EP0575190B1 - Alliage magnétiquement doux à base de fer et procédé de fabrication - Google Patents

Alliage magnétiquement doux à base de fer et procédé de fabrication Download PDF

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Publication number
EP0575190B1
EP0575190B1 EP93304762A EP93304762A EP0575190B1 EP 0575190 B1 EP0575190 B1 EP 0575190B1 EP 93304762 A EP93304762 A EP 93304762A EP 93304762 A EP93304762 A EP 93304762A EP 0575190 B1 EP0575190 B1 EP 0575190B1
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Prior art keywords
alloy
soft magnetic
atomic
magnetic
present
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German (de)
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EP0575190A2 (fr
EP0575190A3 (fr
Inventor
Hiroshi c/o Mitsui Petrochem. Ind. Ltd. Watanabe
Yoshihiko c/o Mitsui Petrochem. Ind. Ltd. Hirota
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Mitsui Petrochemical Industries Ltd
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    • 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
    • H01F1/032—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 hard-magnetic materials
    • H01F1/04—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 hard-magnetic materials metals or alloys
    • 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

Definitions

  • the present invention relates to an Fe-based soft magnetic alloy and, in particular, to an alloy having excellent soft magnetic properties and a process for making it.
  • Fe-based amorphous magnetic alloys having a high saturation magnetic flux density are known to be used as magnetic core materials for magnetic heads, high frequency transformers, saturable reactors, choke coils, etc.
  • Fe-based amorphous magnetic alloys are lower priced than Co-based ones, the former have the drawbacks of large core loss in the high frequency region and low permeability.
  • it's saturation magnetostriction is high.
  • An Fe-B system alloy is known as a conventional Fe-system amorphous magnetic alloy.
  • the alloys including B (boron) are highly priced because the element B is expensive.
  • One object of the present invention is to provide a novel Fe-based soft magnetic alloy, which can be substituted for the above-mentioned conventional soft magnetic materials and has a low saturation magnetostriction and a low iron loss.
  • Another object of the present invention is to provide an Fe-based soft magnetic alloy which is lower priced.
  • an Fe-based soft magnetic alloy which has a composition represented by the formula: Fe 100-a-b-c-d P a M b M' c Cu d where M is at least one element selected from the group consisting of Zr, Hf, Nb, Mo, W, Ta, Ti, V, Cr, Mn, Y and Ce;
  • P phosphorous
  • a determined amount of P enables the extension of the range of formation of amorphous alloys after quenching without using an expensive element B (boron). Thereby, the cost of preparation of the alloy can be reduced.
  • the content (a) of P is more than 0 atomic % and not more than 25 atomic %, preferably from 1 to 15 atomic %, more preferably from 2 to 12 atomic %.
  • the element(s) M added to the Fe-based soft magnetic alloy of the present invention is supposed to prevent crystallization of the Fe-P system crystal which hampers the soft magnetic properties of the alloy or to elevate its crystallization temperature.
  • M is at least one, i.e. one or more of the elements selected from the group consisting of Zr, Hf, Nb, Mo, W, Ta, Ti, V, Cr, Mn, Y and Ce. Particularly Zr is preferable. Addition of the element(s) M is further effective for making the crystal grain fine and for improving the ability of forming the amorphous phase of the alloy in the Fe-P system alloy.
  • the content (b) of the M element(s) is more than 0 atomic % and not more than 15 atomic %, preferably from 2 to 15 atomic %, more preferably from 3 to 12 atomic %.
  • the element(s) M' added to the Fe-based soft magnetic alloy of the pr-esent invention is one or more of the elements selected from the group consisting of Si, Al, Ga, Ge, Ru, Co, Ni,Sn, Sb and Pd. It is considered that these elements are dissolved in the Fe-based solid solution because they have a negative interaction parameter relative to Fe, that is, it is considered that the elements are described as being substituted for Fe atom in the ⁇ -Fe crystalline structure whereby stabilizing the bcc crystal. Thus, it is considered that the crystalline grain having a genuine magnetocrystalline anisotropy of bcc crystalline or low magnetostriction constant is formed to exhibit excellent soft magnetic properties.
  • the content (c) of the M' element(s) is from 0 atomic % to 20 atomic %, preferably from 1 to 15 atomic %.
  • Cu (copper) in the alloy of the present invention is effective for making the crystalline particles obtained by the heat-treatment of the amorphous fine. Further, it improves the magnetic properties of the alloy since the effective magnetic anisotropy energy becomes smaller than its genuine magnetocrystalline anisotropy energy as the particles become fine.
  • the copper content should not be more than 5 atomic % with respect to the preparation of the alloy because the just quenched alloy tends to be brittle. Accordingly, the content (d) of Cu is from 0 to 5 atomic %, preferably from 0.5 to 3 atomic %.
  • alloy further containing inevitable impurities such as N, S, O etc., to the extent that these elements do not deteriorate the properties of the alloy, is also included in the scope of the present invention .
  • the Fe-based soft magnetic alloy according to the present invention has an alloy structure, at least 30 % (30 % - 100 %) of which consists of (is composed of) fine crystalline particles, with the balance of the structure being an amorphous phase or other crystals than above-mentioned fine crystalline particles.
