EP0389511A1 - SINTERMAGNET AUF BASIS VON Fe-Nd-B - Google Patents

SINTERMAGNET AUF BASIS VON Fe-Nd-B

Info

Publication number
EP0389511A1
EP0389511A1 EP19880909531 EP88909531A EP0389511A1 EP 0389511 A1 EP0389511 A1 EP 0389511A1 EP 19880909531 EP19880909531 EP 19880909531 EP 88909531 A EP88909531 A EP 88909531A EP 0389511 A1 EP0389511 A1 EP 0389511A1
Authority
EP
European Patent Office
Prior art keywords
weight
oxygen
added
oxide
magnet
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.)
Withdrawn
Application number
EP19880909531
Other languages
German (de)
English (en)
French (fr)
Inventor
Friedrich J. Esper
Waldemar Draxler
Günter Petzow
Andreas BÜCHEL
Klaus-Dieter Durst
Ernst-Theo Henig
Gerhard Schneider
Helmut KRONMÜLLER
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.)
Robert Bosch GmbH
Max Planck Gesellschaft zur Foerderung der Wissenschaften eV
Original Assignee
Robert Bosch GmbH
Max Planck Gesellschaft zur Foerderung der Wissenschaften eV
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 Robert Bosch GmbH, Max Planck Gesellschaft zur Foerderung der Wissenschaften eV filed Critical Robert Bosch GmbH
Publication of EP0389511A1 publication Critical patent/EP0389511A1/de
Withdrawn legal-status Critical Current

Links

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
    • H01F1/032—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
    • H01F1/047—Alloys characterised by their composition
    • H01F1/053—Alloys characterised by their composition containing rare earth metals
    • H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
    • H01F1/057—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B
    • H01F1/0571—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes
    • H01F1/0575—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together
    • H01F1/0577—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together sintered
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/001—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides
    • C22C32/0015—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides with only single oxides as main non-metallic constituents
    • C22C32/0026—Matrix based on Ni, Co, Cr or alloys thereof

