclosure includes a nanocrystalline alloy ribbon obtained by the method for manufacturing a nanocrystalline alloy ribbon according to the first aspect; preparing a support formed in a band shape and an adhesive layer having an adhesive provided on at least one of a first surface and a second surface of the support; The nanocrystalline alloy ribbon and the adhesive layer are successively guided to a pasting roller, and the nanocrystalline alloy ribbon and the adhesive layer are bonded together by the pasting roller.
  • a nanocrystalline alloy ribbon with high saturation magnetic flux density, high magnetic permeability, and excellent magnetic properties can be obtained using a method of continuously heat-treating the ribbon. Furthermore, a nanocrystalline alloy ribbon having low magnetostriction, low loss, and isotropy can be obtained. In addition, it is possible to obtain a nanocrystalline alloy ribbon that suppresses wrinkles, streaks, etc. and achieves a high space factor. Moreover, a soft magnetic sheet using them can be provided.
  • FIG. 1 is a conceptual diagram showing an embodiment of a heat treatment method of the present disclosure.
  • FIG. 3 is a conceptual diagram showing another embodiment of the heat treatment method of the present disclosure.
  • FIG. 3 is a conceptual diagram showing another embodiment of the heat treatment method of the present disclosure.
  • Sample No. of the present disclosure. 10 is a laser micrograph showing the evaluation of wrinkle height.
  • Sample No. of the present disclosure. It is a laser micrograph showing the evaluation of wrinkle height in No. 16.
  • Sample No. of the present disclosure. This is a laser micrograph showing the evaluation of wrinkle height in No. 17.
  • Sample No. of the present disclosure. It is a laser micrograph in which the wrinkle height of No. 18 was evaluated. It is an example of the temperature profile during the heat treatment of this indication.
  • FIG. 2 is a schematic diagram illustrating a method for manufacturing a magnetic sheet according to the present disclosure. It is a sectional view explaining the composition of the layered product supplied from the 1st unwinding roll.
  • FIG. 2 is a cross-sectional view illustrating the structure of a laminate that is supplied from a first unwinding roll and from which a resin sheet has been peeled off.
  • FIG. 2 is a cross-sectional view illustrating the structure of a nanocrystalline alloy ribbon supplied from a second unwinding roll.
  • FIG. 2 is a cross-sectional view illustrating a state in which a nanocrystalline alloy ribbon is adhered to an adhesive layer by a pasting roller.
  • FIG. 2 is a cross-sectional view illustrating a state in which a crack is formed in a nanocrystalline alloy ribbon by a crack roller.
  • FIG. 1 is a cross-sectional view illustrating a magnetic sheet of the present disclosure.
  • a numerical range indicated using "-" indicates a range that includes the numerical values written before and after "-" as the lower limit and upper limit, respectively.
  • the upper limit or lower limit described in a certain numerical range may be replaced with the upper limit or lower limit of another numerical range described step by step.
  • the upper limit or lower limit described in a certain numerical range may be replaced with the value shown in the Examples.
  • the nanocrystalline alloy ribbon of the present disclosure is represented by the compositional formula (Fe 1-x A x ) a Si b B c Cu d M e , where A is at least one of Ni and Co, and M is Nb, Mo , at least one element selected from V, Zr, Hf and W, and in atomic % 72.0 ⁇ a ⁇ 81.0, 9.0 ⁇ b ⁇ 17.0, 5.0 ⁇ c ⁇ 10 .0, 0.02 ⁇ d ⁇ 1.2, 0.1 ⁇ e ⁇ 3.5, and 0 ⁇ x ⁇ 0.1.
  • composition of the nanocrystalline alloy ribbon of the present disclosure will be explained in detail below.
  • the content of Fe (iron) is 72.0% or more and 81.0% or less in atomic %.
  • a high saturation magnetic flux density can be obtained by setting the Fe content to 72.0% or more. Preferably it is 73% or more, more preferably 75.0% or more, still more preferably 76% or more, and still more preferably 77% or more. In addition, when trying to obtain a saturation magnetic flux density of 1.36 T or more, it is preferable that the Fe content is 75.0% or more.
  • the Fe content is set to 81.0% or less.
  • the Fe content is set to 81.0% or less.
  • it is 80% or less, more preferably 78% or less.
  • a part of Fe may be replaced with at least one element of Ni and Co.
  • (Fe 1-x A x ) A is at least one of Ni and Co, and x is 0.1 or less.
  • a expressed as (Fe 1-x A x ) a , falls within the range of 72.0% ⁇ a ⁇ 81.0%.
  • the content a of (Fe 1-x A x ) is preferably 73% or more, more preferably 75.0% or more, even more preferably 76% or more, and still more preferably 77% or more. .
  • it is 80% or less, more preferably 78% or less.
  • the content of Si is 9.0% or more and 17.0% or less in atomic %.
  • Low magnetostriction can be achieved by setting the Si content to 9.0% or more.
  • the content of Si is preferably 10% or more, more preferably 13% or more, and still more preferably 15% or more. If it exceeds 17.0%, the ability to form an amorphous layer decreases, crystallization occurs during casting, and the soft magnetic properties are significantly deteriorated. Preferably it is 16.5% or less.
  • the content of B (boron) is 5.0% or more and 10.0% or less in atomic %.
  • the B content is set to 5.0% or more. Preferably it is 5.5% or more, more preferably 6.0% or more.
  • the content of B exceeds 10.0%, the amount of Fe and the amount of Si decrease, so the saturation magnetic flux density decreases and the magnetostriction increases. Therefore, the content of B is 10.0% or less. Preferably it is 8.5% or less, more preferably 7.5% or less, still more preferably 7.0% or less.
  • the content of Cu (copper) is 0.02% or more and 1.2% or less in atomic %.
  • the Cu content is set to 0.02% or more.
  • it is 0.05% or more, preferably 0.2% or more, preferably 0.3% or more, and more preferably 0.5% or more.
  • the Cu content When the Cu content exceeds 1.2%, it becomes easily brittle and the saturation magnetic flux density decreases. Therefore, the Cu content is set to 1.2% or less. Preferably it is 1.0% or less, more preferably 0.75% or less, and still more preferably 0.65% or less.
  • the M element is at least one selected from Nb, Mo, V, Zr, Hf, and W, and the content of the M element is 0.1% or more and 3.5% or less in atomic %.
  • the content of element M is preferably 0.3% or more, more preferably 0.4% or more.
  • the content of M element is set to 3.5% or less. Preferably it is 1.5% or less, more preferably 1.0% or less, even more preferably 0.9% or less, still more preferably 0.8% or less, and even more preferably 0.7%. It is as follows.