  • the range of the ratio of the fine crystalline particles in the structure provides the alloy with excellent (soft) magnetic properties.
  • the alloy retains sufficiently good magnetic properties.
  • at least 50 %, more preferably 70 % or more of the alloy structure consists of (is composed of) the fine crystalline particles in view of magnetic properties.
  • the crystalline particles of the alloy of the present invention has mainly a bcc structure and it is considered that Fe is the main component in which M, M' and a small amount of P are believed to be dissolved.
  • the crystalline particles to be formed in the alloy of the present invention have a particle size of 1000 ⁇ or less, preferably 500 ⁇ or less, more preferably 50 to 300 ⁇ .
  • the particle size being 1000 ⁇ or less, preferably 500 ⁇ or less, more preferably 50 to 300 ⁇ , provides the alloy of the present invention having excellent magnetic properties.
  • Preferred Fe-based soft magnetic alloys of the present invention have a saturation magnetostriction ( ⁇ S) in the range of +10x10 -6 to -5x10 -6 .
  • the proportion of the crystalline grains to the total alloy structure in the alloy of the present invention may be determined experimentally by an X-ray diffraction method or the like. Briefly, on the basis of the standard value of the X-ray diffraction intensity of Fe-based crystal in the completely crystallized condition (saturated X-ray diffraction intensity condition), the proportion of the X-ray diffraction intensity of the magnetic alloy material sample to be examined to the standard value may be obtained experimentally.
  • the Fe-based soft magnetic alloy of the present invention may be produced by a heat-treatment of an amorphous metal having a determined shape which is obtained by a common method of forming an amorphous metal.
  • an amorphous alloy is first formed in the form of a ribbon, powder, fiber, or thin film by a melt quenching method such as a single roll method or double roll method, a thin film forming method such as a cavitation method, sputtering method or vapor deposition method, or a powder forming method such as mechanical alloying or the like.
  • the resulting amorphous alloy is optionally shaped and worked into a desired shape, then it is heat-treated so that at least a part, preferably 30 % or more of the whole, of the sample is crystallized to obtain the alloy of the present invention.
  • the structure of the alloy after rapid-quenching is preferably amorphous but it may include partial crystalization to the extent that the resulting alloy exhibits soft magnetic properties after heat-treatment.
  • a quenched alloy ribbon is formed by a single roll method, and this is shaped into a determined shape such as a coiled magnetic core and then heat-treated.
  • the heat-treatment is effected in vacuum, in an inert gas atmosphere, such as an argon gas or nitrogen gas atmosphere, in a reducing gas atmosphere such as H 2 or in an oxidizing gas atmosphere such as air.
  • the heat-treatment temperature is approximately from 200 to 800°C, preferably approximately from 300 to 700°C, preferably from 350 to 700°C and more preferably from 400 to 700 °C.
  • the heat-treatment time is within 24 hours, preferably about from 0.5 to 5 hours.
  • the heat-treatment may be effected either in the absence or presence of a magnetic field. Impressing of a magnetic field brings a magnetic anisotropy to the alloy.
  • Fig. 1 is a graph showing X-ray diffraction patterns of the Fe-base soft magnetic alloy of the present invention after heat-treatment.
  • a quenched ribbon (thin film) sample having a width of about 1.5 mm and a thickness of about 15-24 ⁇ m was formed from a melt containing Fe, P, Zr, and (Cu) in an argon gas atmosphere of one atmosphere pressure by a single roll method.
  • the sample was then heat-treated at the temperature shown by Table 1 for about one hour in the presence of a nitrogen gas and in the absence of a magnetic field.
  • the iron loss (Pc W/kg) of each of the samples was determined under the condition of a frequency of 100 kHz and a maximum magnetic flux density of 0.1 T.
  • the permeability ( ⁇ ) (1KHz) under the condition of a frequency of 1 kHz and a maximum exciting magnetic field of 5 mOe, the saturation magnetization Ms (emu/g) and the saturation magnetostriction constant ⁇ s ( ⁇ 10 -6 ) of each samples were also determined.
  • the composition of the alloy samples, the content of the fine crystalline particles in the alloy and the average particle size are shown in Table 1 below.
  • the content of the fine crystalline particles is 60 % or more in all of the samples.
  • the composition of the alloy was determined by IPC analysis.
  • Fig. 1 shows the X-ray diffraction curves of the alloy of Fe 88 Zr 9 P 2 Cu 1 (atomic %)(Example 3) obtained by heat-treating the quenched alloy formed by a single roll method, at 620 °C in the presense of argon for one hour.
  • the structure of the alloy obtained by heat-treatment has mainly bcc structure.
  • the Fe-based soft magnetic alloy of the present invention shows an excellent magnetic properties such as low ion loss, high permeability and low saturation magnetostriction by adding specific element(s), particularly Zr together with Cu to Fe-P system alloy. Accordingly, the alloy of the present invention can be utilized widely for a magnetic head, high-frequency transformers, saturable reactors, choke coils and like as the magnetic material substitited for the Fe-B system soft magnetic alloy.
  • the Fe-based soft magnetic alloy of the present invention can be prepared at a reduced cost since it utilizes phosphorous P instead of boron B.

