WO2022264999A1 - ナノ結晶合金薄帯の製造方法、およびナノ結晶合金薄帯 - Google Patents

ナノ結晶合金薄帯の製造方法、およびナノ結晶合金薄帯 Download PDF

Info

Publication number
WO2022264999A1
WO2022264999A1 PCT/JP2022/023736 JP2022023736W WO2022264999A1 WO 2022264999 A1 WO2022264999 A1 WO 2022264999A1 JP 2022023736 W JP2022023736 W JP 2022023736W WO 2022264999 A1 WO2022264999 A1 WO 2022264999A1
Authority
WO
WIPO (PCT)
Prior art keywords
alloy ribbon
ribbon
amorphous alloy
nanocrystalline
nanocrystalline alloy
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP2022/023736
Other languages
English (en)
French (fr)
Japanese (ja)
Inventor
小川雄一
豊永詞
福山建史
佐野博久
和田純
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Proterial Ltd
Original Assignee
Hitachi Metals Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Hitachi Metals Ltd filed Critical Hitachi Metals Ltd
Priority to JP2022559370A priority Critical patent/JPWO2022264999A1/ja
Publication of WO2022264999A1 publication Critical patent/WO2022264999A1/ja
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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
    • C21D6/00—Heat treatment of ferrous alloys
    • 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
    • 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
    • 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
    • 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
    • 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

