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EP1320110B1 - Procédé de fabrication de noyaux toroidales nanocristallins - Google Patents

Procédé de fabrication de noyaux toroidales nanocristallins Download PDF

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Publication number
EP1320110B1
EP1320110B1 EP20020027302 EP02027302A EP1320110B1 EP 1320110 B1 EP1320110 B1 EP 1320110B1 EP 20020027302 EP20020027302 EP 20020027302 EP 02027302 A EP02027302 A EP 02027302A EP 1320110 B1 EP1320110 B1 EP 1320110B1
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EP
European Patent Office
Prior art keywords
strip
process according
amorphous
anisotropy
alloy structure
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.)
Expired - Lifetime
Application number
EP20020027302
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German (de)
English (en)
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EP1320110A1 (fr
Inventor
Wulf Dr. Günther
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.)
Vacuumschmelze GmbH and Co KG
Original Assignee
Vacuumschmelze GmbH and Co KG
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Filing date
Publication date
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Publication of EP1320110A1 publication Critical patent/EP1320110A1/fr
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Publication of EP1320110B1 publication Critical patent/EP1320110B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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Classifications

    • 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
    • H01F1/15341—Preparation processes therefor
    • 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
    • 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)
    • H01F41/0226—Manufacturing of magnetic circuits made from strip(s) or ribbon(s) from amorphous ribbons