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  • Engineering & Computer Science (AREA)
  • Chemical & Material Sciences (AREA)
  • Power Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Electromagnetism (AREA)
  • Dispersion Chemistry (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Soft Magnetic Materials (AREA)
  • Powder Metallurgy (AREA)

Claims (9)

  1. Alliage magnétique doux à base de fer, qui présente une composition répondant à la formule : Fe (100-a-b-c-d) P a M b M' c Cu d
    Figure imgb0005
     dans laquelle M représente au moins un élément choisi parmi Zr, Hf, Nb, Mo, W, Ta, Ti, V, Cr, Mn, Y et Ce ; M' représente au moins un élément choisi parmi Si, Al, Ga, Ge, Ru, Co, Ni, Sn, Sb et Pd ; a, b, c et d représentent chacun un pourcentage atomique et satisfont aux relations 0 < a ≤ 25, 0 < b ≤ 15, 0 ≤ c ≤ 20 et 0 ≤ d ≤ 5.
  2. Alliage conforme à la revendication 1, dans lequel au moins 30 % de la structure d'alliage est occupée par des particules fines cristallines.
  3. Alliage conforme à la revendication 2, dans lequel les particules cristallines se trouvent dans une solution solide de structure cubique centrée (cc) comprenant principalement du fer.
  4. Alliage conforme à l'une quelconque des revendications 1 à 3, dans lequel la taille moyenne des particules ne dépasse pas 100 nm.
  5. Alliage conforme à l'une quelconque des revendications 1 à 4, dans lequel le coefficient de magnétostriction à saturation (λs) de l'alliage est comprise entre +10 x 10-6 et -5 x 10-6.
  6. Procédé de fabrication d'un alliage magnétique doux à base de fer, comprenant :
    la mise en forme d'un alliage trempé qui présente une composition répondant à la formule : Fe (100-a-b-c-d )P a M b M' c Cu d
    Figure imgb0006
     dans laquelle M représente au moins un élément choisi parmi Zr, Hf, Nb, Mo, W, Ta, Ti, V, Cr, Mn, Y et Ce ; M' représente au moins un élément choisi parmi Si, Al, Ga, Ge, Ru, Co, Ni, Sn, Sb et Pd ; a, b, c et d représentent chacun un pourcentage atomique et satisfont chacun aux relations 0 < a ≤ 25, 0 < b ≤ 15, 0 ≤ c ≤ 20 et 0 ≤ d ≤ 5,
    par un procédé de trempe à l'état fondu, un procédé de mise sous forme de film mince ou un procédé de mise sous forme de poudre, et le traitement thermique de l'alliage trempé.
  7. Procédé conforme à la revendication 6, dans lequel l'alliage trempé est maintenu à une température comprise entre 350° C et 700° C pendant moins de 24 heures au cours du traitement thermique.
  8. Procédé conforme à la revendication 6 ou 7 pour produire un alliage conforme à l'une quelconque des revendications 2 à 5.
  9. Noyau magnétique constitué d'un alliage conforme à l'une quelconque des revendications 1 à 5, ou produit selon la revendication 6 ou 7.
EP93304762A 1992-06-17 1993-06-17 Alliage magnétiquement doux à base de fer et procédé de fabrication Expired - Lifetime EP0575190B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP158338/92 1992-06-17
JP15833892A JP3623970B2 (ja) 1992-06-17 1992-06-17 Ｆｅ基軟磁性合金および製造方法