  • the nanocrystalline alloy ribbon of the present disclosure may contain C (carbon).
  • C has the effect of improving the flow of molten metal, and its inclusion in a small amount improves castability.
  • the content of C is preferably 1% by mass or less.
  • C may be included as an impurity in the raw material. Since the lower the amount of C, the higher the raw material price becomes, it is preferable to allow 0.01% by mass or more.
  • the content of C is preferably 0.1% by mass or more.
  • nanocrystalline alloy ribbon of the present disclosure may contain impurities in addition to the above-mentioned elements.
  • impurities examples include S (sulfur), O (oxygen), N (nitrogen), Cr, Mn, P, Ti, Al, and the like.
  • S content is preferably 200 mass ppm or less
  • O content is preferably 5000 mass ppm or less
  • N content is preferably 1000 mass ppm or less.
  • the content of P is preferably 2000 mass ppm or less.
  • the total content of these impurities is preferably 0.5% by mass or less.
  • an element corresponding to an impurity may be added as long as it is within the above range.
  • the nanocrystalline alloy ribbon of the present disclosure is obtained by ejecting a molten alloy having the above-described alloy composition onto a rotating cooling roller, and rapidly solidifying it on the cooling roller to obtain an alloy ribbon. Then, by heat-treating the alloy ribbon, the nanocrystalline alloy ribbon of the present disclosure can be obtained.
  • An alloy ribbon obtained by rapidly solidifying a molten alloy has an amorphous alloy structure, and is an amorphous alloy ribbon. By heat-treating this amorphous alloy ribbon, a nanocrystalline alloy ribbon is obtained.
  • the amorphous alloy ribbon obtained by rapidly solidifying the molten alloy may contain a crystalline phase consisting of fine crystals.
  • multiple element sources (pure iron, ferroboron, ferrosilicon, etc.) are mixed to obtain the desired alloy composition. Then, the plurality of materials are heated in an induction heating furnace to reach a temperature higher than their melting point, thereby melting and becoming a molten alloy.
  • the alloy ribbon can be obtained by jetting the molten alloy from a slit-shaped nozzle with a predetermined shape onto a rotating cooling roller, and rapidly solidifying the molten alloy on the cooling roller.
  • the cooling roller may have an outer diameter of 350 to 1000 mm, a width of 100 to 400 mm, and a peripheral speed of rotation of 20 to 35 m/sec.
  • This cooling roller is internally equipped with a cooling mechanism (water cooling, etc.) for suppressing a rise in temperature at the outer peripheral portion.
  • the outer peripheral portion of the cooling roller is preferably made of a Cu alloy having a thermal conductivity of 120 W/(m ⁇ K) or more.
  • the thermal conductivity of the outer peripheral portion is set to 120 W/(m ⁇ K) or more.
  • the thermal conductivity of the outer peripheral portion of the cooling roller is preferably 150 W/(m ⁇ K) or more, and more preferably 180 W/(m ⁇ K) or more.
  • the outer peripheral part of the cooling roller is the part that can come into contact with the molten alloy, and its thickness may be about 5 to 15 mm, and a structural material that maintains the roller structure may be used for the inner side.
  • a nanocrystalline alloy ribbon is obtained by heat-treating the amorphous alloy ribbon produced by the above rapid cooling method (method of obtaining an alloy ribbon by rapidly cooling a molten alloy).
  • the method for producing a nanocrystalline alloy ribbon according to the present disclosure is characterized by a heat treatment method.
  • the heat treatment method of the present disclosure is a method of heating an amorphous alloy ribbon by bringing it into contact with a heating body.
  • the amorphous alloy ribbon is brought into contact with a heating body and heated, the amorphous alloy ribbon is conveyed and the ribbon comes into contact with the opposite side of the surface of the amorphous alloy ribbon that comes into contact with the heating body.
  • the amorphous alloy ribbon is heated while being pressed against the heating body by the holding member.
  • the heating body when the heating rate of the amorphous alloy ribbon is 20 K/min and the measured bccFe crystallization start temperature is Tx1°C, the heating body has a heating temperature of Tx1+80°C or higher and Tx1+230°C or lower. It is heated to Ta. Preferably, the heating element is heated to Tx1+100°C or higher. When the amorphous alloy ribbon is heated, the temperature increase rate of the amorphous alloy ribbon is 15000°C/min. It is preferable that it is above.
  • the contact time (holding time) between the amorphous alloy ribbon and the heating body is preferably 0.1 seconds or more and 30 seconds or less.
  • properties such as magnetic permeability and B80 L /B80 W can be adjusted by applying a magnetic field or applying tension to the amorphous alloy ribbon.
  • a flexible member may be used as the ribbon pressing member, and the amorphous alloy ribbon may be pressed against the heating body.
  • the flexible member is preferably a metal member. Note that the flexible member is a member that can be deformed along the roller. Additionally, the ribbon pressing member may be a belt or a roller.
  • FIG. 1 is a conceptual diagram showing an embodiment of the heat treatment method of the present disclosure.
  • the configuration used in the heat treatment method shown in FIG. 1 includes a heating roller 2 serving as a heating element, a thin ribbon pressing metal belt 3 (thin ribbon pressing member), and rollers 4 and 5 that support the ribbon pressing metal belt 3. It is equipped with
  • the ribbon pressing metal belt 3 is an example of a structure in which the amorphous alloy ribbon (hereinafter also referred to as a ribbon) 1 is pressed against a heating roller 2 serving as a heating body.
  • the amorphous alloy ribbon 1 is passed between the heating roller 2 (heating body) and the ribbon pressing metal belt 3, and the ribbon 1 is pressed against the heating body (heating roller 2). Then, heat the ribbon 1.
  • the arrows in FIG. 1 indicate the movements of each part, and the heating roller 2, rollers 4 and 5 are cylindrical and have a rotating structure. As a result, the amorphous alloy ribbon 1 is heated while being conveyed and pressed against the heating roller 2.
  • the ribbon 1 after being heated by the heating roller 2 becomes a nanocrystalline alloy ribbon.
  • heating rollers that can also heat the rollers 4 and 5.
  • the temperature of the ribbon presser metal belt 3 (temperature when in contact with the ribbon 1) is equal to or slightly lower than the heating temperature of the ribbon 1.
  • the temperature of the rollers 4 and 5 may be set to an appropriate temperature for the ribbon pressing metal belt 3.
  • the temperatures of the ribbon pressing metal belt 3 and the rollers 4 and 5 can be selected to be suitable for heat treatment of the ribbon 1.
  • the thin strip presser metal belt 3 is an example of a flexible member, and the flexible member is preferably a metal member from the viewpoint of flexibility and strength.
