Patent Application
20160189836
The present invention relates to Fe16N2 single phase particles having a large BHmax which can be produced for a short period of time, and a process for producing the Fe16N2 single phase particles. Also, in the present invention, there is provided an anisotropic magnet or bonded magnet produced using the Fe16N2 single phase particles.
At present, various magnetic materials such as Sr-based ferrite magnetic particles and Nd—Fe—B-based magnetic particles have been practically used. However, for the purpose of further enhancing properties of these materials, various improvements have been conducted, and in addition, various attempts have also been conducted to develop novel materials. Among the above materials, Fe—N-based compounds such as Fe16N2 have been noticed.
Among the Fe—N-based compounds, α″-Fe16N2 is known as a metastable compound crystallized when subjecting a martensite or ferrite in which nitrogen is incorporated in the form of a solid solution to annealing for a long period of time. The α″-Fe16N2 has a “bct” crystal structure, and therefore it is expected that the α″-Fe16N2 provides a giant magnetic substance having a large saturation magnetization. However, as recognized from the wording “metastable compound”, there have been reported only very few cases where the compounds are successfully chemically synthesized in the form of isolated particles.
Hitherto, in order to obtain an α″-Fe16N2 single phase, various methods such as a deposition method, an MBE method (molecular beam epitaxy method), an ion implantation method, a sputtering method and an ammonia nitridation method have been attempted. However, production of more stabilized γ′-Fe4N or ε′-Fe2-3N is accompanied with an eutectic crystal of martensite (α′-Fe)-like metal or ferrite (α-Fe)-like metal, which tends to cause difficulty in producing the α″-Fe16N2 single phase compound in an isolated state. In some cases, it has been reported that the α″-Fe16N2 single phase compound is produced in the form of a thin film. However, the α″-Fe16N2 single phase compound in the form of such a thin film may be applied to magnetic materials only by a limited range, and tends to be unsuitable for use in still more extensive application fields.
The following known techniques concerning the α″-Fe16N2 have been proposed.
Patent Document 1: Japanese Patent Application Laid-Open (KOKAI) No. 11-340023
Patent Document 2: Japanese Patent Application Laid-Open (KOKAI) No. 2000-277311
Patent Document 3: Japanese Patent Application Laid-Open (KOKAI) No. 2009-84115
Patent Document 4: Japanese Patent Application Laid-Open (KOKAI) No. 2008-108943
Patent Document 5: Japanese Patent Application Laid-Open (KOKAI) No. 2008-103510
Patent Document 6: Japanese Patent Application Laid-Open (KOKAI) No. 2007-335592
Patent Document 7: Japanese Patent Application Laid-Open (KOKAI) No. 2007-258427
Patent Document 8: Japanese Patent Application Laid-Open (KOKAI) No. 2007-134614
Patent Document 9: Japanese Patent Application Laid-Open (KOKAI) No. 2007-36027
Patent Document 10: Japanese Patent Application Laid-Open (KOKAI) No. 2006-319349
Non-Patent Document 1: M. Takahashi, H. Shoji, H. Takahashi, H. Nashi, T. Wakiyama, M. Doi and M. Matsui, “J. Appl. Phys.”, Vol. 76, pp. 6642-6647, 1994.
Non-Patent Document 2: Y. Takahashi, M. Katou, H. Shoji and M. Takahashi, “J. Magn. Magn. Mater.”, Vol. 232, pp. 18-26, 2001.
However, the techniques described in the above Patent Documents 1 to 10 and Non-Patent Documents 1 and 2 have still failed to improve properties of the magnetic materials to a sufficient extent.
That is, in Patent Document 1, it is described that iron particles on which a surface oxide film is present are subjected to reducing treatment and then to nitridation treatment to obtain Fe16N2. However, in the Patent Document 1, it is not taken into consideration to enhance a maximum energy product of the material. In addition, the nitridation treatment requires a prolonged time, thereby failing to provide an industrially suitable process.