Definitions

  • the present disclosure relates to a method for producing a nanocrystalline alloy ribbon having a nanocrystalline structure, and a nanocrystalline alloy ribbon.
  • Nanocrystalline alloy ribbons with a nanocrystalline structure have excellent magnetic properties and are used in transformers, electronic parts, motors, etc. These transformers, electronic components, motors, etc. are required to be smaller and more efficient. Therefore, there is a demand for further improvement in the properties of nanocrystalline alloys used in magnetic cores for these parts (transformers, electronic parts, motors, etc.). Characteristics required for the nanocrystalline alloy include high saturation magnetic flux density and low core loss. Among these parts, along with the high frequency of semiconductors, efforts are being made to increase the operating frequency to reduce the size of these parts, and Fe-based amorphous alloys and Fe-based nanocrystalline alloys with low core loss are attracting attention. Therefore, soft magnetic alloys with excellent price, productivity, and heat treatability are required for their commercial spread.
  • the Fe-based nanocrystalline alloy ribbon can achieve both high saturation magnetic flux density, low coercive force, and iron loss by heat treatment at a very high temperature rise rate.
  • a heat treatment method for achieving a high rate of temperature rise a method of bringing the ribbon into contact with a heated plate, a method of sandwiching the ribbon between heated plates, and the like are known.
  • the composition formula is Fe100 - abcBaCubM'c
  • M' is at least one element selected from Nb , Mo, Ta, W, Ni, and Co.
  • An alloy having a composition satisfying 10 ⁇ a ⁇ 16, 0 ⁇ b ⁇ 2, and 0 ⁇ c ⁇ 8 and having an amorphous phase is heated at a heating rate of 10 ° C./sec or more, and It describes a method for producing a soft magnetic material that achieves both high saturation magnetization and low coercive force by holding for 0 to 80 seconds above the crystallization start temperature and below the formation start temperature of the Fe—B compound.
  • Patent Document 2 it is represented by the composition formula Fe 100-abc-d B a Si b Cu c M d , where a, b, c, and d are all atomic %, and 0 ⁇ satisfying a, 0 ⁇ b, 0 ⁇ c, 0 ⁇ d, and 78 ⁇ 100-abcd, and M is Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, A nanocrystalline alloy ribbon representing at least one element selected from the group consisting of and W, which is continuously run under tension F, and part of the amorphous alloy ribbon continuously running under tension F By bringing the region into contact with a heat transfer medium maintained at a temperature of 450 ° C.
  • the temperature of the amorphous alloy ribbon is increased so that the average temperature increase rate in the temperature region from 350 ° C. to 450 ° C. is 10 ° C./sec or more. It is described that the temperature is raised to a temperature of 450° C. or higher at a temperature rate.
  • Patent Literature 1 a method of sandwiching a strip between heated plates is disclosed. According to this method, isotropic and good characteristics can be obtained, and the occurrence of wrinkles and streaks can be suppressed. However, it takes a long time to perform a series of heat treatment operations such as inserting the strip, sandwiching it between the heating bodies, and taking it out. In addition, since the amount to be processed at one time is limited, it is not suitable as a method for heat-treating a large amount of ribbon during mass production. In addition, since the soft magnetic material described in Patent Document 1 does not contain Si, a SiO 2 film that contributes to the corrosion resistance of the soft magnetic material is not formed on the surface of the material. Therefore, it becomes difficult to prevent rust and the like.
  • the nanocrystalline alloy ribbon is produced by ejecting a molten alloy adjusted to a predetermined alloy composition onto a rotating cooling roll, rapidly cooling and solidifying it to produce an alloy ribbon, and then heat-treating the alloy ribbon. be done.
  • the nanocrystalline alloy ribbon is thin, has 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, magnetic properties are maintained in the longitudinal direction of the elongated shape and in the width direction orthogonal to the longitudinal direction. tend to be different.
  • nanocrystalline alloy ribbons used in motors are required to have isotropic properties as much as possible.
  • a nanocrystalline alloy ribbon having excellent magnetic properties (high saturation magnetic flux density, low iron loss) and isotropy can be obtained by a highly productive method. was difficult to obtain.
  • the present disclosure provides a nanocrystalline alloy ribbon having excellent magnetic properties and isotropy, and a nanocrystalline alloy ribbon that suppresses wrinkles or streaks and realizes a high space factor. It is an object of the present invention to provide a method for producing nanocrystalline alloy ribbons, which can obtain them and obtain them in a highly productive manner. In addition, a nanocrystalline alloy ribbon obtained by the method and having excellent magnetic properties and isotropy, and a nanocrystalline alloy ribbon that suppresses wrinkles or streaks and realizes a high space factor. intended to provide
  • the present disclosure has the following configurations. ⁇ 1>
  • the amorphous alloy ribbon is brought into contact with a heating body to heat the amorphous alloy ribbon, thereby obtaining a nanocrystalline alloy thin film having a structure in which crystal grains having an average grain size of 30 nm or less exist in the amorphous phase.
  • the nanocrystalline alloy ribbon is represented by the composition formula (Fe 1-x A x ) a Si b B c Cu d Me , where A is at least one of Ni and Co, and M is Nb, Mo, V , Zr, Hf and W, in terms of atomic %, 80.0 ⁇ a ⁇ 87.0, 0 ⁇ b ⁇ 9.0, 12.0 ⁇ c ⁇ 16.0, 0 ⁇ d ⁇ 1.5, 0 ⁇ e ⁇ 1.5, 0 ⁇ x ⁇ 0.1;
  • the amorphous alloy ribbon is brought into contact with the heating body to heat the amorphous alloy ribbon, the amorphous alloy ribbon is conveyed and the The ribbon pressing member is in contact with the surface opposite to the surface that contacts the heating body, and the amorphous alloy ribbon is heated while being sandwiched between the heating body and the ribbon pressing member,
  • the bccFe crystallization start temperature measured at a heating rate of 20 K/min
  • a method for producing a crystal alloy ribbon ⁇ 2> The method for producing a nanocrystalline alloy ribbon according to ⁇ 1>, wherein the ribbon pressing member is a flexible member. ⁇ 3> When the amorphous alloy ribbon is brought into contact with the heating body to heat the amorphous alloy ribbon, the heating rate of the amorphous alloy ribbon is 50°C/sec to 4000°C. / second, the method for producing a nanocrystalline alloy ribbon according to ⁇ 1> or ⁇ 2>.
  • ⁇ 4> When the amorphous alloy ribbon is brought into contact with the heating body to heat the amorphous alloy ribbon, the conveying speed of the amorphous alloy ribbon is 1 m/min or more ⁇ 1 A method for producing a nanocrystalline alloy ribbon according to any one of ⁇ 3>.
  • ⁇ 5> When the amorphous alloy ribbon is brought into contact with the heating body to heat the amorphous alloy ribbon, the contact time of the amorphous alloy ribbon with the heating body is 0.1. The method for producing a nanocrystalline alloy ribbon according to any one of ⁇ 1> to ⁇ 4>, wherein the time is from 1 to 30 seconds.
  • ⁇ 6> The maximum temperature of the amorphous alloy ribbon heated in contact with the heating body, where the FeB precipitation start temperature measured at a heating rate of 20 K/min of the amorphous alloy ribbon is Tx2°C.
  • ⁇ 7> In the composition formula, 82.0 ⁇ a ⁇ 86.5, 0.01 ⁇ b ⁇ 3.0, 13.0 ⁇ c ⁇ 15.0, 0.01 ⁇ d ⁇ 1.5, 0 ⁇
  • ⁇ 8> The amorphous alloy ribbon is heated while being pressed against the heating body or the ribbon holding member, and the pressure pressing the amorphous alloy ribbon against the heating body is 0.03 MPa or more.
  • ⁇ 9> The nanocrystal according to any one of ⁇ 1> to ⁇ 8>, wherein the surface of the nanocrystalline alloy ribbon has a wrinkle height of 0.15 mm or less and a space factor of 84.0% or more.
  • ⁇ 10> The method for producing a nanocrystalline alloy ribbon according to any one of ⁇ 1> to ⁇ 9>, wherein the nanocrystalline alloy ribbon has a saturation magnetic flux density Bs of 1.75 T or more.
  • ⁇ 12> Any one of ⁇ 1> to ⁇ 11>, wherein the nanocrystalline alloy ribbon has a coercive force Hc of 25 A/m or less, a core loss (1 T, 1 kHz) of 15 W/kg or less, and a saturation magnetostriction of 20 ppm or less. 2.
  • ⁇ 13> The method for producing a nanocrystalline alloy ribbon according to any one of ⁇ 1> to ⁇ 12>, wherein the amorphous alloy ribbon has a thickness of 20 ⁇ m or more and a width of 10 mm or more.