  • the flexible member is preferably a metal member from the viewpoint of flexibility and strength.
  • a structure is created in which a flexible member (thin strip pressing metal belt 3) is pressed against the surface of the amorphous alloy thin strip 1 opposite to the surface that contacts the heating element.
  • the band 1 is pressed against the heating body (heating roller 2).
  • the amorphous alloy ribbon 1 is brought into close contact with the heating roller 2 by the ribbon pressing metal belt 3, and the amorphous alloy ribbon 1, the ribbon pressing metal belt 3, and the heating roller 2 move in unison. It is preferable to do so.
  • the heating roller 2 is a heating body (heating body of the present disclosure) that directly contacts and heats the amorphous alloy ribbon 1.
  • the amorphous alloy ribbon 1 abuts (contacts) a part of the outer circumferential surface (partial region in the circumferential direction) of the cylindrical heating roller 2 and is heated.
  • the heating roller 2 may have a driving force for conveying the amorphous alloy ribbon.
  • the roller for driving the thin strip presser metal belt 3 may be both the rollers 4 and 5, or either one of them may be used.
  • the roller 5 may have a driving force, and the roller 4 may be mechanically dependent. By doing so, complicated control such as electrically synchronized operation for the rollers 4 and 5 can be avoided, and furthermore, there is no need to correct synchronization deviations due to differences in thermal expansion between the rollers 4 and 5.
  • the heating roller 2 is an example of a heating body having a convex surface for heating the amorphous alloy ribbon 1 in contact with it.
  • the term "convex surface” means a surface that is raised toward the amorphous alloy ribbon 1 side.
  • the heating roller 2 may have a curved surface formed by a cylindrical side surface, as in the roller shown in FIG. The shape may be such that the amorphous alloy ribbon follows and ensures sufficient contact.
  • the heating body of the present disclosure may have a configuration in which it does not rotate, or a configuration in which the ribbon moves (slides) on the heating body.
  • FIG. 2 is a conceptual diagram showing another embodiment of the heat treatment method of the present disclosure.
  • the configuration used in the heat treatment method shown in FIG. 2 includes a heating roller 2 serving as a heating body, and ribbon pressing rollers 6, 7, and 8.
  • the ribbon pressing rollers 6 , 7 , and 8 function as ribbon pressing members that press the amorphous alloy ribbon 1 against the heating roller 2 .
  • the ribbon 1 is passed between the heating roller 2 (heating body) and ribbon pressing rollers 6, 7, and 8, and the ribbon 1 is pressed against the heating body (heating roller 2).
  • the thin ribbon 1 is heated while being in a heated state.
  • the arrows in FIG. 2 indicate the movements of each part, and the heating roller 2 and the ribbon pressing rollers 6, 7, and 8 are cylindrical and have a rotating structure.
  • the amorphous alloy ribbon 1 is heated while being conveyed and pressed against the heating roller 2.
  • FIG. 3 is a conceptual diagram showing another embodiment of the heat treatment method of the present disclosure.
  • a substantially D-shaped heating body 32 is provided in place of the heating roller 2 in FIG. 1, and the amorphous alloy ribbon 1 is pressed against the heating body 32.
  • it is provided with a thin ribbon presser metal belt 33 and rollers 34 and 35 that support the thin ribbon presser metal belt 33.
  • the ribbon 1 is passed between the heating body 32 and the ribbon pressing metal belt 33 (thin ribbon pressing member), and while the ribbon 1 is pressed against the heating body 32, , heat.
  • the arrows in FIG. 3 indicate the movements of each part, and the rollers 34 and 35 are cylindrical and have a rotating structure.
  • the amorphous alloy ribbon 1 is heated while being conveyed and being pressed against the heating body 32.
  • the amorphous alloy ribbon 1 slides on the heating body 32.
  • the temperature increase rate of the amorphous alloy ribbon 1 was set at 15000°C/min. It is preferable to set it as above. Further, the heating rate of the amorphous alloy ribbon 1 was set to 30000°C/min. It is more preferable to set it as above.
  • the appropriate heating rate to achieve a fine nanocrystalline structure varies depending on the composition.
  • the composition of the amorphous alloy ribbon 1 may be low Cu (lower Cu content), low M element (lower M element content), and high Fe (lower M element content) to obtain a high saturation magnetic flux density.
  • the lower limit of the temperature increase rate is 15000°C/min.
  • the upper limit can be determined depending on the equipment capacity of the heat treatment apparatus, the temperature of the heating body and ribbon pressing member, the contact state of the heating body and ribbon pressing member with the ribbon, etc.
  • the practical upper limit of the temperature increase rate is 240000°C/min. That's about it. Preferably 100000°C/min. It is.
  • the heating body has a width wider than the width of the amorphous alloy ribbon 1.
  • the ribbon pressing member also has a width wider than the width of the amorphous alloy ribbon 1.
  • the longitudinal direction the direction in which the amorphous alloy ribbon 1 is conveyed
  • the length in the longitudinal direction is simply called the length.
  • the width direction the direction perpendicular to the longitudinal direction
  • the width direction the length in the width direction
  • the distance from when the amorphous alloy ribbon 1 comes into contact with the heating body to when it leaves the heating body is the length of the surface of the heating body.
  • the length is preferably 50 mm or more.
  • the distance from when this amorphous alloy ribbon comes into contact with the heating element to when it leaves the heating element is 150 mm or more in terms of the length of the heating element surface.
  • the conveying speed of the amorphous alloy ribbon 1 is preferably 1 m/min or more.
  • the transport speed is more preferably 10 m/min or more.
  • the contact time between the amorphous alloy ribbon 1 and the heating body is preferably 0.1 seconds to 30 seconds.
  • the lower limit of the contact time is more preferably 0.2 seconds
  • the upper limit of the contact time is more preferably 10 seconds, even more preferably 5 seconds, and most preferably 2 seconds.
  • the contact time is preferably within the range of 0.2 seconds to 2 seconds.
  • the heat treatment method of the present disclosure by pressing the amorphous alloy ribbon 1 against the heating body, the heating body and the ribbon 1 are brought into good contact, and the heating body and the ribbon 1 are transferred from the heating body to the ribbon 1.
  • the heat transferability of the ribbon 1 is improved, and the temperature increase rate of the ribbon 1 becomes faster.
  • more heat generated by crystallization can be released to the heating element and the ribbon pressing member (belt or roller). Therefore, the maximum temperature of the ribbon 1 can be suppressed (temperature rise due to self-heating can be suppressed).
