CN106971799B - Hard magnetic phase, preparation method thereof and magnetic material - Google Patents
Hard magnetic phase, preparation method thereof and magnetic material Download PDFInfo
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- 239000000696 magnetic material Substances 0.000 title claims description 19
- 238000002360 preparation method Methods 0.000 title claims description 3
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 6
- 229910052742 iron Inorganic materials 0.000 claims abstract description 4
- 238000000034 method Methods 0.000 claims description 16
- 238000000227 grinding Methods 0.000 claims description 8
- 239000000843 powder Substances 0.000 claims description 7
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- 239000000203 mixture Substances 0.000 abstract description 14
- 229910052723 transition metal Inorganic materials 0.000 abstract description 12
- 150000003624 transition metals Chemical class 0.000 abstract description 12
- 229910052802 copper Inorganic materials 0.000 abstract description 3
- 229910052748 manganese Inorganic materials 0.000 abstract description 3
- 229910052759 nickel Inorganic materials 0.000 abstract description 3
- 239000000126 substance Substances 0.000 abstract description 3
- 229910052721 tungsten Inorganic materials 0.000 abstract description 3
- 229910052782 aluminium Inorganic materials 0.000 abstract description 2
- 229910052804 chromium Inorganic materials 0.000 abstract description 2
- 229910052733 gallium Inorganic materials 0.000 abstract description 2
- 229910052735 hafnium Inorganic materials 0.000 abstract description 2
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 2
- 229910052758 niobium Inorganic materials 0.000 abstract description 2
- 229910052698 phosphorus Inorganic materials 0.000 abstract description 2
- 229910052710 silicon Inorganic materials 0.000 abstract description 2
- 229910052715 tantalum Inorganic materials 0.000 abstract description 2
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- 238000010438 heat treatment Methods 0.000 description 14
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- 239000002994 raw material Substances 0.000 description 9
- 239000010936 titanium Substances 0.000 description 6
- 229910052720 vanadium Inorganic materials 0.000 description 6
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- 239000000463 material Substances 0.000 description 5
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- -1 Ti and W Chemical class 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
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- 229910017052 cobalt Inorganic materials 0.000 description 1
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- 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
- H01F1/0551—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 in the form of particles, e.g. rapid quenched powders or ribbon flakes
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- 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
- H01F1/0555—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 pressed, sintered or bonded together
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- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- 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
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- H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
- H01F1/0555—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 pressed, sintered or bonded together
- H01F1/0556—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 pressed, sintered or bonded together pressed
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
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- 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
- H01F1/059—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and Va elements, e.g. Sm2Fe17N2
- H01F1/0593—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and Va elements, e.g. Sm2Fe17N2 of tetragonal ThMn12-structure
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- 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
- H01F1/059—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and Va elements, e.g. Sm2Fe17N2
- H01F1/0596—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and Va elements, e.g. Sm2Fe17N2 of rhombic or rhombohedral Th2Zn17 structure or hexagonal Th2Ni17 structure
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Abstract
The invention relates to a hard magnetic phase, which is characterized by the following chemical formula: (Ce)1‑xSmx)aTMbVcAdWherein TM is at least one transition metal selected from Fe, Co, Ni, Mn and mixtures thereof, a is at least one element selected from W, Ti, Mo, Cr, Nb, Ta, Hf, Al, Si, Ga, Cu, Zr, Sn, Zn and P, wherein 0 < x < 1, a =2-20 at%, b =60-85 at%, c =0.5-15 at% and d =0.5-15 at%, and a + b + c + d =100 at%.
Description
Technical Field
The present invention relates to a hard magnetic phase and a magnetic material having improved magnetic properties. Furthermore, the invention relates to a method for producing the hard magnetic phase and to the use thereof, and also to an electromechanical machine using the hard magnetic phase according to the invention or the magnetic material according to the invention.
Background
The demand for highly efficient magnetic materials, in particular permanent magnets, has increased considerably in recent years due to the recent increase in the use of electric motors, in particular in the field of automobile construction. The new high-efficiency magnets are made of intermetallic rare earth-transition metal-compounds such as Nd-Fe and their inclusion in Nd2Fe14B forms and is characterized by high coercivity, large coercive field (koezitvfeld), and high energy product. The disadvantage of magnetic materials based on high concentrations of rare earth metals is their high raw material costs and their limited availability in the market.