  • a nanocrystalline alloy ribbon having a structure in which crystal grains having an average grain size of 30 nm or less exist in an amorphous phase It is represented by the composition formula (Fe 1-x A x ) 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 saturation magnetic flux density Bs is 1.75 T or more
  • ⁇ 16> The nanocrystalline alloy ribbon according to ⁇ 14> or ⁇ 15>, wherein the surface of the nanocrystalline alloy ribbon has a wrinkle height of 0.15 mm or less and a space factor of 84.0% or more.
  • ⁇ 17> The nanocrystalline alloy according to any one of ⁇ 14> to ⁇ 16>, having a coercive force Hc of 25 A/m or less, an iron loss (1 T, 1 kHz) of 15 W/kg or less, and a saturation magnetostriction of 20 ppm or less.
  • ribbon. ⁇ 18> The nanocrystalline alloy ribbon according to any one of ⁇ 14> to ⁇ 17>, which has a thickness of 20 ⁇ m or more and a width of 10 mm or more.
  • a nanocrystalline alloy ribbon that has excellent magnetic properties and is isotropic, and a nanocrystalline alloy ribbon that suppresses wrinkles or streaks and realizes a high space factor.
  • a nanocrystalline alloy ribbon obtained by the method and having excellent magnetic properties and isotropy, and a nanocrystalline alloy ribbon that suppresses wrinkles or streaks and realizes a high space factor. can be provided.
  • FIG. 1 is a conceptual diagram showing one embodiment of a heat treatment method of the present disclosure
  • FIG. FIG. 4 is a conceptual diagram showing another embodiment of the heat treatment method of the present disclosure
  • FIG. 4 is a conceptual diagram showing another embodiment of the heat treatment method of the present disclosure
  • 4 is a laser micrograph showing evaluation of the wrinkle height of the amorphous alloy ribbon before heat treatment of Sample No. 4 of the present disclosure.
  • FIG. 10 is a laser microscope photograph for evaluating the wrinkle height of Sample No. 8 of the present disclosure
  • FIG. FIG. 10 is a laser microscope photograph for evaluating the wrinkle height of Sample No. 9 of the present disclosure
  • FIG. 4 is a laser microscope photograph for evaluating the wrinkle height of Sample No. 4 of the present disclosure. It is an example of a temperature profile during the heat treatment of the present disclosure.
  • a numerical range indicated using “to” indicates a range including the numerical values described before and after "to” as lower and upper limits, respectively.
  • upper or lower limits described in a certain numerical range may be replaced with upper or lower limits of other numerical ranges described step by step.
  • upper or lower limits described in a certain numerical range may be replaced with values shown in Examples.
  • a combination of two or more preferred aspects is a more preferred aspect.
  • the nanocrystalline alloy ribbon of the present disclosure is represented by the composition formula ( Fe1 - xAx ) aSibBcCudMe , where A is at least one of Ni and Co, M is Nb , Mo , V, Zr, Hf and W, in terms of atomic %, 80.0 ⁇ a ⁇ 87.0, 0 ⁇ b ⁇ 9.0, 12.0 ⁇ c ⁇ 16.0, 0 ⁇ d ⁇ 1.5, 0 ⁇ e ⁇ 1.5, and 0 ⁇ x ⁇ 0.1.
  • Fe is 80.0% or more and 87.0% or less in atomic %.
  • a high saturation magnetic flux density can be obtained by setting the Fe content to 80.0% or more. preferably 81% or more, more preferably 82.0% or more, still more preferably 82.5% or more, still more preferably 83% or more, still more preferably 83.5% or more, More preferably, it is 84% or more.
  • the Fe content exceeds 87.0%, it becomes difficult to amorphize, so the Fe content is made 87.0% or less. It is preferably 86.5% or less, more preferably 86% or less.
  • part of Fe may be replaced with at least one element selected from Ni and Co.
  • A is at least one of Ni and Co
  • Co has the effect of increasing the saturation magnetic flux density by substituting Fe, but it is very expensive and increases the coercive force and iron loss. 0.03 or less.
  • a represented by (Fe 1-x A x ) a is within the range of 80.0% to 87.0% of Fe (80.0% to 87.0%). 0 ⁇ a ⁇ 87.0). preferably 81% or more, more preferably 82.0% or more, still more preferably 82.5% or more, still more preferably 83% or more, still more preferably 83.5% or more, More preferably, it is 84% or more. Also, it is preferably 86.5% or less, more preferably 86% or less.
  • Si is 0% or more and 9.0% or less in atomic %. Si may be 0%.
  • Si may be 0%.
  • an oxide film of SiO 2 with a thickness of several tens of nanometers can be formed on the surface of the alloy. This can improve the corrosion resistance of the nanocrystalline alloy ribbon.
  • B (boron) is 12.0% or more and 16.0% or less in atomic %. If the B content is less than 12.0%, it becomes difficult to form an amorphous material, so the B content is made 12.0% or more. It is preferably 12.5% or more, more preferably 13.0% or more, further preferably 13.5% or more. When the B content exceeds 16.0%, the difference between the bccFe( ⁇ Fe) crystallization start temperature and the FeB precipitation start temperature becomes small, narrowing the temperature range in which heat treatment is possible. When the temperature range in which heat treatment is possible is narrowed, productivity is likely to be affected. Therefore, the content of B is set to 16.0% or less. It is preferably 15.0% or less, more preferably 14.5% or less, still more preferably 14.4% or less.
  • Cu copper
  • the content of Cu may be 0%, but the inclusion of Cu facilitates obtaining a uniform and fine nanocrystalline structure.
  • the Cu content is preferably 0.01% or more. It is more preferably 0.05% or more, and still more preferably 0.1% or more. Furthermore, it may be 0.2% or more, or 0.4% or more, or 0.5% or more. If the Cu content exceeds 1.5%, embrittlement tends to occur, making it difficult to increase the thickness of the soft magnetic alloy ribbon. Therefore, the Cu content is set to 1.5% or less. It is preferably 1.0% or less, more preferably 0.9% or less. Furthermore, it may be 0.85% or less, or 0.7% or less, or 0.6% or less.
  • the M element is at least one selected from Nb, Mo, V, Zr, Hf and W, and its atomic % is 0% or more and 1.5% or less.
  • the M element may be 0%, but by including the M element, the precipitation start temperature of the FeB compound that significantly deteriorates the soft magnetism can be shifted to a higher temperature side. As a result, the difference between the bccFe( ⁇ Fe) crystallization start temperature and the FeB precipitation start temperature can be widened, which has the effect of widening the optimum heat treatment temperature range and relaxes the heat treatment conditions. It is preferably 0.1% or more, more preferably 0.15% or more. Since the M element is expensive, the price rises. Therefore, the smaller the content, the better.
  • the M element content is set to 1.5% or less. It is preferably 1.0% or less, more preferably 0.9% or less. Furthermore, it may be 0.8% or less, or 0.7% or less, or 0.6% or less. Also, the M element is preferably less than 0.4%, more preferably 0.3% or less, and further preferably 0.25% or less.
  • the nanocrystalline alloy ribbon of the present disclosure may contain C (carbon).
  • C is preferably 1% by mass or less.
  • the fluidity of the molten metal is improved (the viscosity of the molten metal is reduced), the adhesion with the cooling roll is improved, and the effect of contributing to the smoothing of the surface of the alloy ribbon can be expected. is likely to segregate on the surface of the alloy ribbon, and is expected to have the effect of promoting structural relaxation and improving the squareness of the DC BH curve when diffusing on the surface during heat treatment.
  • C when C is contained, it is preferably 0.03% by mass or more.
  • the nanocrystalline alloy ribbon of the present disclosure may contain impurities other than the above elements.
  • Impurities include, for example, S (sulfur), O (oxygen), N (nitrogen), Cr, Mn, P, Ti, and Al.
  • the S content is preferably 200 mass ppm or less
  • the O content is preferably 5000 mass ppm or less
  • the N content is preferably 1000 mass ppm or less
  • the Ti content is preferably 1000 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 within the above range.
  • the nanocrystalline alloy ribbon of the present disclosure is obtained by ejecting a molten alloy having the alloy composition described above onto a rotating cooling roll, rapidly cooling and solidifying it on the cooling roll to obtain an alloy ribbon, and heat-treating the alloy ribbon.
  • the alloy ribbon obtained by quenching and solidifying the molten alloy has an alloy structure in an amorphous state, and is an amorphous alloy ribbon.