Also, in Patent Document 2, it is described that iron oxide particles are subjected to reducing treatment to produce metallic iron particles, and the resulting metallic iron particles are subjected to nitridation treatment to obtain Fe16N2. However, in Patent Document 2, the iron particles are used as magnetic particles for magnetic recording media and therefore tend to be unsuitable as a hard magnetic material having a maximum energy product as high as not less than 5 MGOe as required for a magnet material.
Also, in Patent Documents 3 to 9, there are described maximum magnetic substances for magnetic recording media which can be used instead of ferrite. However, these magnetic substances are obtained in the form of not an α″-Fe16N2 single phase but a mixed phase of still stabler γ′-Fe4N or ε′-Fe2-3N, and martensite (α′-Fe)-like metal or ferrite (α-Fe)-like metal.
Also, in Patent Document 10, it is described that the α″-Fe16N2 single phase has been successfully produced. However, in Patent Document 10, the α″-Fe16N2 single phase is produced only under the limited conditions for a prolonged period of time, i.e., at a temperature of 110 to 120° C. for 10 days. Therefore, the production method is not suitable for mass-production of the material. Further, the α″-Fe16N2 single phase obtained in Patent Document 10 has failed to exhibit a maximum energy product BHmax as high as not less than 5 MGOe as required for a magnet material.
In Non-Patent Documents 1 and 2, there is such a scientifically interesting report that the α″-Fe16N2 single phase has been successfully produced in the form of a thin film. However, the α″-Fe16N2 single phase in the form of such a thin film is usable in only limited applications, and therefore unsuitable for use in more extensive applications. Further, the α″-Fe16N2 single phase has problems concerning productivity and economy when obtaining a generally used magnetic material therefrom.
In consequence, an object of the present invention is to provide Fe16N2 single phase particles having a BHmax value as high as not less than 5 MGOe as required for a magnet material and a process for producing the particles, and an anisotropic magnet and a bonded magnet using the particles.
The above object can be achieved by the following aspects of the present invention.
That is, according to the present invention, there are provided ferromagnetic particles comprising an Fe16N2 single phase and having a BHmax value of not less than 5 MGOe (Invention 1).
Also, according to the present invention, there are provided ferromagnetic particles as described in the above Invention 1, further comprising an Si compound and/or an Al compound with which a surface of the respective Fe16N2 particles is coated (Invention 2).
Also, according to the present invention, there are provided ferromagnetic particles as described in the above Invention 1 or 2, wherein the ferromagnetic particles have a saturation magnetization value σs of not less than 130 emu/g and a coercive force Hc of not less than 1800 Oe (Invention 3).
Also, according to the present invention, there are provided ferromagnetic particles as described in any one of the above Inventions 1 to 3, wherein the ferromagnetic particles comprise primary particles having an average minor axis diameter of 5 to 40 nm and an average major axis diameter of 30 to 250 nm (Invention 4).
Also, according to the present invention, there are provided ferromagnetic particles as described in any one of the above Inventions 1 to 4, wherein the ferromagnetic particles have a BET specific surface area of 80 to 250 m2/g (Invention 5).
In addition, according to the present invention, there is provided a process for producing the ferromagnetic particles as described in any one of the above Inventions 1 to 5, comprising the step of subjecting iron compound particles to reducing treatment and then to nitridation treatment, wherein the iron compound particles used as a starting material are in the form of iron oxide or iron oxyhydroxide which comprises primary particles having an average minor axis diameter of 5 to 40 nm and an average major axis diameter of 30 to 200 nm, and has a BET specific surface area of 85 to 230 m2/g (Invention 6).
Also, according to the present invention, there is provided the process for producing the ferromagnetic particles as described in the above Invention 6, wherein a surface of the respective iron compound particles is coated with an Si compound and/or an Al compound, and then the resulting coated particles are subjected to the reducing treatment (Invention 7).
Also, according to the present invention, there is provided the process for producing the ferromagnetic particles as described in the above Invention 6 or 7, wherein a total treatment time of the reducing treatment and the nitridation treatment is not more than 36 hr (Invention 8).