Disclosure of Invention
In contrast, the hard-magnetic phase of the invention according to claim 1 is characterized by excellent magnetic properties and thus high coercivity, large coercive field strength, and furthermore by a high energy product. The specific composition of the hard-magnetic phase, defined by the following formula, also allows the hard-magnetic phase of the present invention to have a lower material cost with good raw material availability:
(Ce1-xSmx)aTMbVcAd
in the above formula, Ce represents cerium, Sm represents samarium and TM is at least one transition metal, where mixtures of transition metals may also be present. The transition metal TM is selected from: iron (Fe), cobalt (Co), nickel (Ni), manganese (Mn) and mixtures thereof. The transition metals mentioned here form a very stable lattice structure with the remaining constituents of the hard-magnetic phase according to the invention and are very particularly advantageous for the formation of the desired advantageous magnetic properties, i.e. in particular for the saturation and the magnetic anisotropy of the material according to the invention. Furthermore, the transition metals defined here are characterized by high availability on the market and low raw material costs, which further significantly reduces the material costs and/or the production costs of the hard magnetic phase according to the invention.
V represents the element vanadium and A represents at least one element selected from the group consisting of W, Ti, Mo, Cr, Nb, Ta, Hf, Al, Si, Ga, Cu, Zr, Sn, Zn and P. The chemical composition of the hard magnetic phase of the invention can be determined by means of roentgen structural analysis and elemental analysis. A high proportion of transition metals and a high proportion of element a result of the proportions of the elements, i.e. 0 < x < 1, a =2-20 atomic%, b =60-85 atomic%, c =0.5-15 atomic% and d =0.5-15 atomic%, and a + b + c + d =100 atomic%, thus maintaining a moderate proportion of cerium and samarium. The combination of cerium metal and samarium has a decisive influence on the magnetic properties of the hard magnetic phase, which is characterized by a suitable cost-effectiveness compared with the commonly used rare earth metals. This significantly reduces the raw material cost of the hard magnetic phase of the present invention. The elements samarium and cerium may be substituted for each other. The high proportion of transition metal and of element a also contributes to a reduction in the raw material costs. In addition to other transition metals such as Ti and W, the element vanadium also stabilizes the structure of the hard magnetic phase and leads to an improved coercive field strength compared to other stabilizing elements. Due to its specific composition, the hard magnetic phase of the invention has excellent mechanical, magnetic and thermal stability, which makes it particularly suitable for use under strong stress, i.e. for example in mobile devices such as cars and portable electronic instruments. Thus, by using the hard magnetic phase of the invention, a plurality of application possibilities are opened even in low-priced products without the product quality being impaired.
The dependent claims show preferred embodiments of the invention.
According to an advantageous embodiment of the hard-magnetic phase according to the invention, the transition metal TM is preferably iron (Fe). The preference for Fe is due to its health and ecological safety and, in addition, to its again significant reduction in raw material costs compared to Co, Ni and Mn.
According to a further advantageous embodiment of the hard-magnetic phase according to the invention, (Ce)1-xSmx) Is advantageously selected such that a = 5-15 atomic%, in particular 7-9 atomic%, based on the total composition of the hard magnetic phase. (Ce) in the given preferred amount1-xSmx) Resulting in a magnetically efficient hard magnetic phase with lower raw material costs.
For reasons of reducing the price of the hard-magnetic phase according to the invention and in view of a high saturation polarization, a proportion of the transition metal TM which is as high as possible is particularly advantageous. In view of optimizing mechanical, chemical and magnetic properties with a maximum reduction in raw material costs, it is advantageous for the proportion of TM to be 70 to 80 atomic%, in particular 72 to 77 atomic% (equivalent to b = 70 to 80 atomic%, in particular 72 to 77 atomic%), based on the total composition of the hard magnetic phase.
It is furthermore advantageous if the proportion of vanadium is from 5 to 10 at.%, more preferably from 6 to 9 at.%, which corresponds to c = 5 to 10 at.%, in particular from 6 to 9 at.%. Mixing V in this concentration range results in a significant improvement in coercive field strength.
By means of this advantageous embodiment, the proportion of the element or elements a is selected such that d = 5-10 at.%, in particular 6-9 at.%, based on the total composition of the hard-magnetic phase, the magnetic properties can be modulated very efficiently. This can improve the structure of the magnetic material (Gef ü ge), for example. Mixing a in this concentration range results in a significant improvement in coercive field strength.