  • a nanocrystalline alloy ribbon is obtained by heat-treating this amorphous alloy ribbon.
  • the amorphous alloy ribbon obtained by quenching and solidifying the molten alloy may contain a crystalline phase composed of fine crystals.
  • the molten alloy can be obtained by blending each element source (pure iron, ferroboron, ferrosilicon, etc.) for the desired alloy composition, heating in an induction heating furnace, and melting above the melting point to obtain a molten alloy.
  • An alloy ribbon can be obtained by ejecting a molten alloy from a slit-shaped nozzle having a predetermined shape onto a rotating cooling roll and rapidly solidifying the molten alloy on the cooling roll.
  • the cooling roll can 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 roll is internally provided with a cooling mechanism (such as water cooling) for suppressing an increase in the temperature of the outer peripheral portion.
  • the outer peripheral portion of the cooling roll is 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 cooling rate when the molten alloy is cast into the alloy ribbon can be increased.
  • the embrittlement of the alloy ribbon is suppressed, making it possible to increase the thickness of the alloy ribbon, and surface crystallization during casting is suppressed, thereby suppressing coarsening of crystal grains during heat treatment. , iron loss can be reduced.
  • the thermal conductivity of the outer peripheral portion of the chill roll is preferably 150 W/(m ⁇ K) or more, more preferably 180 W/(m ⁇ K) or more.
  • the thermal conductivity of the outer peripheral portion is preferably 150 W/(m ⁇ K) or more.
  • the outer peripheral portion of the cooling roll is the portion in contact with the molten alloy, and the thickness thereof may be about 5 to 15 mm.
  • a nanocrystalline alloy ribbon is obtained by heat-treating the amorphous alloy ribbon produced by the above quenching method.
  • the method for manufacturing the nanocrystalline alloy ribbon of the present disclosure is characterized by the heat treatment method.
  • the heat treatment method of the present disclosure is a method of heating the amorphous alloy ribbon by contacting the amorphous alloy ribbon and a heating body, and bringing the amorphous alloy ribbon and the heating body into contact to heat the amorphous alloy ribbon.
  • the amorphous alloy ribbon is heated, the amorphous alloy ribbon is conveyed, and the surface of the amorphous alloy ribbon opposite to the surface in contact with the heating body is brought into contact with the ribbon pressing member, and the heating body and the thin film are brought into contact with each other.
  • the amorphous alloy ribbon is heated while being sandwiched between it and the band pressing member.
  • the heating temperature Ta of the heater is Tx1+80°C or higher and Tx1+160°C or lower.
  • the heating rate of the amorphous alloy ribbon is preferably set to 50° C./sec to 4000° C./sec. Further, the conveying speed of the amorphous alloy ribbon is preferably 1 m/min or more.
  • the amorphous alloy ribbon may be pressed against the heating body by pressing a flexible member against the surface of the amorphous alloy ribbon opposite to the surface that contacts the heating body.
  • a metal member is preferably used as the flexible member.
  • a belt or a roll may be used as the ribbon pressing member.
  • FIG. 1 is a conceptual diagram showing one embodiment of the heat treatment method of the present disclosure.
  • the heat treatment method shown in FIG. 1 includes a heating roller 2 serving as a heating body, a ribbon pressing metal belt 3 (a ribbon pressing member), and rollers 4 and 5 supporting the ribbon pressing metal belt 3. .
  • the heating roller 2 and the ribbon presser metal belt 3 are arranged in a contactable state.
  • the amorphous alloy ribbon 1 is heated while the amorphous alloy ribbon 1 is sandwiched.
  • the amorphous alloy ribbon 1 is pressed against the heating member (heating roller 2) by the ribbon pressing metal belt 3 (thin ribbon pressing member).
  • the ribbon pressing metal belt 3 (the ribbon pressing member) may press the amorphous alloy ribbon 1 against the heating member (heating roller 2). It may be in a state in which the raw alloy ribbon 1 is pressed against a ribbon pressing metal belt 3 (a ribbon pressing member).
  • a ribbon pressing member a ribbon pressing member
  • arrows indicate the movement of each part, and the heating roller 2 and rollers 4 and 5 are structured to rotate.
  • the amorphous alloy ribbon 1 (hereinafter also referred to as the ribbon 1) is heated while being conveyed and pressed against the heating roller 2.
  • the ribbon presser metal belt 3 As shown in FIG. It is preferable to use heating rollers capable of heating the rollers 4 and 5 as well. Therefore, it is preferable to heat the ribbon presser metal belt 3 .
  • the temperature of the ribbon presser metal belt 3 (the temperature when in contact with the ribbon 1) is preferably 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 a temperature that makes the temperature of the ribbon presser metal belt 3 appropriate.
  • the temperature of the rollers 4 and 5 it is desirable to set the temperature of the rollers 4 and 5 about 50° C. higher than the temperature of the heating element.
  • the temperature suitable for the heat treatment of the strip 1 can be selected.
  • the ribbon 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. For example, it is more preferable to use a material with excellent heat resistance such as heat-resistant stainless steel or a nickel-based super heat-resistant alloy.
  • the structure is such that the flexible member (thin ribbon holding metal belt 3) is pressed against the surface of the amorphous alloy ribbon 1 opposite to the surface in contact with the heating body. 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 together. preferably.
  • the heating roller 2 is a heating body (heating body of the present disclosure) for directly contacting and heating the amorphous alloy ribbon.
  • the amorphous alloy ribbon 1 abuts (contacts) a part (partial region in the circumferential direction) of the outer peripheral surface of the cylindrical heating roller 2 and is heated.
  • the heating roller 2 may be provided with a driving force for conveying the amorphous alloy ribbon.
  • Either one of the rollers 4 and 5 may be used as the rollers for driving the ribbon presser metal belt 3 .
  • the roller 5 may be provided with a driving force, and the roller 4 may be driven mechanically. This makes it possible to avoid complicated control such as electrical synchronous operation of the rollers 4 and 5, and further eliminates the need to correct the synchronous deviation due to the difference 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 contacting and heating the amorphous alloy ribbon.
  • convex surface means a surface that rises toward the side of the amorphous alloy ribbon, and like the roller shown in FIG. Any shape such as a curved surface configured as a part of the member can be used as long as the amorphous alloy ribbon can follow and ensure sufficient contact.
  • FIG. 2 is a conceptual diagram showing another embodiment of the heat treatment method of the present disclosure.
  • the heat treatment method shown in FIG. 2 includes a heating roller 2 as a heating body, and ribbon pressing rollers 6, 7 and 8 as ribbon pressing members for pressing the amorphous alloy ribbon 1 against the heating roller 2 as a heating body.
  • the ribbon 1 is passed between the heating roller 2 (heating member) and the ribbon pressing rollers 6, 7 and 8, and is heated while being pressed against the heating member (heating roller 2).
  • the arrows indicate the movement of each part, and the heating roller 2 and ribbon pressing rollers 6, 7 and 8 are structured to rotate. Thereby, the amorphous alloy ribbon 1 is heated while being conveyed and pressed against the heating roller 2 .
  • FIG. 3 is a conceptual diagram illustrating another embodiment of the heat treatment method of the present disclosure.
  • a metal belt 33 and rollers 34 and 35 for supporting the metal belt 33 for holding the thin ribbon are provided.
  • the thin ribbon 1 is passed between the heating member 32 and the thin ribbon pressing metal belt 33 (thin ribbon pressing member), and the thin ribbon 1 is heated while being pressed against the heating member 32 .
  • Arrows indicate movements of respective parts, and the rollers 34 and 35 are structured to rotate. Thereby, the amorphous alloy ribbon 1 is heated while being conveyed and pressed against the heating body 32 .
  • the amorphous alloy ribbon when the amorphous alloy ribbon is brought into contact with the heating body to heat the amorphous alloy ribbon, the amorphous alloy ribbon is conveyed while the heating body is heated.