Further, according to the present invention, there is provided an anisotropic magnet comprising the ferromagnetic particles as described in any one of the above Inventions 1 to 5 (Invention 9).
Furthermore, according to the present invention, there is provided a bonded magnet comprising the ferromagnetic particles as described in any one of the above Inventions 1 to 5 (Invention 10).
The ferromagnetic particles according to the present invention have a large BHmax value and therefore can be suitably used as a magnetic material.
Further, in the process for producing the ferromagnetic particles according to the present invention, the Fe16N2 particles having a large BHmax value can be readily obtained, and therefor the production process is suitable as a process for producing ferromagnetic particles.
The ferromagnetic particles according to the present invention comprise an Fe16N2 single phase. When the other crystal phases are present in the ferromagnetic particles, the resulting ferromagnetic particles may fail to exhibit sufficient magnetic properties.
The ferromagnetic particles according to the present invention have a maximum energy product BHmax of not less than 5 MGOe. When the maximum energy product BHmax of the ferromagnetic particles is less than 5 MGOe, the ferromagnetic particles may fail to exhibit sufficient magnetic properties required for hard magnetic materials such as magnet materials. The maximum energy product BHmax of the ferromagnetic particles is preferably not less than 6.0 MGOe, and more preferably 6.5 MGOe.
The ferromagnetic particles according to the present invention have a saturation magnetization value σs of not less than 130 emu/g and a coercive force Hc of not less than 1800 Oe. When the magnetization value σs and the coercive force Hc of the ferromagnetic particles are respectively out of the above-specified ranges, the resulting ferromagnetic particles may fail to exhibit sufficient magnetic properties required for hard magnetic materials such as magnet materials. The magnetization value σs of the ferromagnetic particles is preferably not less than 135 emu/g, and the coercive force Hc of the ferromagnetic particles is preferably not less than 2000 Oe and more preferably not less than 2200 Oe.
The primary particles of the ferromagnetic particles according to the present invention preferably have an average minor axis diameter of 5 to 40 nm and an average major axis diameter of 5 to 250 nm. When the average minor axis diameter and the average major axis diameter of the primary particles are respectively out of the above-specified ranges, it may be difficult to obtain the Fe16N2 single phase particles. The primary particles of the ferromagnetic particles preferably have an average minor axis diameter of 7 to 38 nm and an average major axis diameter of 7 to 220 nm, and more preferably an average minor axis diameter of 8 to 35 nm and an average major axis diameter of 8 to 200 nm.
The ferromagnetic particles according to the present invention preferably have a specific surface area of 80 to 250 m2/g. When the specific surface area of the ferromagnetic particles is less than 80 m2/g, the nitridation of the particles tends to hardly proceed, so that it may be difficult to obtain Fe16N2 particles in the form of a single phase. When the specific surface area of the ferromagnetic particles is more than 250 m2/g, the nitridation of the particles tends to be caused excessively, so that it may also be difficult to obtain Fe16N2 particles in the form of a single phase. The specific surface area of the ferromagnetic particles is more preferably 82 to 245 m2/g, and still more preferably 85 to 240 m2/g.
In the present invention, the respective ferromagnetic particles may be coated with an Si compound and/or an Al compound. When being coated with the Si compound and/or the Al compound, the temperatures used upon the heat treatments (including the reducing treatment and nitridation treatment) can be lowered, so that the particles can be prevented from suffering from excessive local nitridation. When being coated with the Si compound and/or the Al compound, it is preferred that the Si compound and/or the Al compound be respectively present in an amount of not more than 20000 ppm in terms of Si and/or Al. When the coating amounts of the Si compound and/or the Al compound are respectively more than 20000 ppm, the non-magnetic components in the particles tend to be undesirably increased. The coating amounts of the Si compound and/or the Al compound are respectively more preferably 1000 to 15000 ppm and still more preferably 1500 to 13000 ppm.