Definitions

  • Nanocrystalline alloys are generally for example in the EP 0 271 657 B1 described. As a rule, these are iron-based alloys. However, other alloys are also conceivable.
  • the magnetic properties are essentially determined by the magnitude of the so-called anisotropy energy K, which is composed of several contributions, but typically only the magnetically-induced anisotropy energy K u is used for adjusting the magnetic properties in magnetic cores.
  • the size of the magnetically induced anisotropic energy K u limited to values less than 100 J / m 3 . Since it is additionally required for most applications that the magnetostriction ⁇ s is as low as possible, the attractive alloy regions are limited to inducible anisotropy energies in the range of less than 25 J / m 3 .
  • the minimum permeability of the magnetic cores is thus about 5000 or 18,000. It is usually achieved by a so-called heat treatment in a magnetic transverse field. This heat treatment is called cross-field annealing and the resulting BH loop has a so-called "F-shape".
  • Another way to induce magnetic anisotropy is to induce them via mechanical stress.
  • the so-called stress-induced magnetic anisotropies can achieve higher anisotropy energies in comparison to the magnetically induced anisotropies. These higher anisotropic energies, in turn, improve aging stability.
  • the object of the present invention is therefore to provide a process which can be realized on an industrial scale for the production of magnetic cores from nanocrystalline alloy strips which simultaneously have a low magnetostriction ⁇ s and a high voltage-induced anisotropy energy K u .
  • anisotropy incubator in the present patent application means are generally understood to act in concert with the first amorphous ribbon to create a mechanical strain in the first amorphous ribbon during the heat treatment which results in a permanent directional stress-induced anisotropy K u .
  • These may be a body or a material having a different crystallization temperature, a metallic band or a coating or a support body.
  • the different thermal expansion coefficients of the first amorphous ribbon and of the anisotropic incubator and / or the volume shrinkage of an amorphous ribbon in the nanocrystalline ion or a conventional crystallization are exploited.
  • either F or Z-shaped BH loops can be generated.
  • the magnetic cores are much more resistant to aging than the magnetic cores of the prior art, which in particular allows continuous use temperatures above 150 ° C.
  • the achievable stress-induced anisotropy K u is distributed homogeneously or inhomogeneously in the magnetic core.
  • magnetic cores can be produced with a linear BH loop or with a so-called "soft" junction into saturation.
  • the first amorphous ribbons are made of iron-based alloys, such as those mentioned in the introduction EP 0 271 657 B1 are known. However, in principle, other nanocrystalline alloy systems are conceivable.
  • a support body is used on which the first amorphous ribbon is wound.
  • a metallic sleeve is provided as a support body.
  • the first amorphous tape is then wound as tight as possible on this support body.
  • this band shrinks during the nanocrystallization on the support body.
  • the tape is pulled in the tape direction and pressed perpendicular to the tape surface on the support body.
  • both the support body and the nanocrystallizing first amorphous band expand.
  • the support body has a higher thermal expansion coefficient than the first amorphous belt. This increases the inducible tension.
  • a body made of metal for example a sleeve used of a non-magnetic material.
  • This metallic sleeve can also be used as part of the fixation of the material.
  • a ceramic body for example a sleeve or the like.
  • This can be alleviated by giving the first amorphous ribbon, through a smooth surface and / or a "lubricating film", at least in the first phase of shrinkage, an opportunity to more evenly distribute the tension by sliding the band layers.
  • lubricating film is a coating of magnesium methylate or other known insulation coatings into consideration.
  • a Z-shaped B-H loop or an F-shaped B-H loop is obtained.
  • Magnet cores with F-shaped B-H loops which have been produced by the process according to the invention, have a conspicuously low permeability, typically permeabilities less than 5000. They are extremely resistant to aging and almost magnetostriction-free, i. (
  • a thin film having a second coefficient of thermal expansion which is applied to the first amorphous ribbon before being wound into a magnetic core.
  • the coating can be either irregular, isotropic or anisotropic.