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EP0575190A2 EP0575190A2 (fr) 1993-12-22
EP0575190A3 EP0575190A3 (fr) 1994-01-26
EP0575190B1 true EP0575190B1 (fr) 1997-09-17

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EP (1) EP0575190B1 (fr)
JP (1) JP3623970B2 (fr)
KR (1) KR0131376B1 (fr)
CA (1) CA2098532A1 (fr)
DE (1) DE69313938T2 (fr)

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE4444482A1 (de) * 1994-12-14 1996-06-27 Bosch Gmbh Robert Weichmagnetischer Werkstoff
KR100916602B1 (ko) * 2002-11-11 2009-09-11 엘지디스플레이 주식회사 소다라임 글라스를 이용한 액정표시장치와 그 제조방법
CN102360670B (zh) * 2011-10-24 2014-01-08 南京信息工程大学 一种铁氧体磁层非晶软磁芯复合材料及其制备方法
CN104962821B (zh) * 2015-05-26 2017-03-22 北京科技大学 一种针式打印机轭铁座零件的加工方法
JP7106919B2 (ja) * 2018-03-23 2022-07-27 Tdk株式会社 軟磁性薄膜、薄膜インダクタおよび磁性製品
CN110998918B (zh) 2018-04-10 2022-12-06 株式会社Lg新能源 制备磷化铁的方法、包含磷化铁的锂二次电池用正极和包含所述正极的锂二次电池
WO2019198949A1 (fr) * 2018-04-10 2019-10-17 주식회사 엘지화학 Procédé de production de phosphure de fer, électrode positive pour batterie secondaire au lithium comprenant du phosphure de fer, et batterie secondaire au lithium la comprenant
KR102229460B1 (ko) * 2018-04-10 2021-03-18 주식회사 엘지화학 인화철(FeP)의 제조방법
DE102019105215A1 (de) * 2019-03-01 2020-09-03 Vacuumschmelze Gmbh & Co. Kg Legierung und Verfahren zur Herstellung eines Magnetkerns
KR20220038899A (ko) * 2020-09-21 2022-03-29 엘지전자 주식회사 합금 분말 및 이의 제조방법
CN112176222B (zh) * 2020-10-30 2021-12-17 东北大学 一种含Ce的Fe-Ni坡莫合金材料及其制备方法

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2713711B2 (ja) * 1987-11-17 1998-02-16 日立金属株式会社 防犯センサ用マーカ
JPH04272159A (ja) * 1991-01-08 1992-09-28 Sumitomo Metal Ind Ltd Ｆｅ基磁性合金

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Publication number Publication date
JP3623970B2 (ja) 2005-02-23
JPH062076A (ja) 1994-01-11
CA2098532A1 (fr) 1993-12-18
EP0575190A2 (fr) 1993-12-22
EP0575190A3 (fr) 1994-01-26
KR0131376B1 (ko) 1998-04-24
KR940006157A (ko) 1994-03-23
DE69313938D1 (de) 1997-10-23
DE69313938T2 (de) 1998-03-05

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