Next, the process for producing the ferromagnetic particles according to the present invention is described.
The ferromagnetic particles according to the present invention may be obtained by subjecting iron compound particles to reducing treatment and then to nitridation treatment, if required, after coating the surface of the respective iron compound particles with an Si compound and/or an Al compound.
The shape of iron oxide particles or iron oxyhydroxide particles as a starting material is not particularly limited, and may be of any shape such as an acicular shape, a granular shape, a spindle shape, a plate shape, a spherical shape, a cubic shape and a rectangular shape.
As the iron compound particles as the starting material, there may be used iron oxide or iron oxyhydroxide. Examples of the iron oxide or iron oxyhydroxide include magnetite, γ-Fe2O3, α-Fe2O3, α-FeOOH, β-FeOOH and γ-FeOOH, although not particularly limited thereto. The starting material may be in the form of a single phase, or may comprise impurities. As the impurities, the starting material may comprise iron oxide or iron oxyhydroxide other than those in a main phase thereof.
The primary particles of the iron compound particles as the starting material have an average minor axis diameter of 5 to 40 nm and an average major axis diameter of 5 to 200 nm. When the average minor axis diameter of the primary particles is less than 5 nm and/or when the average major axis diameter of the primary particles is less than 5 nm, the nitridation tends to excessively proceed, thereby failing to obtain Fe16N2 in the form of a single phase. When the average minor axis diameter of the primary particles is more than 40 nm and/or when the average major axis diameter of the primary particles is more than 200 nm, the nitridation tends to hardly proceed, thereby failing to obtain Fe16N2 in the form of a single phase. The primary particles of the iron compound particles preferably have an average minor axis diameter of 7 to 38 nm and an average major axis diameter of 7 to 190 nm, and more preferably an average minor axis diameter of 8 to 35 nm and an average major axis diameter of 8 to 185 nm.
The specific surface area of the iron oxide or iron oxyhydroxide used as the iron compound particles as the starting material is 85 to 230 m2/g. When the specific surface area of the iron oxide or iron oxyhydroxide is less than 85 m2/g, the nitridation tends to hardly proceed, thereby failing to obtain Fe16N2 in the form of a single phase. When the specific surface area of the iron oxide or iron oxyhydroxide is more than 230 m2/g, the nitridation tends to excessively proceed, thereby failing to obtain Fe16N2 in the form of a single phase. The specific surface area of the iron oxide or iron oxyhydroxide is preferably 90 to 220 m2/g and more preferably 95 to 210 m2/g.
The contents of impurity elements such as Al, Mn and Si in the iron compound particles as the starting material are preferably as small as possible. When these different kinds of elements are present in a large amount in the iron compound particles, the resulting ferromagnetic particles may fail to exhibit suitable magnetic properties required for hard magnetic materials. The contents of the impurity elements are preferably less than 3% by weight.
In the present invention, the surface of the respective iron compound particles may be coated with an Si compound and/or an Al compound, if required.
The coating of the respective iron compound particles with the Si compound and/or the Al compound may be conducted as follows. That is, after adjusting a pH value of a water suspension prepared by suspending the iron compound particles in water, the Si compound and/or the Al compound are added to the water suspension and mixed and stirred therewith, if required, followed by further adjusting the pH value of the mixture obtained after the mixing and stirring, thereby coating the surface of the respective iron compound particles with the Si compound and/or the Al compound. Next, the thus obtained coated particles are subjected to filtration, washing with water, drying and pulverization.
Examples of the Si compound usable in the present invention include water glass #3, sodium orthosilicate, sodium metasilicate and colloidal silica.
Examples of the Al compound usable in the present invention include aluminum salts such as aluminum acetate, aluminum sulfate, aluminum chloride and aluminum nitrate, aluminic acid alkali salts such as sodium aluminate, and alumina sol.