  • stresses also arise both transversely and longitudinally relative to the strip direction, so that an isotropic distribution of the light preferred directions in the strip plane is produced for larger widths of the first amorphous strip.
  • undefined B-H loop shapes can arise with high magnetization losses.
  • anisotropic-area coatings have proven to be preferred.
  • Anisotropic coatings can be done, for example, in line forms.
  • the thin layer acting as an anisotropy incubator is typically a metallic layer which is preferably electroplated onto the first amorphous ribbon.
  • other coating methods are also conceivable, in particular coatings via CVD or PVD methods.
  • a second band of metal having a second thermal expansion coefficient is used, wherein the first amorphous band and the second band of metal are bifilarly wound into a magnetic core.
  • the magnetic core thus wound is then subjected to the heat treatment used to produce the nanocrystalline alloy structure.
  • a crystalline band is provided as the second band of metal.
  • the difference in thermal expansion coefficients between the first amorphous ribbon on the one hand and the second ribbon of metal on the other hand is exploited here.
  • a second amorphous ribbon is used instead of a crystalline ribbon.
  • This second amorphous ribbon has a different (second) crystallization temperature from the first amorphous ribbon.
  • the first amorphous ribbon and the second amorphous ribbon are bifilarly wound into a magnetic core. Due to the different crystallization temperatures of the two amorphous ribbons and the associated different "shrinkage", in turn, mechanical stresses are generated between the two originally amorphous ribbons.
  • the result of the heat treatment initially depends on what volume fraction of the first crystallizing amorphous ribbon is already crystallized when the second amorphous ribbon begins to crystallize. As a result, the strain exerted on the two amorphous ribbons during the adjustment of induced anisotropy is controlled.
  • the setting parameters for this are the differences in the two crystallization temperatures, which in turn can be adjusted via the respective alloy compositions of the amorphous ribbons.
  • Another setting parameter is the local heating rate during the heat treatment.
  • the magnetostriction ⁇ s and, in turn, the composition of the two amorphous bands has a significant influence on the magnitude of the induced anisotropy K u .
  • the second amorphous band consists of an alloy which can be converted into a nanocrystalline alloy during the heat treatment.
  • the second amorphous band consists of an alloy which crystallizes out "normally", i. completely crystallized during the heat treatment. Examples of these are the amorphous cobalt-base alloys which are known from the prior art.
  • the nanocrystalline alloys are generally so brittle that the winding of nanocrystalline alloy strips into magnetic cores is very difficult to impossible.
  • a variant of the third embodiment of the method according to the invention would be possible in which a bifilar wound magnetic core is again "wrapped” and the “second wrapping” removes the second metallic strip.
  • the exposed nanocrystalline alloy ribbon can then be wound back into a magnetic core.
  • the alloys on which the exemplary embodiments are based were selected from the alloy system Fe a CO b CU c Si d B e M f K g , where M is at least one of the elements V, Nb, Ta, Ti, Mo, W, Zr and / or Hf and K is at least one of the elements C, P, Ge, As, Sb, In, O, N and the indices a, b, c, d, e, f, g are expressed in atomic percent and the following relationships apply:
  • amorphous strips having thicknesses of 12-40 ⁇ m and widths of 1 to 200 mm were cast by means of rapid solidification technology. To reduce the eddy current losses between the tape layers in the magnetic cores to be produced with each other, these first amorphous band were provided with layers of magnesium methylate.
  • An alloy having a composition Fe BAL- Cu 1 Nb 3 Si 15.5 B 7 was cast to a first amorphous ribbon.
  • the tape had a width of 25mm and was provided with a magnesium methylate coating.
  • This first amorphous ribbon was wound on a metal sleeve serving as a support body.
  • the metal sleeve had a diameter of 26mm and a winding height of 1mm was made.
  • the metal sleeve thus wound was then field-annealed at a temperature of about 550 ° C for one hour.
  • the resulting magnetic core had an F-shaped BH loop with a remanence ratio B r / B m of about 5%.
  • the anisotropy field strength achieved was 1200 A / m, which corresponded to a permeability of 800.
  • Comparative magnetic cores which were annealed without the voltage induction according to the invention in the magnetic transverse field, had only anisotropic field strengths of 50 A / m, which corresponds to permeabilities of about 20,000.