  • the amorphous alloy ribbon can be heated while being sandwiched between it and the ribbon pressing member.
  • the heating rate of the amorphous alloy ribbon is preferably 50° C./second to 4000° C./second.
  • the heating rate at which a fine nanocrystalline structure is realized differs depending on the composition. A temperature rate is required.
  • the lower limit of the temperature rise rate is 50° C./sec
  • the upper limit is the facility capacity of the heat treatment apparatus, the temperature of the heating body and the ribbon pressing member, and the contact state between the heating body and the ribbon pressing member and the ribbon. etc., but it is substantially about 4000° C./sec. It is preferably 500° C./second or more.
  • the heating body preferably has a width wider than that of the amorphous alloy ribbon.
  • the entire width of the ribbon comes into close contact with the heating body.
  • the distance from the contact of the amorphous alloy ribbon to the heating body until it separates from the heating body is 50 mm or more in terms of the length of the surface of the heating body. It is preferable to Further, it is more preferable that the distance between the contact of the amorphous alloy ribbon with the heating body and separation from the heating body is 150 mm or more in the length of the surface of the heating body.
  • the conveying speed of the amorphous alloy ribbon is preferably 1 m/min or more. In mass production, the faster the conveying speed, the higher the production volume, so the conveying speed is more preferably 10 m/min or more.
  • the contact time between the amorphous alloy ribbon and the heater is preferably 0.1 to 30 seconds.
  • the lower limit of contact time is more preferably 0.2 seconds, and the upper limit of contact time is more preferably 10 seconds, more preferably 5 seconds, and most preferably 2 seconds. In order to improve mass productivity, it is preferable to set the time from 0.2 seconds to 2 seconds when speeding up and stabilizing.
  • the maximum temperature reached by the ribbon may be higher than the temperature of the heating element due to self-heating associated with crystallization of the ribbon. If the temperature of the amorphous alloy ribbon becomes too high, desired magnetic properties cannot be obtained. Therefore, it is preferable to control the temperature of the ribbon to Tx2 + 160°C or less, where Tx2°C is the precipitation start temperature of FeB measured at a heating rate of 20 K/min for the amorphous alloy ribbon.
  • the heating temperature Ta, the transport speed, etc. are set so that this control can be performed. If the temperature exceeds Tx2+160° C., FeB precipitates and the magnetic properties deteriorate significantly.
  • the heat treatment method of the present disclosure by pressing the amorphous alloy ribbon against the heating body, the contact between the heating body and the ribbon is improved, the heat transfer is improved, and the temperature rise rate is increased. , more heat generated by crystallization can be released to the heating body and the pressing belt or roll, and the maximum temperature of the ribbon can be suppressed (temperature rise due to self-heating can be suppressed). Furthermore, wrinkles or streaks that tend to occur during crystallization can be suppressed by pressing with a belt or roll. As a result, heat treatment at higher temperatures becomes possible, and heat treatment can be performed at a high rate of temperature rise and with short-time contact. Therefore, productivity can be improved and a uniform nanocrystalline structure can be obtained, and a nanocrystalline alloy ribbon having a higher saturation magnetic flux density and excellent magnetic properties can be obtained.
  • the heating rate and maximum temperature of the amorphous alloy ribbon during heat treatment were confirmed by the following methods.
  • 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 perform fixed-point measurement, temperature measurement of the amorphous alloy ribbon during heat treatment was performed without transporting the ribbon.
  • the thin ribbon presser metal belt 33 is not driven, the ribbon 1 is placed between the thin ribbon presser metal belt 33 and the heater 32, and tension is applied to the ribbon presser metal belt 33. Then, the ribbon 1 is pressed against the heating body 32. As shown in FIG.
  • FIG. 8 shows an example temperature profile measured.
  • the x-axis is time (seconds) and the y-axis is the measured ribbon temperature.
  • the contact time in FIG. 8 is the time during which the ribbon was pressed against the heating element. According to this measuring method, the ribbon temperature rises to about 400° C. before contacting the heating element. Therefore, as shown in FIG.
  • the rate of temperature increase was calculated as a value obtained by dividing the change in temperature from the point of contact with the heating plate until reaching the set temperature (520° C.) by the time.
  • the maximum temperature of the ribbon was the maximum temperature of the peak that appeared after the ribbon contacted the heating element.
  • the temperature of the ribbon was measured by making a measurement hole in the metal ribbon pressing belt 33 .
  • the pressure for pressing the amorphous alloy ribbon against the heating body is preferably 0.03 MPa or more. It is more preferably 0.04 MPa or more, still more preferably 0.05 MPa or more. In order to improve the contact between the amorphous alloy ribbon and the heating body, it is also effective to give the heating body a curvature. As for the curvature of the heating element, the radius of curvature is preferably 25 mm or more. In order to increase the rate of temperature rise during heating of the amorphous alloy ribbon, it is also effective to heat the pressing belt or roll to the same temperature as the heating body and heat the ribbon from both sides. , 3, heating rolls are used as the rolls 4, 5, 6, 7, 8, 34, and 35. It is also effective to set the temperature of the belt or rolls lower than the hot plate temperature Ta° C. in order to suppress the heat generated by the bccFe crystallization of the ribbon.
  • a nanocrystalline alloy ribbon having excellent magnetic properties and isotropy, and a nanocrystalline alloy ribbon that suppresses wrinkles or streaks and realizes a high space factor is obtained. be able to.
  • the nanocrystalline alloy ribbon of the present disclosure has a saturation magnetic flux density Bs of 1.75 T or more, preferably 1.80 T 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 field of 80 A / m in the width direction orthogonal to the longitudinal direction. It is preferable that the ratio (B80 L /B80 W ) of the magnetic flux density B80 W of is 0.80 to 1.20, and that both B80 L and B80 W are 1.0 T or more. (B80 L /B80 W ) is more preferably 0.90 to 1.10.
  • the nanocrystalline alloy ribbon of the present disclosure preferably has a space factor of 84.0% or more.
  • the space factor is preferably 86% or more, more preferably 88% or more.
  • the space factor can be measured by the following method based on JIS C 2534:2017. Twenty strips cut to a length of 120 mm are stacked and set on a flat sample stage, and a flat anvil with a diameter of 16 mm is placed on the stacked strip under a pressure of 50 kPa to measure the height at intervals of 10 mm in the width direction. Assuming that the maximum height at that time is hmax ( ⁇ m), the space factor LF is obtained from the following formula.
  • LF (%) sample weight (g)/density (g/cm 3 )/hmax ( ⁇ m)/sample length (240 cm)/ribbon width (cm) ⁇ 10000
  • the density (g/cm 3 ) is the density of the alloy ribbon after heat treatment. This density can be 7.5 g/cm 3 .
  • the amorphous alloy ribbon When the amorphous alloy ribbon is brought into contact with a heating body and heated to make the amorphous alloy ribbon into a nanocrystalline alloy ribbon, non-uniformity may occur due to variations in contact between the amorphous alloy ribbon and the heating body. If there is a local difference in the heating rate or temperature of the crystalline alloy ribbon, the progress of crystallization will also differ. As a result, localized distortion occurs, causing the problem that the alloy ribbon floats up from the heating body. At the raised portion, the self-heating due to crystallization becomes difficult to escape to the heating body, the alloy ribbon temperature rises rapidly, reaches the FeB precipitation temperature, and wrinkles or streaks are likely to occur. As a result, the space factor decreases and the wrinkles or streaks become very fragile, causing handling problems such as cracking during transportation and stacking, and deterioration of magnetic properties.