  • the ribbon 1 can be held in a pressed state by a ribbon pressing member (belt or roller), and therefore wrinkles or streaks that tend to occur during crystallization can be suppressed.
  • a radiation thermometer FLHX-TNE0090 manufactured by Japan Sensor Co., Ltd. was used to measure the surface temperature of the amorphous alloy ribbon. Since this radiation thermometer can only measure at a fixed point, the temperature measurement of the amorphous alloy ribbon 1 during heat treatment was carried out without the ribbon 1 being transported.
  • the ribbon 1 is placed between the ribbon presser metal belt 33 and the heating element 32 without driving the ribbon presser metal belt 33, and tension is applied to the ribbon presser metal belt 33.
  • the thin ribbon 1 is pressed against the heating body 32.
  • the heating body 32 was configured to move up and down, and the heating body 32 was lowered to heat the ribbon 1 without contacting it.
  • the heating body 32 reached a predetermined heat treatment temperature
  • the heating body 32 was raised, the ribbon 1 was pressed against the heating body 32 by the metal belt 33, and the temperature of the ribbon 1 was measured. Thereby, the temperature change after the ribbon 1 was pressed against the heating body was confirmed.
  • FIG. 8 shows an example temperature profile measured when the temperature of the heating body 32 is 620°C
  • FIG. 9 shows an example temperature profile measured when the temperature of the heating body 32 is 640°C.
  • the X-axis is time (seconds) and the Y-axis is the measured temperature of the ribbon 1. Measurements were made by pressing the ribbon 1 against the heating element 32 heated to a set temperature (620° C., 640° C.) using the method described above.
  • the contact time shown by the arrow parallel to the X axis in FIGS. 8 and 9 is the time during which the ribbon 1 was pressed against the heating body 32. According to this measurement method, the temperature of the ribbon 1 rises to about 450° C. before it comes into contact with the heating body 32.
  • the temperature increase rate is indicated by an arrow parallel to the Y axis in FIGS. 8 and 9.
  • the temperature increase rate was calculated as the value obtained by dividing the temperature change from the time when the ribbon 1 came into contact with the heating element 32 until the set temperature was reached by the time.
  • the temperature of the ribbon 1 was measured by making a hole in the ribbon holding metal belt 33. When the ribbon 1 is actually heat-treated, it is held down by the metal belt 33, so it can be assumed that the temperature increase rate is faster than that shown in FIGS. 8 and 9, but since it cannot be measured, the temperature increase rate under each condition has not been measured. However, from FIGS. 8 and 9, the temperature increase rate when the set temperature is 620°C is 1240°C/sec.
  • the pressure with which the amorphous alloy ribbon 1 is pressed against the heating body is preferably 0.03 MPa or more. More preferably it is 0.05 MPa or more, and still more preferably 0.07 MPa or more.
  • the radius of curvature of the heating body is preferably 25 mm or more.
  • heating rollers are used as the rollers 4, 5, 6, 7, 8, 34, and 35. It is also effective to set the temperature of the belt and rollers to be lower than the heating plate temperature Ta° C. in order to suppress heat generation during bccFe crystallization of the ribbon.
  • nanocrystalline alloy ribbon that has excellent magnetic properties and isotropy. Furthermore, it is possible to obtain a nanocrystalline alloy ribbon that suppresses wrinkles or streaks and achieves a high space factor.
  • the nanocrystalline alloy ribbon of the present disclosure has a saturation magnetic flux density Bs of 1.15T or more, preferably 1.20T or more, further preferably 1.35T or more, further preferably 1.36T or more, and It is preferably 1.37T or more, and more preferably 1.40T or more.
  • the ratio Br/B 8000 of the residual magnetic flux density Br to the magnetic flux density B 8000 at a magnetic field of 8000 A/m is preferably 0.20 or more. Moreover, it is preferable that the maximum magnetic permeability is 4000 or more. Moreover, it is preferable that the maximum magnetic permeability is 5000 or more.
  • the nanocrystalline alloy ribbon of the present disclosure has a magnetic flux density B80 L when a magnetic field of 80 A/m is applied in the longitudinal direction of the nanocrystalline alloy ribbon, and a magnetic flux density B80 L when a magnetic field of 80 A/m is applied in the width direction perpendicular to the longitudinal direction.
  • the ratio (B80 L /B80 W ) of the magnetic flux density B80 W is 0.60 to 1.40, and that both B80 L and B80 W are 0.4 T or more.
  • the ratio (B80 L /B80 W ) is more preferably 0.70 to 1.30.
  • both B80L and B80W are 0.5T or more.
  • the nanocrystalline alloy ribbon of the present disclosure preferably has a space factor of 68.0% or more.
  • the space factor is preferably 70% or more, more preferably 75% or more.
  • the space factor can be measured by the following method based on JIS C 2534:2017.
  • Stack 20 nanocrystalline alloy thin strips cut to a length of 120 mm and set them on a flat sample stand. Place a flat anvil with a diameter of 16 mm on the laminated thin strips at a pressure of 50 kPa and measure the height at 10 mm intervals in the width direction. do. The maximum height at that time is assumed to be hmax ( ⁇ m), and the space factor LF is determined from the following calculation formula.
  • LF (%) Weight of sample (g) / Density (g/cm 3 ) / hmax ( ⁇ m) / Sample length (240 cm) / Width of ribbon (cm) x 10000 At this time, the density (g/cm 3 ) is the density of the alloy ribbon after heat treatment. This density may be 7.4 g/cm 3 .
  • the amorphous alloy ribbon 1 When the amorphous alloy ribbon 1 is brought into contact with a heating body and heated to turn the amorphous alloy ribbon 1 into a nanocrystalline alloy ribbon, variations in the contact between the amorphous alloy ribbon 1 and the heating body, etc. Therefore, if a local difference occurs in the heating rate or temperature of the amorphous alloy ribbon 1, a difference also occurs in the way crystallization progresses. This causes local distortion, causing a problem in which a portion of the ribbon 1 lifts off from the heating element. In the raised portions, it becomes difficult for self-heating due to crystallization to escape to the heating element, and the temperature of the ribbon 1 rises rapidly, reaching the FeB precipitation temperature, which tends to cause wrinkles or streaks. This reduces the space factor. In addition, since the wrinkles or streaks become extremely brittle, the nanocrystalline alloy ribbon may crack during transportation, stacking, etc., causing problems in handling and deterioration of magnetic properties.