The amounts of the Si compound and/or the Al compound added are respectively preferably 1000 to 20000 ppm in terms of Si or in terms of Al based on the iron compound particles. When the amounts of the Si compound and/or the Al compound added are respectively less than 1000 ppm, it may be difficult to attain a sufficient effect of suppressing sintering between the particles upon the heat treatments. When the amounts of the Si compound and/or the Al compound added are respectively more than 20000 ppm, the content of non-magnetic components in the resulting particles tends to be undesirably increased.
The iron oxide or iron oxyhydroxide used as the starting material in the present invention is preferably coated with at least alumina or silica. More specifically, the surface of respective goethite particles is coated in order to suppress occurrence of sintering between the particles upon the heat treatment for obtaining metallic iron as a raw material used before subjected to the nitridation treatment from the goethite. The surface coating amount of the alumina or silica is not particularly limited, and is preferably 1000 to 20000 ppm, more preferably 1500 to 15000 ppm and still more preferably 1500 to 13000 ppm in terms of Si or Al metal element.
The specific surface area of the iron oxide or iron oxyhydroxide coated with the Si compound and/or the Al compound is preferably 90 to 250 m2/g. When the specific surface area of the iron oxide or iron oxyhydroxide coated is less than 90 m2/g, the nitridation tends to hardly proceed, thereby failing to obtain Fe16N2 in the form of a single phase. When the specific surface area of the iron oxide or iron oxyhydroxide coated is more than 250 m2/g, the nitridation tends to excessively proceed, thereby failing to obtain Fe16N2 in the form of a single phase. The specific surface area of the iron oxide or iron oxyhydroxide coated with the Si compound and/or the Al compound is more preferably 92 to 240 m2/g, and still more preferably 95 to 240 m2/g.
In the present invention, the iron oxide or iron oxyhydroxide may be coated with a compound of a rare earth element such as Y and La in addition to the above Si compound and Al compound.
Next, the iron compound particles, or the iron compound particles whose surface is coated with the Si compound and/or the Al compound, are subjected to reducing treatment.
The temperature of the reducing treatment is 300 to 600° C. When the temperature of the reducing treatment is less than 300° C., the iron compound particles may fail to be reduced into metallic iron to a sufficient extent. When the temperature of the reducing treatment is more than 600° C., although the iron compound particles can be sufficiently reduced into metallic iron, the sintering between the particles also tends to undesirably proceed. The temperature of the reducing treatment is preferably 350 to 500° C.
The atmosphere upon the reducing treatment is preferably a hydrogen atmosphere.
After conducting the reducing treatment, the nitridation treatment is carried out.
The temperature of the nitridation treatment is 100 to 200° C. When the temperature of the nitridation treatment is less than 100° C., the nitridation treatment tends to hardly proceed to a sufficient extent. When the temperature of the nitridation treatment is more than 200° C., γ′-Fe4N or ε′-Fe2-3N tends to be undesirably produced, thereby failing to produce Fe16N2 in the form of a single phase. The temperature of the reducing treatment is preferably 110 to 180° C.
The atmosphere upon the nitridation treatment is preferably an N2 atmosphere and may be mixed with NH3, H2, etc., in addition to N2.
The ferromagnetic particles according to the present invention can be obtained through the heat treatments for not more than 36 hr (total treatment time of the reducing treatment and the nitridation treatment). Upon industrially producing the Fe16N2 particles in the form of a single phase, it is preferred to form the single phase for a time period as short as possible to increase a yield of the ferromagnetic particles per unit time, thereby attaining an excellent industrial productivity. The total treatment time of the reducing treatment and the nitridation treatment is preferably not more than 33 hr and more preferably not more than 30 hr.
In the present invention, the properties of the iron oxide or iron oxyhydroxide as the starting material are well controlled, and the conditions of the above reducing treatment and nitridation treatment are appropriately selected, to obtain the ferromagnetic particles as aimed by the present invention.
Next, the anisotropic magnet according to the present invention is described.
The magnetic particles of the ferromagnetic magnet according to the present invention may be controlled so as to attain desired magnetic properties (such as a coercive force, a residual magnetic flux density and a maximum energy product) according to the purposes and applications as aimed.