  • the magnetic properties at room temperature and temperatures of about 150 ° C were almost identical. Changes in the magnetic characteristics after a field-free aging of 14 days at 150 ° C, then 2 days at 200 ° C and again 2 hours at 220 ° C were undetectable. After another 10 days at 205 ° C and a DC magnetization of 200A / m, no changes were detectable. By contrast, the comparative magnetic cores were at temperatures above 140 ° changes in magnetic properties clearly detectable after only 10 days.
  • a first amorphous ribbon having the Fe BAL Cu 1 Nb 3 Si 15.5 B 7 alloy composition having a width of 4.4 mm and a thickness of 20 ⁇ m was isotropically electrodeposited on both sides with a gold layer about 2 ⁇ m thick.
  • the thus-coated first amorphous ribbon was wound into a magnetic core, and then annealed at 550 ° C for one hour without field soldering.
  • the quasi-static BH loop then showed a coercive field strength H c of 50mA / cm, a high remanent ratio and an untypically wide BH loop even at high modulation. This could be explained by a superimposition of Z and F components in the BH loop by relatively large induced anisotropy energies K u , whose preferential direction showed an isotropic distribution in the band plane.
  • a first amorphous ribbon having the alloy composition FC Bal Cu 1 Nb 3 Si 12.5 B 8 and a second amorphous ribbon having the alloy composition Fe BAL Cu 1 Nb 3 Si 16 B 7 were bifilarly wound into a magnetic core measuring 60 mm ⁇ 40 mm ⁇ 25 mm , The difference in crystallization temperatures between the two alloys was about 20K.
  • the bifilar wound magnetic core was field annealed at 550 ° C for 1 hour.
  • the heating rate was 1 K / min.
  • the magnetic core showed an F-shaped B-H loop having an anisotropy field strength of 120 A / m, which corresponded to a permeability of 8000.
  • the remanence ratio was 5% for the magnetic core thus obtained.
  • the magnetic core was subsequently "rewound", ie decomposed into the individual nanocrystallized strip components.
  • the first crystallized ribbon showed a Z-shaped B-H loop in the "wrapped" and thus relaxed state.
  • the influence of the magnetostriction ⁇ s could also be verified by an audible noise during excitation in the audible frequency range.
  • the initial permeability decreased from the initial permeability at room temperature by 15%. More commonly, comparative cores made by the prior art processes have a much higher permeability and a 30-50% initial permeability reduction at 140 ° C relative to the room temperature value.
  • a first amorphous ribbon having an alloy composition Fe BAL Cu 1 Nb 3 Si 15.5 B 7 having a thickness of about 20 ⁇ m and a second metallic ribbon made of aluminum and had a thickness of about 10 microns were bifilar wound into a magnetic core with the dimensions 50mm x 30mm x 15mm.
  • the thus wound magnetic core was then annealed field-free at a temperature of 550 ° C for 1 hour.
  • the resulting magnetic core had a relatively round BH loop with increased anisotropic field strength compared to reference cores without aluminum tape.
  • a first amorphous ribbon having the same composition as in the 4th embodiment was bifilarly wound with a second amorphous ribbon of a cobalt-based alloy into a magnetic core having a dimension of approximately 50mm x 30mm x 15mm. Both amorphous ribbons had thicknesses of about 20 ⁇ m.
  • the resulting magnetic core was also annealed field-free at 550 ° C for 1 hour. The resulting magnetic core then had an F-shaped B-H loop due to the fact that the cobalt-based alloy used crystallized before the nanocrystalline iron-based alloy.
  • magnetic cores having Z-shaped BH loops were obtained which had coercive forces H c of 35mA / cm and remanence ratios of B r / B m of almost 99% at frequencies of 1 Hertz.
  • filling factors can be present in the magnetic cores, which lie in the range between 40% and 95%.
  • the reversal magnetization losses of the magnetic cores obtainable in the method according to the invention are 2-20 times the losses according to the classical eddy current theory. In unipolar operation, the magnetic reversal losses are 1.3-10 times the losses according to the classical eddy current theory. If the anisotropic incubator is removed, for example, by "wrapping", magnetic cores with an F-loop will be subject to magnetization losses according to the classical eddy current theory
  • the magnetic cores produced according to the invention have very small magnetostrictions, typically magnetostrictions
  • the magnetic cores according to the invention have a low dependence of the magnetic characteristics on the temperature, are very resistant to aging and have a high continuous temperature load capacity. Depending on the modulation and design, continuous temperature capacities are possible, which are well above 150 ° C.