  • the amorphous alloy ribbon 1 is pressed against the heating body by the ribbon pressing member that contacts the surface opposite to the surface of the amorphous alloy ribbon 1 that contacts the heating body. . Therefore, the amorphous alloy ribbon 1 can be heated uniformly, and lifting of the alloy ribbon can be suppressed, and the occurrence of wrinkles or streaks can be suppressed. Furthermore, the present disclosure has the effect of correcting wrinkles and the like caused by variations in cooling that occur during casting of the amorphous alloy ribbon 1. According to the present disclosure, wrinkles or streaks are suppressed, and a nanocrystalline alloy ribbon with good flatness can be obtained.
  • the nanocrystalline alloy ribbon of the present disclosure preferably has a wrinkle height of 0.15 mm or less. More preferably, it is 0.10 mm or less, and still more preferably 0.08 mm or less.
  • Wrinkle height refers to the height of wrinkles or streaks, and can be evaluated by the method described in the Examples below.
  • the nanocrystalline alloy ribbon of the present disclosure preferably has a thickness of 25 ⁇ m or less, more preferably 20 ⁇ m or less. Further, the thickness is preferably 5 ⁇ m or more, and more preferably 10 ⁇ m or more. The width is preferably 5 mm or more, more preferably 20 mm or more, and even more preferably 30 mm or more.
  • the width of the nanocrystalline alloy ribbon of the present disclosure becomes too wide, stable production becomes difficult, so the width is preferably 500 mm or less. Moreover, it is more preferably 400 mm or less.
  • nanocrystalline alloy ribbon of the present disclosure for magnetic cores and magnetic shielding materials used in electronic components, motors, etc., magnetic cores and magnetic shielding materials with excellent properties can be obtained.
  • the nanocrystalline alloy ribbon of the present disclosure can constitute a magnetic sheet that can be used as a magnetic sheet for non-contact charging, for example.
  • Example 1 In Example 1, the element sources were blended so that the alloy composition was Fe 76.4 Si 16 B 6.5 Cu 0.6 Nb 0.5 , and the alloy was heated to 1350°C to prepare a molten alloy.
  • the molten metal was jetted onto a cooling roller having an outer diameter of 400 mm and a width of 200 mm rotating at a circumferential speed of 30 m/sec, and was rapidly solidified on the cooling roller to produce an amorphous alloy ribbon.
  • the outer circumferential portion of the cooling roller is made of a Cu alloy with a thermal conductivity of 150 W/(m ⁇ K), and is provided with a cooling mechanism for controlling the temperature of the outer circumferential portion.
  • This amorphous alloy ribbon was heated at a heating rate of 6°C/min. , a sample heat-treated at a heat treatment temperature of 470°C and a holding time of 1 hour (Comparative Example 1), and a sample heat-treated at a heating rate of 79200°C/min. , and a sample (Example 1) which was heat-treated under conditions of a heat treatment temperature of 660° C. and a holding time of 1.2 seconds was prepared.
  • the heat treatment in Example 1 used the heat treatment method shown in FIG.
  • the samples of Example 1 and Comparative Example 1 after heat treatment are nanocrystalline alloy ribbons.
  • the heat treatment temperature in Example 1 is the heating temperature of the heating body.
  • Tx1 of this alloy composition (same as No. 10 in Table 2) was 468.5°C.
  • the heating temperature Ta of the heating element in Example 1 was Tx1+191.5°C.
  • the width of the nanocrystalline alloy ribbons of Example 1 and Comparative Example 1 was 50 mm, and the thickness was 16.4 ⁇ m.
  • Table 1 shows the average grain size, iron loss at 20 kHz, 0.2 T, Br/B 8000 , and maximum magnetic permeability for Example 1 and Comparative Example 1.
  • B 8000 (Bs) in Example 1 and Comparative Example 1 was equivalent to 1.41T.
  • the temperature increase rate was 15000°C/min.
  • the average crystal grain size could be made 50 nm or less.
  • the iron loss at 20kHz and 0.2T is also excellent at 10W/kg or less.
  • Br/B 8000 was 0.20 or more
  • the maximum magnetic permeability was 4000 or more.
  • Example 1 a nanocrystalline alloy ribbon with high saturation magnetic flux density, low loss, and high magnetic permeability could be realized. Note that the measurement method will be explained in Example 2.
  • Example 2 In Example 2, element sources were blended to have the respective compositions shown in Table 2, heated to 1350°C to produce a molten alloy, and the molten alloy was rotated at a circumferential speed of 30 m/sec with an outer diameter of 400 mm and a width. The mixture was jetted onto a 200 mm cooling roller and rapidly solidified on the cooling roller to produce an amorphous alloy ribbon. Table 3 shows the width and thickness of the amorphous alloy ribbon.
  • the outer circumferential portion of the cooling roller is made of a Cu alloy with a thermal conductivity of 150 W/(m ⁇ K), and is provided with a cooling mechanism for controlling the temperature of the outer circumferential portion.
  • the average crystal grain size was determined from the Scherrer equation using the integral width of the diffraction peak from the (110) plane in the X-ray diffraction pattern obtained from the X-ray diffraction experiment.
  • the integral width of the diffraction peak from the (110) plane is obtained by performing peak decomposition using the pseudo-Voigt function for the diffraction pattern, where D is the average particle diameter, ⁇ is the integral width, ⁇ is the diffraction angle, and K is the Scherrer constant.
  • the integral width is a value corrected so that the integral width is narrowed by the width of the diffraction line width due to the device.
  • the volume fraction is the volume fraction of nanocrystals, and portions other than nanocrystals are amorphous portions.
  • This volume fraction is determined by the ratio of the integrated intensity of the diffraction peak from the (110) plane of Fe to the integrated intensity of the halo pattern.
  • the integrated intensity of the peak exhibited by nanocrystals and the halo pattern exhibited by amorphous is determined by performing peak decomposition using a pseudo-Voigt function for the X-ray diffraction pattern.
  • Ic and Ia also include the integrated intensity of Fe 2 B, which is precipitated in a small amount. Can be included.
  • the saturation magnetic flux density Bs is obtained by applying a magnetic field of 8000 A/m to the heat-treated nanocrystalline alloy ribbon (single plate sample) using a DC magnetization characteristic testing device manufactured by Metron Giken Co., Ltd., and measuring the maximum magnetic flux density at that time. . Since the nanocrystalline alloy ribbon of the present disclosure has a characteristic that saturates relatively easily, it saturates when a magnetic field of 8000 A/m is applied. Since B 8000 and the saturation magnetic flux density Bs have almost the same value, the saturation magnetic flux density Bs is expressed as B 8000 .