  • the amorphous alloy ribbon is pressed against the heating body by a ribbon holding member that contacts the opposite side of the amorphous alloy ribbon to the heating body, whereby the amorphous alloy ribbon is It is possible to uniformly heat the strip and suppress the floating of the alloy strip by pressing down, thereby suppressing the occurrence of wrinkles or streaks. Furthermore, it also has the effect of correcting wrinkles and the like caused by uneven cooling during casting of the amorphous alloy ribbon. Thereby, according to the present disclosure, wrinkles or streaks are suppressed, and a nanocrystalline alloy ribbon with good flatness is obtained.
  • the nanocrystalline alloy ribbon of the present disclosure preferably has wrinkles or streaks with a height of 0.15 mm or less. More preferably, it is 0.10 mm or less. In the present disclosure, the height of wrinkles or streaks is also referred to as "wrinkle height.” Further, the wrinkle height can be evaluated by the method described in Examples below.
  • the nanocrystalline alloy ribbon of the present disclosure has a coercive force Hc of 25 A/m or less, preferably 15 A/m or less, an iron loss (1 T, 1 kHz) of 15 W/kg or less, preferably 10 W/kg or less, and a saturation magnetostriction of 20 ppm. Below, it is preferably 15 ppm.
  • the thickness of the nanocrystalline alloy ribbon of the present disclosure is preferably 20 ⁇ m or more, more preferably 25 ⁇ m or more, and even more preferably 30 ⁇ m or more.
  • the width is preferably 10 mm or more, more preferably 100 mm or more, and still more preferably 200 mm or more.
  • the thickness of the nanocrystalline alloy ribbon of the present disclosure is preferably 50 ⁇ m or less because it becomes difficult to obtain good magnetic properties when the thickness is increased. Moreover, it is more preferably 40 ⁇ m or less.
  • the width of the nanocrystalline alloy ribbon of the present disclosure is too wide, stable production becomes difficult, so the width is preferably 500 mm or less. Moreover, it is more preferably 400 mm or less.
  • the nanocrystalline alloy ribbon of the present disclosure can be used to form magnetic cores for use in transformers, electronic components, motors, and the like, so that magnetic cores with excellent properties can be obtained.
  • the magnetic core can be formed by stacking an alloy ribbon cut into a predetermined shape, winding the alloy ribbon, or stacking and bending the alloy ribbon.
  • the magnetic core and windings of the present disclosure may be combined with a magnetic core made of another magnetic material.
  • Example 1 An element source was blended so as to have each composition shown in Table 1, heated to 1300 ° C. to prepare a molten alloy, and the molten alloy was rotated at a peripheral speed of 30 m / sec on a cooling roll with an outer diameter of 400 mm and a width of 200 mm. and rapidly solidified on a cooling roll to produce an amorphous alloy ribbon.
  • the outer peripheral portion of the cooling roll is made of a Cu alloy with a thermal conductivity of 150 W/(m ⁇ K), and has a cooling mechanism for controlling the temperature of the outer peripheral portion.
  • the width of the produced amorphous alloy ribbon was 50 mm, and the thickness was 30 ⁇ m.
  • Amorphous alloy ribbons of each material were measured using a Rigaku differential scanning calorimeter DSC8231 at a heating rate of 20 K/min. °C and were measured. Table 1 shows the results.
  • a magnetic field of 8000 A/m is applied to the heat-treated veneer sample using a DC magnetization property tester manufactured by Metron Giken, and the maximum magnetic flux density at that time is measured and defined as Bs. Since the nanocrystalline alloy ribbon of the present disclosure is relatively easily saturated, it is saturated at the time of applying a magnetic field of 8000 A / m. Bs is represented by B8000 .
  • Magnetic flux density B80 A magnetic field of 80 A/m was applied to the nanocrystalline alloy ribbon in the longitudinal direction (casting direction) and in the width direction perpendicular to the longitudinal direction using a DC magnetization property tester manufactured by Metron Giken, and the maximum magnetic flux densities at that time were B80 L and B80, respectively. W , and the ratio B80 L /B80 W was calculated to evaluate the isotropy.
  • ⁇ Particle size ⁇ Particle size refers to the average particle size of the nanocrystals.
  • volume fraction is the volume fraction of nanocrystals, and the portion other than the nanocrystals is the amorphous portion. This volume fraction is determined by the ratio of the integrated intensity of nanocrystals and the integrated intensity of (crystal+amorphous).
  • the integrated intensity of the peak indicated by the nanocrystal and the halo pattern indicated by the amorphous is obtained by performing peak decomposition using the pseudo-Voigt function for the X-ray diffraction pattern, and the sum of the integrated intensities of all the peaks indicated by the nanocrystal is Ic, Assuming that the sum of the integrated intensities of all the halo patterns exhibited by the amorphous is Ia, the volume ratio V can be obtained from the formula (Equation 2) given below.
  • the wrinkle height is the height of wrinkles or streaks formed on the surface of the ribbon.
  • the height of the surface was measured, and the difference between the maximum value and the minimum value was calculated as the wrinkle height.
  • the reason why the ribbon is sandwiched between the glass plates is that if the ribbon is placed on the measurement stage alone, it will be partially lifted by undulations, etc., and this will affect the height of the ribbon. .
  • the field of view of the laser microscope was about 18 mm ⁇ 25 mm, three points of each sample were measured, and the largest value was taken as the wrinkle height.
  • a glass plate of 70 mm ⁇ 70 mm and a thickness of 3 mm was used.
  • FIG. 4 shows the evaluation results of the amorphous alloy ribbon of Sample No. 4 before heat treatment.
  • FIG. 5 shows the measurement results of the nanocrystalline alloy ribbon (No. 8) obtained by heat-treating the amorphous alloy ribbon of sample No. 4 before heat treatment at 510° C. without pressing. It was found that the wrinkles formed during the heat treatment were raised, and the difference between the maximum value and the minimum value (wrinkle height) was 0.156 mm. Moreover, the space factor of No. 8 was 83.5%.
  • FIG. 6 shows the measurement results of the nanocrystalline alloy ribbon (No. 9) obtained by heat-treating the amorphous alloy ribbon of sample No. 4 before heat treatment at 515° C. without pressing.
  • FIG. 7 shows the measurement results of the nanocrystalline alloy ribbon shown in sample No. 4, which was heat-treated at a pressing pressure of 0.115 MPa and a heating element temperature of 530°C. There were no wrinkles and the wrinkle height was 0.052 mm, which was better than that of the amorphous alloy ribbon. By heat-treating the ribbon while holding it down, wrinkles or streaks can be suppressed, and heat treatment can be performed at a higher temperature than when there is no presser. And the space factor was as good as 89.3%.
  • Example No. 7 the wrinkle height was as high as 0.220 mm.
  • the pressing pressure of the ribbon pressing member was as low as 0.029 MPa, which is considered to be the reason why the height of wrinkles was high.
  • Bs is 1.75 T or more
  • B80 L and B80 W are both 1.0 T or more
  • the ratio B80 L /B80 W is in the range of 0.80 to 1.20.
  • the coercive force Hc and iron loss were low, and excellent magnetic properties were exhibited. Therefore, a nanocrystalline alloy ribbon having excellent magnetic properties and isotropy was obtained.
  • a nanocrystalline alloy ribbon having a low wrinkle height, suppressed wrinkles or streaks, and realizing a high lamination factor was obtained.
  • a nanocrystalline alloy ribbon was obtained in which the average grain size of the nanocrystals was 30 nm or less and the volume fraction of the nanocrystals was 30% or more. In samples Nos.
  • the ribbon was heat-treated without being pressed against the heating body, and B80 L /B80 W did not fall within the range of 0.80 to 1.20, and the coercive force Hc was It was a high result.
  • Samples No. 8 and No. 9 were heat-treated without pressing the ribbon against the heating body, resulting in large wrinkles and a low lamination factor.
  • Sample No. 19 had a ribbon maximum temperature exceeding Tx2+160° C., a high (bad) coercive force Hc and core loss, a low B80, and a B80 L /B80 W greater than 1.2.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Power Engineering (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Electromagnetism (AREA)
  • Dispersion Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Soft Magnetic Materials (AREA)
PCT/JP2022/023736 2021-06-16 2022-06-14 ナノ結晶合金薄帯の製造方法、およびナノ結晶合金薄帯 Ceased WO2022264999A1 (ja)