Definitions

  • Sintered magnets of the Fe-Nd-B type are characterized by particularly high magnetic properties at room temperature: However, their temperature resistance - mainly the coercive force H CJ - is unsatisfactory and prevents the use of the magnets in temperature-stressed machines.
  • the magnets For technical applications it is therefore necessary to improve the magnets to such an extent that they can be used at up to 200 ° C with strong opposing fields.
  • the coercive field strength of the magnet in particular must be further improved and the temperature dependence of the coercive field strength reduced in order to ensure sufficient values at higher temperatures.
  • Dy and Tb as expensive, heavy RE metals have a favorable influence on the crystal anisotropy of the Fe 14 Nd 2 B phase and thus also on the coercive force.
  • Nb causes precipitations in the Fe 14 Nd 2 B grains, which are said to act as obstacles to the movement of the domain wall.
  • the cause of Al's influence on H CJ has not yet been fully elucidated.
  • the object of the invention is therefore to improve the coercive field strength in sintered magnets of the Fe-Nd-B type and to reduce the temperature dependency thereof without having to add heavy RE metals such as Dy and Tb.
  • a sintered magnet based on Fe-Nd-B which is characterized in that it consists of 25 to 50% by weight of Nd, 0.5 to 2% by weight of B, 0 to 5% by weight.
  • -% AI, 0.5 to 3 wt .-% O, rest Fe and usual impurities and the oxygen content is adjusted by adding at least one Al and / or Nd oxide before the dense sintering.
  • Fig .; 4 is a graphical representation corresponding to FIG. 1 for a base alloy and Nd203 additive.
  • Sintered magnets based on Fe-Nd-B normally contain small amounts of oxygen as an impurity, depending on the manufacturing process.
  • the oxygen content of the Fe-Nd-B master alloys usually produced as intermediates for the production of the sintered magnets is usually about 0.02% by weight. Grinding the master alloys can result in a further increase in the oxygen content if this is not carefully excluded by maintaining an inert atmosphere. Oxygen levels up to about 0.25% by weight can occur in this way.
  • This oxygen accumulates in later liquid phase sintering in the liquid, Nd-rich phase and can lead to the formation of new phases when it solidifies.
  • the invention is based on the knowledge that these phases can be influenced by the targeted addition of oxygen in the form of an Al or Nd oxide, in particular Al 2 O 3 or / and Nd 2 O 3 , that the desired improvement in Properties, as explained above, is achieved.
  • the oxides are expediently added to the master alloy Fe-Nd-B before or during grinding, preferably already in powder form.
  • the average particle size of Al 2 O 3 added is preferably 0.5 to 0.05 ⁇ m.
  • Nd 2 O 3 is expediently finely ground first in the attritor and then added to the present alloy for further grinding. In this way, a particularly uniform distribution of the oxide grains in the powder mixture is achieved.
  • the sintered magnet contains 48 to 60% by weight of Fe, 38 to 50% by weight of Nd, 0.9 to 1.1% by weight of B and 0.1 to 2% by weight of Al 2 O 3 .
  • Compositions of the type mentioned which are obtained with master alloys whose Nd content is between 18.5 and 25 atom% and the B content is 6.0 to 7.0 atom% are particularly preferred. This enables the H to be increased by 40 to 60% depending on the Nd content of the master alloy compared to the corresponding values without the addition of Al oxide.
  • the increase in the coercive field strength and its temperature resistance through the addition of Al 2 O 3 is more pronounced the higher the Nd content.
  • the sintered magnet contains 2 to 6.5% Nd 2 O 3 .
  • FIG. 4 shows that starting from a master alloy Fe 75 Nd 18.5 B 6, the addition of Nd 2 O 3 results in an increase in H CJ in the range from 2 to 6.5% by weight, which is up to 15% , if the Nd 2 O 3 content exceeds the specified upper limit, the non-magnetic phase components increase.
  • the sintered magnets according to the invention are produced by a modification of the known production method.
  • This consists of melting the pure components together to form a master alloy, pulverizing the master alloy, aligning the powder in a magnetic field and compressing the powder so aligned to a green formation, sintering the molding at a temperature between 1040 to 1100 ° C and then tempering at 600 up to 700 ° C.
  • a composition of 25 to 50% by weight of Nd, 0.5 to 2% by weight of B, 0.5 to 3% by weight of 0.0 to 5% by weight.
  • -% AI, rest Fe and usual impurities used wherein at least part of the oxygen is added in the form of an Al and / or Nd oxide and mixed in homogeneously before the green body is produced.
  • the addition is preferably 0.1 to 2% Al 2 O 3 or 2 to 6.5% Nd 2 O 3 . Mixtures of these oxides can also be used.
  • the Al or / and Nd oxide preferably in the finely powdered form, is generally added to the powdered master alloy and ground with it in order to achieve the most homogeneous possible distribution.
  • the values shown in the figures were obtained with magnets produced in this way, which were ground for 30 minutes, sintered at 1060 ° C. for 1 hour and then tempered at 600 ° C. for 1 hour.
  • the same improvements in magnetic properties are achieved if, alternatively, Al and / or Nd oxide is added during melting of the master alloy or the oxygen is added via the grinding and / or sintering atmosphere.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Inorganic Chemistry (AREA)
  • Power Engineering (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Hard Magnetic Materials (AREA)
EP19880909531 1987-11-26 1988-10-28 SINTERMAGNET AUF BASIS VON Fe-Nd-B Withdrawn EP0389511A1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE19873740157 DE3740157A1 (de) 1987-11-26 1987-11-26 Sintermagnet auf basis von fe-nd-b
DE3740157 1987-11-26

Publications (1)

Publication Number Publication Date
EP0389511A1 true EP0389511A1 (de) 1990-10-03

Family

ID=6341366

Family Applications (1)

Application Number Title Priority Date Filing Date
EP19880909531 Withdrawn EP0389511A1 (de) 1987-11-26 1988-10-28 SINTERMAGNET AUF BASIS VON Fe-Nd-B

Country Status (5)

Country Link
US (1) US5194099A (ja)
EP (1) EP0389511A1 (ja)
JP (1) JPH03501189A (ja)
DE (1) DE3740157A1 (ja)
WO (1) WO1989005031A1 (ja)