  • the maximum magnetic permeability is determined by applying a magnetic field of 800 A/m to the heat-treated nanocrystalline alloy ribbon (single plate sample) using a DC magnetization characteristic testing device manufactured by Metron Giken Co., Ltd., and measuring the magnetic permeability against the magnetic field H at that time. The magnetic permeability that indicates the maximum when
  • Magnetic flux density B80 A magnetic field of 80 A/m was applied in the longitudinal direction (casting direction) of the nanocrystalline alloy ribbon and in the width direction perpendicular to the longitudinal direction using a DC magnetization characteristic testing device manufactured by Metron Giken Co., Ltd., and the maximum magnetic flux density at that time was B80 L. , B80W . Then, the ratio B80 L /B80 W was calculated and the isotropy was evaluated.
  • Wrinkle height refers to the height of streaks or wrinkles formed on the surface of the ribbon.
  • the height of the ribbon surface was measured using a laser microscope VR3200 manufactured by Keyence Corporation, and the difference between the maximum and minimum values was calculated as the wrinkle height.
  • the reason for sandwiching the nanocrystalline alloy ribbon between glass plates is that the ribbon is extremely thin and if only the ribbon is placed on the measurement stage, the ribbon will partially lift due to undulations, which will affect the height measurement. The purpose is to minimize the impact of
  • Magnetic flux density Br A magnetic field of 8000 A/m was applied to the heat-treated nanocrystalline alloy ribbon (single plate sample) using a DC magnetization characteristic testing device manufactured by Metron Giken Co., Ltd., and the value of magnetic flux density B when the magnetic field was 0 was defined as Br.
  • a ring core with an inner diameter of 8.8 mm and an outer diameter of 19.9 mm was punched out from a 15-layer nanocrystalline alloy ribbon using a BH Analyzer SY8218 manufactured by Iwasaki Tsushinki Co., Ltd., and placed in a case to measure iron loss.
  • 15 turns of primary and secondary windings, a frequency of 20 kHz, and a magnetic flux density of 0.2 T were adopted.
  • Example 3 Table 5 shows the evaluation results of the nanocrystalline alloy ribbon produced in Example 3.
  • Example 3 No. 2 of Example 2 was used.
  • nanocrystalline alloy ribbons were created by changing the pressure to press the ribbon to 0.019, 0.038, 0.058, and 0.086 MPa.
  • Example 3 a space factor of 68.0% or more was obtained by pressing the ribbon at a pressure of 0.03 MPa or more.
  • No. Laser micrographs of samples Nos. 10, 16, 17, and 18 in which the wrinkle heights were evaluated are shown in FIGS. 4, 5, 6, and 7, respectively.
  • a nanocrystalline alloy ribbon having a saturation magnetic flux density of 1.15 T or more and a maximum magnetic permeability of 4000 or more was obtained. Further, a nanocrystalline alloy ribbon was obtained in which the ratio Br/B 8000 of the residual magnetic flux density Br to the magnetic flux density B 8000 at a magnetic field of 8000 A/m was 0.20 or more.
  • the ratio of the magnetic flux density B80L when a magnetic field of 80 A/m is applied in the longitudinal direction of the nanocrystalline alloy ribbon to the magnetic flux density B80W when a magnetic field of 80 A/m is applied in the width direction perpendicular to the longitudinal direction (B80L /B80W) was 0.60 to 1.40, and a nanocrystalline alloy ribbon exhibiting isotropic properties was obtained.
  • a nanocrystalline alloy ribbon with a wrinkle height of 0.15 mm or less was obtained. Further, by setting the pressure for pressing the ribbon to 0.03 MPa or more, a nanocrystalline alloy ribbon with a wrinkle height of 0.10 mm or less and a space factor of 68.0% or more was obtained.
  • nanocrystalline alloy ribbon with high saturation magnetic flux density, high magnetic permeability, and excellent magnetic properties. Furthermore, it was possible to obtain a nanocrystalline alloy ribbon with low magnetostriction, low loss, and isotropy. In addition, we were able to obtain a nanocrystalline alloy ribbon with suppressed wrinkles and streaks and a high space factor.
  • Example 4 In Example 4, a 3 ⁇ m thick adhesive layer was attached to one surface of the nanocrystalline alloy ribbons of Examples 1 and 2 to produce a magnetic sheet.
  • FIG. 14 is a cross-sectional view cut in the width direction to explain the structure of the magnetic sheet.
  • the magnetic sheet has a structure in which one layer of adhesive layer 10, one layer of resin sheet 15 (15B), and one layer of nanocrystalline alloy ribbon 20 are laminated.
  • the adhesive layer 10 is mainly provided with a support 11 and a plurality of adhesives 12.
  • the support 11 is a long strip-shaped membrane member, for example, a rectangular membrane member.
  • the support body 11 is formed using a flexible resin material.
  • the resin material polyethylene terephthalate (PET) can be used.
  • PET polyethylene terephthalate
  • a pressure-sensitive adhesive can be used as the adhesive 12.
  • known adhesives such as acrylic adhesives, silicone adhesives, urethane adhesives, synthetic rubber, and natural rubber can be used as the adhesive 12.
  • Acrylic adhesives are preferable as the adhesive 12 because they have excellent heat resistance and moisture resistance, and can be bonded to a wide range of materials.
  • the adhesive 12 is provided in the form of a film or layer on the first surface 11A and the second surface 11B of the support 11.
  • the total thickness of each of the adhesive 12 on the first surface 11A side, the support 11, and the adhesive 12 on the second surface 11B side was 3 ⁇ m.
  • the magnetic sheet can be attached to another member using the adhesive 12 on the second surface 11B side.
  • a plurality of the above-mentioned magnetic sheets were prepared to produce a magnetic sheet in which a plurality of nanocrystalline alloy ribbons were laminated.
  • a plurality of magnetic sheets were used so that nanocrystalline alloy ribbons were laminated with an adhesive layer interposed therebetween.
  • the resin sheet 15 (15B) is peeled off from the side of the adhesive layer 10 of the first magnetic sheet to which the nanocrystalline alloy ribbon 20 is not attached.
  • another magnetic sheet nanocrystalline alloy ribbon 20 is attached to the exposed portion of the adhesive layer 10 where the adhesive 12 is exposed.
  • a magnetic sheet with 15 layers of nanocrystalline alloy ribbons was used, and the magnetic sheet was punched out into a ring shape with an inner diameter of 8.8 mm and an outer diameter of 19.9 mm.
  • the core loss at 128 kHz and 0.2 T and the real part of complex magnetic permeability at 128 kHz and 0.03 V were evaluated. The results are shown in Table 6.
  • a magnetic sheet with an iron loss of 2000 kW/m 3 or less at 128 kHz and 0.2 T and a real part of complex magnetic permeability of 1500 or more was obtained.
  • a magnetic sheet with excellent magnetic properties could be constructed.