Priority Applications (1)

Application Number Priority Date Filing Date Title
JP2022559370A JPWO2022264999A1 (https=) 2021-06-16 2022-06-14

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP2021-099933 2021-06-16
JP2021099933 2021-06-16
JP2021129413 2021-08-06
JP2021-129413 2021-08-06

Publications (1)

Publication Number Publication Date
WO2022264999A1 true WO2022264999A1 (ja) 2022-12-22

Family

ID=84526520

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2022/023736 Ceased WO2022264999A1 (ja) 2021-06-16 2022-06-14 ナノ結晶合金薄帯の製造方法、およびナノ結晶合金薄帯

Country Status (2)

Country Link
JP (1) JPWO2022264999A1 (https=)
WO (1) WO2022264999A1 (https=)

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPWO2023127199A1 (https=) * 2021-12-28 2023-07-06
JPWO2023127198A1 (https=) * 2021-12-28 2023-07-06
WO2023190770A1 (ja) * 2022-03-30 2023-10-05 株式会社プロテリアル 磁性シートの製造方法
DE102023122712A1 (de) * 2023-08-24 2025-02-27 Vacuumschmelze Gmbh & Co. Kg Gegenstand aus einer nanokristallinen weichmagnetischen Legierung und Verfahren zum Herstellen einer nanokristallinen weichmagnetischen Legierung
JP2025065896A (ja) * 2023-10-10 2025-04-22 トヨタ自動車株式会社 軟磁性材料及びその製造方法
JP7765140B1 (ja) * 2025-07-02 2025-11-06 ネクストコアテクノロジーズ株式会社 鉄基軟磁性合金およびその製造方法