The magnetic orientation method of the magnet is not particularly limited. For example, the Fe16N2 single phase particles are mixed and kneaded together with a dispersant in an EVA resin (ethylene-vinyl acetate resin) at a temperature not lower than a glass transition temperature thereof and molded, and an external magnetic field is applied to the resulting molded product at a temperature nearly exceeding the glass transition temperature to accelerate a magnetic orientation of the molded product. Alternatively, a resin such as urethane resins, an organic solvent and the Fe16N2 single phase particles may be strongly mixed with each other using a paint shaker, etc., and pulverized to prepare an ink, and the resulting ink may be applied and printed on a resin film with a blade or by a roll-to-roll method, and rapidly passed through a magnetic field to magnetically orient the resulting coated film.
Next, the resin composition for bonded magnet according to the present invention is described.
The resin composition for bonded magnet according to the present invention may be prepared by dispersing the ferromagnetic particles according to the present invention in a binder resin. The resin composition for bonded magnet comprises 85 to 99% by weight of the ferromagnetic particles, and the balance comprising the binder resin.
The binder resin used in the resin composition for bonded magnet may be selected from various resins depending upon the molding method used. In the case of an injection molding method, an extrusion molding method and a calender molding method, thermoplastic resins may be used as the binder resin. In the case of a compression molding method, thermosetting resins may be used as the binder resin. Examples of the thermoplastic resins include nylon (PA)-based resins, polypropylene (PP)-based resins, ethylene-vinyl acetate (EVA)-based resins, polyphenylene sulfide (PPS)-based resins, liquid crystal (LCP)-based resins, elastomer-based resins and rubber-based resins. Examples of the thermosetting resins include epoxy-based resins and phenol-based resins.
Meanwhile, upon production of the resin composition for bonded magnet, in order to facilitate the molding procedure and attain sufficient magnetic properties, in addition to the binder resin, there may also be used various known additives such as a plasticizer, a lubricant and a coupling agent, if required. Further, various kinds of magnet particles such as ferrite magnet particles may also be mixed in the resin composition.
These additives may be adequately selected according to the aimed applications. As the plasticizer, commercially available products may be appropriately used according to the resins used. The total amount of the plasticizers added is about 0.01 to about 5.0% by weight based on the weight of the binder resin.
Examples of the lubricant usable in the present invention include stearic acid and derivatives thereof, inorganic lubricants, oil-based lubricants. The lubricant may be used in an amount of about 0.01 to about 1.0% by weight based on a whole weight of the bonded magnet.
As the coupling agent, commercially available products may be used according to the resins and fillers used. The coupling agent may be used in an amount of about 0.01 to about 3.0% by weight based on the weight of the binder resin used.
The resin composition for bonded magnet according to the present invention may be produced by mixing and kneading the ferromagnetic particles with the binder resin.
The mixing of the ferromagnetic particles with the binder resin may be carried out using a mixing device such as a Henschel mixer, a V-shaped mixer and a Nauta mixer, whereas the kneading may be carried out using a single-screw kneader, a twin-screw kneader, a mill-type kneader, an extrusion kneader or the like.
Next, the bonded magnet according to the present invention is described.
The magnetic properties of the bonded magnet may be controlled so as to attain desired magnetic properties (such as a coercive force, a residual magnetic flux density and a maximum energy product) according to the aimed applications.
The bonded magnet according to the present invention may be produced by subjecting the above resin composition for bonded magnet to molding process by a known molding method such as an injection molding method, an extrusion molding method, a compression molding method or a calender molding method, and then subjecting the resulting molded product to electromagnet magnetization or pulse magnetization by an ordinary method to form a bonded magnet.
The ferromagnetic particles according to the present invention are in the form of Fe16N2 single phase particles without inclusion of any other phases and therefore can exhibit a large BHmax value.
Next, the present invention is described in more detail by the following Examples. However, these Examples are only illustrative and not intended to limit the present invention thereto. The evaluation methods used in Examples, etc., are as follows.