  • Example 5 In Example 5, a 3 ⁇ m thick adhesive layer 10 was attached to one side of the nanocrystalline alloy ribbon of Example 1, and then cracks 21 were formed in the nanocrystalline alloy ribbon to produce a magnetic sheet.
  • FIG. 15 is a cross-sectional view cut in the width direction to explain the structure of this magnetic sheet 100.
  • the magnetic sheet 100 has a structure in which one layer of adhesive layer 10, one layer of resin sheet 15 (15B), and one layer of nanocrystalline alloy ribbon 20 are laminated.
  • a crack 21 is formed in the nanocrystalline alloy ribbon 20, and the nanocrystalline alloy ribbon 20 is divided into small pieces 22 by the crack 21.
  • a plurality of the above-mentioned magnetic sheets were prepared to produce a magnetic sheet in which a plurality of nanocrystalline alloy ribbons were laminated.
  • a plurality of magnetic sheets were used to stack nanocrystalline alloy ribbons 20 with adhesive layers 10 in between.
  • the resin sheet 15 (15B) is peeled off from the side of the adhesive layer 10 of the first magnetic sheet 100 on which the nanocrystalline alloy ribbon 20 is not attached.
  • the nanocrystalline alloy ribbon 20 of another magnetic sheet 100 is attached to the exposed portion of the adhesive layer 10 where the adhesive 12 is exposed.
  • a magnetic sheet with 15 layers of nanocrystalline alloy ribbons was used, and the magnetic sheet was punched out into a ring shape with an inner diameter of 8.8 mm and an outer diameter of 19.9 mm.
  • the core loss at 128 kHz and 0.2 T and the real part of complex magnetic permeability at 128 kHz and 0.03 V were evaluated. The results are shown in Table 7.
  • Example 2 No. 2 of Example 2 was prepared. A 15-layer magnetic sheet was also produced for No. 4, and the core loss at 128 kHz and 0.2 T and the real part of complex magnetic permeability at 128 kHz and 0.03 V were evaluated. The results are shown in Table 7.
  • a magnetic sheet with an iron loss of 2000 kW/m 3 or less at 128 kHz and 0.2 T and a real part of complex magnetic permeability of 400 to 3000 was obtained.
  • FIG. 10 is a schematic diagram illustrating a method for manufacturing a magnetic sheet 100 having one layer of nanocrystalline alloy ribbons according to the present disclosure.
  • FIG. 10 shows a method of continuously attaching the adhesive layer 10 to the nanocrystalline alloy ribbon 20.
  • the magnetic sheet 100 is manufactured using a manufacturing apparatus 500 shown in FIG.
  • the manufacturing apparatus 500 includes, from upstream to downstream in the manufacturing process, a first unwinding roll 510, a first winding roll 520, a second unwinding roll 530, a plurality of pasting rollers 540, and a crack part 550. , a plurality of flattening rollers 560, and a third take-up roll 570 are mainly provided.
  • the manufacturing apparatus 500 may further be provided with a plurality of guide rollers 580. Note that the guide roller 580 can be placed at a position not shown if necessary.
  • FIG. 11 is a cross-sectional view illustrating the structure of the laminate supplied from the first unwinding roll 510.
  • a laminate in which resin sheets 15A and 15B are laminated on the first surface 11A and second surface 11B of the adhesive layer 10 is wound around the first unwinding roll 510.
  • the resin sheet 15A arranged on the first surface 11A is a protective sheet.
  • the resin sheet 15B disposed on the second surface 11B is also referred to as a liner.
  • the resin sheet 15A is thinner than the resin sheet 15B.
  • FIG. 12 is a cross-sectional view illustrating the structure of the laminate supplied from the first unwinding roll 510 and from which the resin sheet 15A has been peeled off.
  • the resin sheet 15A is peeled off from the laminate unwound from the first unwinding roll 510.
  • the peeled resin sheet 15A is wound onto a first winding roll 520, as shown in FIG.
  • FIG. 13 is a cross-sectional view illustrating the structure of the nanocrystalline alloy ribbon 20 supplied from the second unwinding roll 530.
  • the laminate from which the resin sheet 15A has been peeled is guided to the pasting roller 540 by a plurality of guide rollers 580.
  • the nanocrystalline alloy ribbon 20 unwound from the second unwinding roll 530 is further guided to the pasting roller 540 . As shown in FIG. 13, no cracks 21 are formed in the nanocrystalline alloy ribbon 20 guided by the pasting roller 540.
  • FIG. 14 is a cross-sectional view illustrating the state in which the nanocrystalline alloy ribbon 20 is adhered to the adhesive layer 10 by the pasting roller 540.
  • the pasting roller 540 includes two cylindrical rollers arranged to face each other.
  • the two rollers each have a smooth circumferential surface without protrusions.
  • the two rollers press and adhere the nanocrystalline alloy ribbon 20 to the laminate from which the resin sheet 15A has been peeled off.
  • the laminate and the nanocrystalline alloy ribbon 20 are guided between two rollers arranged to face each other, and the two rollers are used to roll the adhesive layer 10 as shown in FIG.
  • the nanocrystalline alloy ribbon 20 is pressed and adhered to the first surface 11A.
  • the laminate to which the nanocrystalline alloy ribbon 20 is adhered is guided from the pasting roller 540 to the crack portion 550, as shown in FIG.
  • the film may be wound onto the third winding roll 570 without being guided to the crack portion 550, or may be cut to a desired length.
  • FIG. 15 is a cross-sectional view illustrating a state in which a crack 21 is formed in the nanocrystalline alloy ribbon 20 due to a crack portion 550.
  • the crack portion 550 forms a crack 21 in the nanocrystalline alloy ribbon 20 adhered to the adhesive layer 10.
  • the crack section 550 includes two rollers arranged to face each other. That is, the crack portion 550 includes a crack roller 550A and a support roller 550B.
  • the manufacturing apparatus 500 guides the laminate to which the nanocrystalline alloy ribbon 20 is adhered between these two rollers.
  • the crack roller 550A is a cylindrical roller with protrusions on its circumferential surface.
  • the support roller 550B is a cylindrical roller with no protrusions on its circumferential surface.
  • the manufacturing apparatus 500 presses the protruding portion of the crack roller 550A against the nanocrystalline alloy ribbon 20 to form a crack 21 as shown in FIG.
  • the support roller 550B is arranged on the side of the laminate from which the resin sheet 15 has been peeled off.
  • a plurality of small pieces 22 are included in the nanocrystalline alloy ribbon 20 in which cracks 21 are formed. The plurality of small pieces 22 are adhered to the adhesive layer 10.