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5483622A (en) * 1977-12-16 1979-07-03 Matsushita Electric Ind Co Ltd Heat treatment method for amorphous magnetic alloy sheet
JPS63302504A (ja) * 1987-06-02 1988-12-09 Hitachi Metals Ltd 磁心およびその製造方法
JPH0219442A (ja) * 1988-07-07 1990-01-23 Nippon Steel Corp 超微細結晶組織を有する高飽和磁束密度Ｆｅ基合金
JP2002280224A (ja) * 2001-01-05 2002-09-27 Humanelecs Co Ltd アモルファス合金粉末コア及びナノクリスタル合金粉末コア並びにそれらの製造方法
JP2013055182A (ja) * 2011-09-02 2013-03-21 Nec Tokin Corp 軟磁性合金粉末、ナノ結晶軟磁性合金粉末、その製造方法、および圧粉磁心
JP2016145373A (ja) * 2015-02-06 2016-08-12 Ｎｅｃトーキン株式会社 Ｆｅ基ナノ結晶合金の製造方法

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10337081B2 (en) * 2016-11-04 2019-07-02 Metglas, Inc. Apparatus for annealing alloy ribbon and method of producing annealed alloy ribbon
WO2022065370A1 (ja) * 2020-09-25 2022-03-31 日立金属株式会社 非晶質合金リボンの熱処理方法、及び非晶質合金リボンの熱処理装置

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5483622A (en) * 1977-12-16 1979-07-03 Matsushita Electric Ind Co Ltd Heat treatment method for amorphous magnetic alloy sheet
JPS63302504A (ja) * 1987-06-02 1988-12-09 Hitachi Metals Ltd 磁心およびその製造方法
JPH0219442A (ja) * 1988-07-07 1990-01-23 Nippon Steel Corp 超微細結晶組織を有する高飽和磁束密度Ｆｅ基合金
JP2002280224A (ja) * 2001-01-05 2002-09-27 Humanelecs Co Ltd アモルファス合金粉末コア及びナノクリスタル合金粉末コア並びにそれらの製造方法
JP2013055182A (ja) * 2011-09-02 2013-03-21 Nec Tokin Corp 軟磁性合金粉末、ナノ結晶軟磁性合金粉末、その製造方法、および圧粉磁心
JP2016145373A (ja) * 2015-02-06 2016-08-12 Ｎｅｃトーキン株式会社 Ｆｅ基ナノ結晶合金の製造方法

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPWO2023127199A1 (https=) * 2021-12-28 2023-07-06
JPWO2023127198A1 (https=) * 2021-12-28 2023-07-06
WO2023190770A1 (ja) * 2022-03-30 2023-10-05 株式会社プロテリアル 磁性シートの製造方法
DE102023122712A1 (de) * 2023-08-24 2025-02-27 Vacuumschmelze Gmbh & Co. Kg Gegenstand aus einer nanokristallinen weichmagnetischen Legierung und Verfahren zum Herstellen einer nanokristallinen weichmagnetischen Legierung
DE102023122712B4 (de) * 2023-08-24 2025-10-09 Vacuumschmelze Gmbh & Co. Kg Verfahren zum Herstellen einer nanokristallinen weichmagnetischen Legierung
JP2025065896A (ja) * 2023-10-10 2025-04-22 トヨタ自動車株式会社 軟磁性材料及びその製造方法
JP7765140B1 (ja) * 2025-07-02 2025-11-06 ネクストコアテクノロジーズ株式会社 鉄基軟磁性合金およびその製造方法

Also Published As

Publication number Publication date
JPWO2022264999A1 (https=) 2022-12-22

Similar Documents

Publication Publication Date Title
WO2022264999A1 (ja) ナノ結晶合金薄帯の製造方法、およびナノ結晶合金薄帯
JP6444504B2 (ja) 積層磁芯及びその製造方法
JP2698369B2 (ja) 低周波トランス用合金並びにこれを用いた低周波トランス
JP6669082B2 (ja) Ｆｅ基軟磁性合金薄帯およびそれを用いた磁心
JP6080094B2 (ja) 巻磁心およびこれを用いた磁性部品
JP6867744B2 (ja) Ｆｅ基ナノ結晶合金の製造方法
JP5656114B2 (ja) 超急冷Ｆｅ基軟磁性合金薄帯および磁心
MX2013001344A (es) Placa de acero magnetica direccional y metodo de produccion para la misma.
CN103097563A (zh) 方向性电磁钢板及其制造方法
JP6605182B2 (ja) アモルファス合金リボン及びその製造方法、アモルファス合金リボン片
TW200800440A (en) An amorphous alloy thin strip excellent in magnetic property and space factor
JP7683197B2 (ja) 軟磁性合金、軟磁性合金薄帯およびその製造方法、磁心、ならびに部品
TWI769275B (zh) 非晶質合金條帶及其製造方法
WO2019009311A1 (ja) 巻磁心及び巻磁心の製造方法
JP5206017B2 (ja) 高珪素鋼板の製造方法
JP2022523627A (ja) 鉄系合金
TWI733766B (zh) 疊層塊磁芯、疊層塊及疊層塊之製造方法
WO2022264998A1 (ja) ナノ結晶合金薄帯の製造方法、およびナノ結晶合金薄帯
JP7803097B2 (ja) 軟磁性合金薄帯およびその製造方法、磁心、ならびに部品
CN113053611A (zh) 软磁性合金、软磁性合金薄带及其制造方法、磁芯以及部件
JP7424549B1 (ja) ナノ結晶合金薄帯及び磁性シート
US20250129447A1 (en) Methodfor manufacturing nanocrystal alloy ribbon, and method for manufacturing magnetic sheet
EP4040453A1 (en) Soft magnetic alloy, soft magnetic alloy ribbon, method of manufacturing soft magnetic alloy ribbon, magnetic core, and component
CN118974288A (zh) 纳米晶合金薄带的制造方法及磁性片的制造方法

Legal Events

Date Code Title Description
ENP Entry into the national phase

Ref document number: 2022559370

Country of ref document: JP

Kind code of ref document: A

121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 22824987

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 22824987

Country of ref document: EP

Kind code of ref document: A1