In a further advantageous embodimentCharacterized in that the structure of the magnetic material is selected from: ThMn12Structure, Th2Zn17-structure or Nd3(Fe, Ti)29-a structure. The structures mentioned here are particularly advantageous for forming the anisotropic phase of the hard magnetic phase of the invention. This is due to its favorable electronic structure and configuration, as well as the spin and orbit moments of the atom.
Magnetic materials comprising the aforementioned hard magnetic phases are also described. The magnetic material is not limited individually, and may be, for example, a permanent magnet or a magnet bonded via plastic. Due to the specific composition of the hard magnetic phase, the magnetic material of the invention also has very good magnetic properties and thus has a high energy product, a large coercive field and a high coercivity. Furthermore, due to the use of Ce — Sm, transition metals TM, vanadium and additive elements a, the raw material costs and thus the manufacturing costs of the magnetic material of the invention are kept at a low level with good availability.
Furthermore, the present invention also provides a first method for preparing the aforementioned hard magnetic phase. The inventive method is characterized by the steps of i) mixing and melting the elements of the hard magnetic phase to obtain a cast structure (Gussgefuge), and ii) sintering the powder produced from the obtained cast structure or melt-spinning the obtained cast structure or strongly grinding the obtained cast structure. This results in a homogeneous metal structure which is characterized by a high coercivity, a large coercive field strength and a high energy product. The method can be easily changed without high technical expenditure.
The sintering step can be carried out in particular as follows: the molten cast structure (casting alloy) is first heat treated at a temperature of 500-1500 deg.C, preferably 700-1100 deg.C, for a period of 10 minutes up to 2 weeks, preferably 1 hour up to 25 hours. The complete formation of the hard magnetic phase is favoured by a heat treatment, preferably carried out under vacuum or under a protective gas atmosphere, in particular under argon. After grinding to an average particle size of 1-10 μm, pressing while powder orientation in a magnetic field (particle orientation creates anisotropy of the magnet, which is necessary for high coercivity and high energy product), and sintering at 1000-. The desired good hard magnetic properties are produced by sintering. Followed by another heat treatment or additional heat treatments at 400-900 deg.c, whereby the advantageous hard magnetic properties can be improved again.
The melt spinning can be carried out in particular as follows: the resulting cast structure (molten cast alloy) is first melted in a crucible with a nozzle by means of induction melting. The liquid melt is then extruded onto a rapidly rotating copper wheel. The material is rapidly condensed into a band of average thickness of 20-70 μm. The tape pieces have a nanocrystalline structure with an average particle size of 15-50 nm. Thereby producing the desired superior hard magnetic properties. Followed by heat treatment at 400-900 deg.C or more, whereby the superior hard magnetic characteristics can be improved again. The resulting hard magnetic phase is then ground to the desired particle size. The resulting powder can then be processed into bonded magnets (gebundenen magnets) or further processed into thermoformed magnets. To prepare a thermoformed magnet, the hard magnetic phase is hot-pressed to almost its theoretical density and then thermoformed.
The intensive grinding includes in particular high-energy grinding of the resulting cast structure to obtain an amorphous or nanocrystalline structure. The desired good hard magnetic properties are produced by one or more subsequent heat treatments at 700-1000 c to form the hard magnetic phase. The microstructure and magnetic properties can be optimized by performing one or more heat treatments at 400-900 ℃. The advantageous hard magnetic properties are improved once more by this heat treatment. Furthermore, there are also a number of possibilities for further processing of the resulting magnetic material into bonded magnets or into thermoformed magnets by means of hot pressing to almost the theoretical density of the hard magnetic phase and subsequent thermoforming.
An advantageous embodiment of the process according to the invention provides that the melting is carried out in an arc furnace or in an induction furnace under vacuum or under a protective gas, preferably argon. This procedure ensures that all elements are completely fused without causing oxidation of the material, so that a uniform crystal structure of the hard-magnetic phase is formed in the subsequent heat treatment step, which not only has a favorable effect on the mechanical stability of the formed hard-magnetic phase, but also has a large influence on the desired magnetic properties.