Families Citing this family (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1989012113A1 (en) * 1988-06-03 1989-12-14 Mitsubishi Metal Corporation SINTERED RARE EARTH ELEMENT-B-Fe-MAGNET AND PROCESS FOR ITS PRODUCTION
US5478411A (en) * 1990-12-21 1995-12-26 Provost, Fellows And Scholars Of The College Of The Holy And Undivided Trinity Of Queen Elizabeth Near Dublin Magnetic materials and processes for their production
JPH11307327A (ja) * 1998-04-22 1999-11-05 Sanei Kasei Kk 永久磁石用組成物
JP2001123201A (ja) 1999-08-17 2001-05-08 Sanei Kasei Kk 焼結永久磁石の製造方法
DE19945942C2 (de) * 1999-09-24 2003-07-17 Vacuumschmelze Gmbh Verfahren zur Herstellung von Dauermagneten aus einer borarmen Nd-Fe-B-Legierung
DE60131699T2 (de) * 2000-06-13 2008-11-20 Shin-Etsu Chemical Co., Ltd. Dauermagnetmaterialien auf R-Fe-B-Basis
US6648984B2 (en) * 2000-09-28 2003-11-18 Sumitomo Special Metals Co., Ltd. Rare earth magnet and method for manufacturing the same
JP5437544B2 (ja) * 2001-06-11 2014-03-12 株式会社三徳 二次電池用負極の製造法
US20050062572A1 (en) * 2003-09-22 2005-03-24 General Electric Company Permanent magnet alloy for medical imaging system and method of making
CN1898757B (zh) * 2004-10-19 2010-05-05 信越化学工业株式会社 稀土永磁材料的制备方法
TWI413136B (zh) * 2005-03-23 2013-10-21 Shinetsu Chemical Co 稀土族永久磁體
MY141999A (en) * 2005-03-23 2010-08-16 Shinetsu Chemical Co Functionally graded rare earth permanent magnet
TWI417906B (zh) * 2005-03-23 2013-12-01 Shinetsu Chemical Co 機能分級式稀土族永久磁鐵
TWI364765B (en) * 2005-03-23 2012-05-21 Shinetsu Chemical Co Rare earth permanent magnet
US7955443B2 (en) * 2006-04-14 2011-06-07 Shin-Etsu Chemical Co., Ltd. Method for preparing rare earth permanent magnet material
JP4656323B2 (ja) * 2006-04-14 2011-03-23 信越化学工業株式会社 希土類永久磁石材料の製造方法
JP4840606B2 (ja) 2006-11-17 2011-12-21 信越化学工業株式会社 希土類永久磁石の製造方法

Family Cites Families (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CA1316375C (en) * 1982-08-21 1993-04-20 Masato Sagawa Magnetic materials and permanent magnets
US4601875A (en) * 1983-05-25 1986-07-22 Sumitomo Special Metals Co., Ltd. Process for producing magnetic materials
EP0153744B1 (en) * 1984-02-28 1990-01-03 Sumitomo Special Metals Co., Ltd. Process for producing permanent magnets
JPS61245505A (ja) * 1985-04-23 1986-10-31 Seiko Instr & Electronics Ltd 希土類鉄系磁石の製造方法
JPH0685369B2 (ja) * 1985-05-17 1994-10-26 日立金属株式会社 永久磁石の製造方法
US4588439A (en) * 1985-05-20 1986-05-13 Crucible Materials Corporation Oxygen containing permanent magnet alloy
US4762574A (en) * 1985-06-14 1988-08-09 Union Oil Company Of California Rare earth-iron-boron premanent magnets
JPS62134907A (ja) * 1985-12-09 1987-06-18 Hitachi Metals Ltd Ｒ−Ｂ−Ｆｅ系焼結磁石およびその製造方法
US4954186A (en) * 1986-05-30 1990-09-04 Union Oil Company Of California Rear earth-iron-boron permanent magnets containing aluminum
CA1336866C (en) * 1986-08-04 1995-09-05 Setsuo Fujimura Rare earth magnet having excellent corrosion resistance
DE3637521A1 (de) * 1986-11-04 1988-05-11 Schramberg Magnetfab Permanentmagnet und verfahren zu seiner herstellung
US4834812A (en) * 1987-11-02 1989-05-30 Union Oil Company Of California Method for producing polymer-bonded magnets from rare earth-iron-boron compositions
JPH06260207A (ja) * 1993-03-02 1994-09-16 Fuji Electric Co Ltd 燐酸形燃料電池のスタック

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See references of WO8905031A1 *

Also Published As

Publication number Publication date
WO1989005031A1 (en) 1989-06-01
JPH03501189A (ja) 1991-03-14
DE3740157A1 (de) 1989-06-08
US5194099A (en) 1993-03-16

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