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  • Engineering & Computer Science (AREA)
  • Power Engineering (AREA)
  • Chemical & Material Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Electromagnetism (AREA)
  • Dispersion Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Inorganic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Manufacturing & Machinery (AREA)
  • Soft Magnetic Materials (AREA)
  • Manufacturing Cores, Coils, And Magnets (AREA)

Claims (13)

  1. Procédé de fabrication d'un noyau magnétique à partir d'un alliage de base à aimantation douce, au moins 50 % de la structure de l'alliage étant occupés par des particules de cristaux fins ayant une dimension moyenne de particules de 100 nanomètres ou moins,
    procédé comprenant les étapes suivantes :
    a) on fournit une première bande amorphe à partir d'un bain de fusion d'alliage à base de fer par une technologie de figeage rapide, la bande amorphe ayant un premier coefficient de dilatation thermique et une première température de cristallisation,
    b) on fournit un incubateur anisotrope,
    c) on enroule la première bande amorphe pour former un noyau magnétique en utilisant l'incubateur anisotrope,
    d) on effectue un traitement thermique sans champ magnétique du noyau magnétique enroulé, la structure d'alliage amorphe étant transformée en une structure d'alliage, et au moins 50 % de la structure d'alliage est occupée par des particules de cristaux fins ayant une dimension moyenne de particules de 100 nanomètres ou moins (structure d'alliage nanocristallin), et
    à l'aide de l'incubateur anisotrope, on génère une seconde mise en tension mécanique périodique ou permanente dans le noyau magnétique qui conduit à une anisotropie Ku magnétique induite, permanente, dirigée.
  2. Procédé selon la revendication 1,
    selon lequel
    comme incubateur anisotrope, on utilise un organe d'appui sur lequel est enroulée la première bande amorphe.
  3. Procédé selon la revendication 2,
    selon lequel
    on utilise un organe de support en métal ou en céramique.
  4. Procédé selon la revendication 1,
    selon lequel
    on utilise comme incubateur anisotrope, une mince couche ayant un second coefficient de dilatation thermique, cette couche étant appliquée sur la première bande amorphe avant d'enrouler la première bande amorphe pour former un noyau magnétique.
  5. Procédé selon la revendication 4,
    selon lequel
    on applique la couche mince anisotrope sur le premier ruban amorphe.
  6. Procédé selon la revendication 4 ou 5,
    selon lequel
    on utilise une couche métallique, comme couche mince.
  7. Procédé selon les revendications 4 à 6,
    selon lequel
    on utilise une couche d'or, d'argent, de cuivre ou d'aluminium, comme couche métallique.
  8. Procédé selon la revendication 6,
    selon lequel
    la couche métallique est galvanisée sur la première bande amorphe.
  9. Procédé selon la revendication 1,
    selon lequel
    comme incubateur anisotrope, on utilise une seconde bande en métal ayant un second coefficient de dilatation thermique, et la première bande amorphe et la seconde bande sont constituées de métal bifilaire enroulé pour former un noyau magnétique.
  10. Procédé selon la revendication 9,
    selon lequel
    comme seconde bande, on utilise une bande cristalline.
  11. Procédé selon la revendication 9,
    selon lequel
    comme seconde bande, on utilise une bande amorphe ayant une seconde température de cristallisation.
  12. Procédé selon la revendication 11,
    selon lequel
    la structure d'alliage de la seconde bande amorphe est mise sous la forme d'une structure d'alliage durant le traitement thermique et au moins 50 % de la structure d'alliage est constituée par les particules de cristaux fins ayant une dimension moyenne de particules de 100 nanomètres ou moins.
  13. Procédé selon les revendications 9 à 12, comprenant les étapes supplémentaires suivantes :
    e) enroulement du noyau magnétique avec des enroulements bifilaires,
    f) enlèvement de la seconde bande du métal, et
    g) nouvel enroulement de la première bande à nanocristaux pour former un noyau magnétique.
EP20020027302 2001-12-17 2002-12-06 Procédé de fabrication de noyaux toroidales nanocristallins Expired - Lifetime EP1320110B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE10161907 2001-12-17
DE2001161907 DE10161907A1 (de) 2001-12-17 2001-12-17 Verfahren zur Herstellung nanokristalliner Ringbandkerne

Publications (2)

Publication Number Publication Date
EP1320110A1 EP1320110A1 (fr) 2003-06-18
EP1320110B1 true EP1320110B1 (fr) 2008-11-12

Family

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Family Applications (1)

Application Number Title Priority Date Filing Date
EP20020027302 Expired - Lifetime EP1320110B1 (fr) 2001-12-17 2002-12-06 Procédé de fabrication de noyaux toroidales nanocristallins

Country Status (2)

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EP (1) EP1320110B1 (fr)
DE (2) DE10161907A1 (fr)

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102015107294A1 (de) * 2015-05-11 2016-11-17 Technische Hochschule Köln Spulenanordnung für Spannungsregler
DE102015211487B4 (de) 2015-06-22 2018-09-20 Vacuumschmelze Gmbh & Co. Kg Verfahren zur herstellung eines nanokristallinen magnetkerns
CN114959213A (zh) * 2022-04-13 2022-08-30 宁波中科毕普拉斯新材料科技有限公司 一种高频低损耗铁基纳米晶磁芯的热处理方法

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4413406A (en) * 1981-03-19 1983-11-08 General Electric Company Processing amorphous metal into packets by bonding with low melting point material
JPS57186306A (en) * 1981-05-11 1982-11-16 Hitachi Ltd Magnetic core and manufacture thereof
JPS58131724A (ja) * 1982-01-30 1983-08-05 Matsushita Electric Works Ltd 磁心の製法
JP2975142B2 (ja) * 1991-03-29 1999-11-10 株式会社日立製作所 アモルファス鉄心製造方法及びその装置
JP2000277357A (ja) * 1999-03-23 2000-10-06 Hitachi Metals Ltd 可飽和磁心ならびにそれを用いた電源装置

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EP1320110A1 (fr) 2003-06-18
DE10161907A1 (de) 2003-06-26
DE50213003D1 (de) 2008-12-24

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