According to another advantageous embodiment of the method according to the invention, the obtained hard magnetic phase is ground and/or nitrided after the heat treatment carried out after melting or in the subsequent step. This is particularly suitable for preparing the hard magnetic phase by sintering or intensive milling. The grinding of the hard magnetic phase facilitates its further processability, for example into plastic-bonded magnets. The magnetic properties of the hard magnetic phase, in particular its anisotropy, can be improved by nitriding. It is particularly advantageous to carry out the final grinding of the resulting mixture first, followed by a nitriding treatment, since in this way a homogeneous nitriding even up to the finest crystal grains can be obtained, thereby improving the magnetic properties of the hard magnetic phase particularly effectively.
Likewise, a second method for preparing the aforementioned hard magnetic phase is also described. This second method is characterized by the step of mechanically alloying.
Mechanical alloying in particular comprises powders of alloys of hard-or hard-magnetic phase elements mixed in a desired final composition, which powder mixture is high-energy milled to obtain an amorphous or nanocrystalline composition and subjected to one or more heat treatments at 700-1000 ℃ to form the hard-magnetic phase, thereby giving good hard-magnetic properties. Multiple heat treatments at 400-900 ℃ may follow to optimize the microstructure and magnetic properties, thereby again improving good hard magnetic properties. Subsequently, there are also two options here as described for melt spinning and power grinding, namely processing into bonded magnets or further processing into thermoformed magnets by means of hot pressing to almost the theoretical density of the hard magnetic phase and subsequent thermoforming.
By means of the second method of the invention, a hard-magnetic phase with a homogeneous metal structure is likewise obtained, which is characterized by a high coercivity, a large coercive field strength and a high energy product. Furthermore, the method allows a simple conversion without high technical effort.
The advantageous properties, effects and embodiments described for the hard-magnetic phase according to the invention also apply to the method according to the invention for producing such a hard-magnetic phase.
The invention also discloses the use of the above-mentioned hard magnetic phase, preferably in wind power installations, PKW, NKW, starting devices, motors, loudspeakers and microelectromechanical systems. The use of the inventive hard-magnetic phase in the device is particularly advantageous because of its outstanding magnetic properties and its excellent stability and thus its suitability for space-saving construction.
The invention also discloses an electric machine, in particular a generator, a car, a starting device, a motor, a loudspeaker or a micro-electromechanical system, comprising the hard magnetic phase of the invention or a magnetic material prepared therefrom. The advantages, advantageous effects and preferred embodiments described for the hard magnetic phase according to the invention and the method according to the invention also apply for the electromechanical machine according to the invention.
Drawings
Embodiments of the present invention are described in detail below with reference to the accompanying drawings. In the drawings:
fig. 1 shows a diagram for illustrating the effect of heat treatment on the hard magnetic phase.
Examples
FIG. 1 shows a diagram in detail, in which the coercive field strength H is for different hard magnetic phasesc(kA/m) is plotted against time. The following two different hard phases are measured in principle:
one is as follows:
- MA3：Ce4.4Sm4.2Fe83.6Ti7.8which is shown in phantom in the figure, and
the other is as follows:
- MA12：Ce4.8Sm4.1Fe75.0Ti8.0V8.1which is shown in solid lines in the figure.
MA3 is a prior art hard magnetic phase. The hard magnetic phase is vanadium free. MA12 is a hard magnetic phase according to a preferred embodiment of the present invention. The hard magnetic phase contains cerium, samarium, vanadium, iron as transition elements and titanium as element A. For each hard magnetic phase, 4 curves were plotted. These hard magnetic phases are produced by mechanical alloying of elemental powders and subsequent heat treatment at 700-. FIG. 1 shows that the hard magnetic phase of the invention is in place compared to a correspondingly treated hard magnetic phase according to the prior artHigher H is obtained at the temperature in the whole time of the heat treatmentcThe value is obtained.
The foregoing description of the invention is provided for the purpose of illustration only and is not intended to be limiting. Various changes and modifications may be made within the scope of the present invention without departing from the scope of the invention and its equivalents.
Claims (11)
1. A hard magnetic phase characterized by the following formula:
(Ce1-xSmx)aTMbVcAd
wherein TM is Fe, a is Ti, wherein 0 < x < 1, a = 7-9 atomic%, b = 72-77 atomic%, c = 6-9 atomic% and d = 6-9 atomic%, and a + b + c + d =100 atomic%.