  • a plurality of convex members are arranged on the circumferential surface of the crack roller 550A as the above-mentioned protrusions.
  • the shape of the tip of the end of the convex member of the crack roller 550A may be flat, conical, inverted conical with a concave center, or cylindrical.
  • the plurality of convex members may be arranged regularly or irregularly.
  • the laminate guided from the crack portion 550 to the flattening roller 560 is flattened by the flattening roller 560.
  • the flattening roller 560 is also referred to as a shaping roller.
  • the laminate is guided between two opposing rollers of the flattening roller 560, and the laminate is sandwiched between the two rollers and pressed. As a result, the surface of the nanocrystalline alloy ribbon 20 on which the cracks 21 have been formed is flattened.
  • the laminate after the planarization process becomes the magnetic sheet 100.
  • the magnetic sheet 100 is guided to the third take-up roll 570 via the guide roller 580.
  • the magnetic sheet 100 is wound onto a third take-up roll 570.
  • the magnetic sheet 100 wound around the third winding roll 570 into a ring or spiral shape is the rolled magnetic sheet 200 .
  • the magnetic sheet 100 may be wound up, or may be cut into a predetermined length without being wound up.
  • the width B of the nanocrystalline alloy ribbon 20 and the width A of the adhesive layer 10 have a shape that satisfies the following relationship (see FIG. 16).
  • the width A is a dimension related to the adhesive layer 10, and more preferably a dimension related to a region of the adhesive layer 10 provided with the adhesive 12 to which the nanocrystalline alloy ribbon 20 is adhered.
  • Width B is a dimension with respect to nanocrystalline alloy ribbon 20. Note that when the adhesive 12 is provided on the entire surface of the support 11 of the adhesive layer 10, the width A is a dimension related to the adhesive layer 10 or the support 11.
  • the lower limit of (width A - width B) is preferably 0.5 mm, more preferably 1.0 mm.
  • the upper limit of (width A-width B) is preferably 2.5 mm, more preferably 2.0 mm.
  • the nanocrystalline alloy ribbon 20 may be arranged so that its center coincides with the adhesive layer 10 in the width direction, or it may be arranged at a distance from its center. In this case, they are arranged so as to satisfy the relationships of 0 mm ⁇ gap a and 0 mm ⁇ gap b (see FIG. 16).
  • Gap a and gap b are the distances from the end of the adhesive layer 10 to the end of the nanocrystalline alloy ribbon 20. Specifically, the gap a is the distance from the first adhesive layer end 10X of the adhesive layer 10 to the first ribbon end 20X of the nanocrystalline alloy ribbon 20. The gap b is the distance from the second adhesive layer end 10Y of the adhesive layer 10 to the second ribbon end 20Y of the nanocrystalline alloy ribbon 20.
  • the first ribbon end 20X is the end of the nanocrystalline alloy ribbon 20 on the same side as the first adhesive layer end 10X.
  • the second adhesive layer end 10Y is the end of the adhesive layer 10 opposite to the first adhesive layer end 10X.
  • the second ribbon end 20Y is the end of the nanocrystalline alloy ribbon 20 on the same side as the second adhesive layer end 10Y.
  • the width A, the width B, the gap a, and the gap b are dimensions in a direction intersecting with the longitudinal direction of the magnetic sheet 100, and more preferably in a direction perpendicular to the longitudinal direction of the magnetic sheet 100.
  • the longitudinal direction of the magnetic sheet 100 and the longitudinal direction of the adhesive layer 10 are the same direction. Further, the longitudinal direction of the magnetic sheet 100 and the longitudinal direction of the nanocrystalline alloy ribbon 20 are the same direction.
  • the width A of the region in the adhesive layer 10 where the adhesive 12 is provided is set wider than the width B of the nanocrystalline alloy ribbon 20. According to such a configuration, even if meandering occurs in the adhesive layer 10 or the nanocrystalline alloy ribbon 20 when attaching the nanocrystalline alloy ribbon 20 to the adhesive layer 10, the entire surface of the nanocrystalline alloy ribbon 20 is covered.
  • the adhesive 12 of the adhesive layer 10 can be easily placed.
  • by disposing the adhesive layer 10 on the entire surface of the nanocrystalline alloy ribbon 20 it is possible to suppress the small pieces 22 from falling off after cracks 21 are formed in the nanocrystalline alloy ribbon 20 and small pieces 22 are formed. can do.
  • the value obtained by subtracting the width B from the width A of the magnetic sheet 100 is set to 0.2 mm or more. According to such a configuration, when attaching the nanocrystalline alloy ribbon 20 to the adhesive layer 10, it is easy to suppress the occurrence of a portion of the nanocrystalline alloy ribbon 20 where the adhesive 12 is not placed.
  • the value obtained by subtracting the width B from the width A of the magnetic sheet 100 is set to 3 mm or less. According to such a configuration, it is easy to suppress the portion of the magnetic sheet 100 where the nanocrystalline alloy ribbon 20 is not arranged from increasing. Furthermore, when the magnetic sheets 100 are arranged in parallel, it is easy to suppress the distance between the nanocrystalline alloy ribbons (magnetic gap) from increasing.
  • the magnetic sheet 100 is set to satisfy the relationships 0mm ⁇ gap a and 0mm ⁇ gap b. According to such a configuration, when attaching the nanocrystalline alloy ribbon 20 to the adhesive layer 10, it is easy to prevent the nanocrystalline alloy ribbon 20 from protruding from the region where the adhesive 12 is provided. Therefore, it is easy to suppress the occurrence of a portion of the nanocrystalline alloy ribbon 20 where the adhesive 12 is not placed.
  • a nanocrystalline alloy ribbon with high saturation magnetic flux density and high magnetic permeability was obtained. Further, according to the present disclosure, a nanocrystalline alloy ribbon with low magnetostriction, low loss, and isotropy was obtained. Further, according to the present disclosure, a nanocrystalline alloy ribbon was obtained in which wrinkles, streaks, etc. were suppressed and a high space factor was achieved.

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PCT/JP2023/013352 2022-03-30 2023-03-30 ナノ結晶合金薄帯の製造方法、及び磁性シートの製造方法 Ceased WO2023190963A1 (ja)

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EP23780971.0A EP4491749A4 (en) 2022-03-30 2023-03-30 METHOD FOR MANUFACTURING A NANOCRYSTALLINE ALLOY RIBBON AND METHOD FOR MANUFACTURING A MAGNETIC SHEET
CN202380031853.9A CN118974288A (zh) 2022-03-30 2023-03-30 纳米晶合金薄带的制造方法及磁性片的制造方法

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