2. A hard magnetic phase according to claim 1, characterized by the following formula: ce4.8Sm4.1Fe75.0Ti8.0V8.1。
3. A magnetic material comprising a hard magnetic phase according to claim 1 or 2.
4. The magnetic material of claim 3, wherein the magnetic material has a structure selected from the group consisting of: ThMn12Structure, Th2Zn17-structure or Nd3(Fe, Ti)29-a structure.
5. Method for preparing a hard magnetic phase according to claim 1 or 2, characterized by the following steps:
-mixing and melting the elements of the hard magnetic phase to obtain a cast structure, and
-sintering a powder made from the obtained cast structure or melt spinning or power grinding the obtained cast structure.
6. The method according to claim 5, wherein the melting is carried out in an electric arc furnace or in an induction furnace under vacuum or protective gas.
7. A method according to claim 5 or 6, characterized in that the resulting hard magnetic phase is ground and/or nitrided in a further step.
8. Process for the preparation of hard magnetic phases according to claim 1 or 2, characterized by a step of mechanical alloying.
9. Use of a hard magnetic phase according to claim 1 or 2 or a magnetic material according to claim 3 or 4 in generators, wind power installations, PKW, NKW, starting installations, motors, loudspeakers and micro-electro-mechanical systems.
10. An electrical machine comprising a hard magnetic phase according to claim 1 or 2 or comprising at least one magnetic material according to claim 3 or 4.
11. The electrical machine of claim 10, which is a generator, an automobile, a starting device, a motor, a loudspeaker, or a microelectromechanical system.
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| DE102015218560.5 | 2015-09-28 | ||
| DE102015218560.5A DE102015218560A1 (en) | 2015-09-28 | 2015-09-28 | Hard magnetic phase, process for its preparation and magnetic material |
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| CN107601439B (en) * | 2017-08-22 | 2020-01-07 | 山西师范大学 | MnTe nanowire and preparation method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06172937A (en) * | 1992-10-05 | 1994-06-21 | Tokin Corp | Permanent magnet material |
| JPH06283316A (en) * | 1992-10-29 | 1994-10-07 | Hitachi Metals Ltd | Iron-rare earth permanent magnet material and its manufacture |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CH603802A5 (en) | 1975-12-02 | 1978-08-31 | Bbc Brown Boveri & Cie | |
| JPS5810454B2 (en) | 1980-02-07 | 1983-02-25 | 住友特殊金属株式会社 | permanent magnet alloy |
| US5041171A (en) * | 1986-07-18 | 1991-08-20 | U.S. Philips Corporation | Hard magnetic material |
| JP3312908B2 (en) * | 1990-08-15 | 2002-08-12 | 日立金属株式会社 | Iron-rare earth-nitrogen permanent magnet material |
| JPH0570900A (en) * | 1991-09-17 | 1993-03-23 | Tokin Corp | Magnetic material |
| JPH0620813A (en) * | 1992-05-08 | 1994-01-28 | Inter Metallics Kk | Rare earth anisotropic permanent magnet powder and manufacture thereof |
| JP3792737B2 (en) * | 1994-09-16 | 2006-07-05 | 株式会社東芝 | Magnet material and permanent magnet using the same |
| JP4481949B2 (en) | 2006-03-27 | 2010-06-16 | 株式会社東芝 | Magnetic material for magnetic refrigeration |
| JP5053195B2 (en) * | 2008-07-18 | 2012-10-17 | 株式会社タムラ製作所 | Powder magnetic core and manufacturing method thereof |
| DE102011108173A1 (en) * | 2011-07-20 | 2013-01-24 | Aichi Steel Corporation | Magnetic material and process for its production |
| JP5586645B2 (en) | 2012-03-15 | 2014-09-10 | 株式会社東芝 | Permanent magnet and motor and generator using the same |
| DE102012207308A1 (en) * | 2012-05-02 | 2013-11-07 | Robert Bosch Gmbh | Magnetic material, its use and process for its preparation |
-
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- 2015-09-28 DE DE102015218560.5A patent/DE102015218560A1/en not_active Withdrawn
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Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06172937A (en) * | 1992-10-05 | 1994-06-21 | Tokin Corp | Permanent magnet material |
| JPH06283316A (en) * | 1992-10-29 | 1994-10-07 | Hitachi Metals Ltd | Iron-rare earth permanent magnet material and its manufacture |
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| DE102015218560A1 (en) | 2017-03-30 |
| JP2017108110A (en) | 2017-06-15 |
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