The specific surface area of the iron oxide or iron oxyhydroxide as the starting material or the obtained Fe16N2 particles was measured by a B.E.T. method using nitrogen.
The particle size of primary particles of the iron oxide or iron oxyhydroxide as the starting material or the obtained Fe16N2 particles was measured using a transmission electron microscope “JEM-1200EXII” manufactured by Nippon Denshi Co., Ltd. In this case, particle sizes of 120 particles randomly selected were measured to obtain an average value thereof.
The compositions of the iron oxide or iron oxyhydroxide as the starting material, the obtained Fe16N2 particles, and the coating material used for forming a surface coating layer on these particles, were determined by analyzing a solution prepared by dissolving the sample in an acid under heating using a plasma emission spectroscopic apparatus “SPS4000” manufactured by Seiko Denshi Kogyo Co., Ltd.
The constituting phase of the iron oxide or iron oxyhydroxide as the starting material or the obtained Fe16N2 particles was determined by the identification carried out using a powder X-ray diffractometer (XRD) “RINT-2500” manufactured by Rigaku Co., Ltd., and by the electron beam diffraction (ED) evaluation carried out using a transmission electron microscope “JEM-1200EXII” manufactured by Nippon Denshi Co., Ltd. In the ED evaluation, it was possible to determine whether or not impurity phases such as α-Fe and Fe4N are present in a micro state, by using the difference in lattice constant therebetween.
The magnetic properties of the obtained Fe16N2 particles were measured at room temperature (300 K) in a magnetic field of 0 to 7 T using a physical property measurement system (PPMS) manufactured by Quantum Design Japan Co., Ltd.
Goethite particles having a minor axis diameter of 17 nm, a major axis diameter of 110 nm and a specific surface area of 123 m2/g were produced from ferric chloride, sodium hydroxide and sodium carbonate. The resulting goethite particles were separated by filtration using a nutshe, and repulped using a disper so as to prepare a slurry having a concentration of 3 g/L in pure water. The resulting slurry was held at a pH value of 6.5 using a dilute nitric acid solution, and a water glass solution comprising SiO2 in an amount of 5% by weight was dropped thereto at 40° C. over 2 hr such that Si content in the SiO2-coated goethite particles was 5000 ppm. The resulting particles were separated again by filtration using a nutsche, and washed with pure water such that the pure water was used in an amount of 150 mL per 5 g of the sample. Successively, the obtained particles were dried at 60° C. using a vacuum dryer, and only aggregated particles having a particle size of not more than 10 μm were extracted using an atomizer mill and a vibration sieve. The Si content in the thus obtained sample was 4800 ppm.
The above obtained sample particles in an amount of 50 g were charged in an alumina sagger (125 mm×125 mm×30 mm in depth), and allowed to stand in a heat treatment furnace. An inside of the furnace was evacuated and then filled with an argon gas, and further evaluated gain. This procedure was repeated three times. Thereafter, while flowing a hydrogen gas at a flow rate of 5 L/min, the sample particles were heated to 400° C. at a temperature rise rate of 5° C./min and held at that temperature for 4 hr to subject the particles to reducing treatment. Thereafter, the particles were cooled to 140° C. at which supply of the hydrogen gas was stopped. Successively, while flowing an ammonia gas at a flow rate of 10 L/min, the particles were subjected to nitridation treatment at 140° C. for 20 hr. Thereafter, while flowing an argon gas, the particles were cooled to room temperature at which supply of the argon gas was stopped, and the inside atmosphere was replaced with air over 3 hr.
As a result of subjecting the resulting sample particles to XRD and ED analysis, it was confirmed that the sample particles exhibited an Fe16N2 single phase, and primary particles thereof had a minor axis diameter of 22 nm, a major axis diameter of 98 nm and a specific surface area of 132 m2/g. As a result of measurement of magnetic properties of the sample particles, it was confirmed that the sample particles had a saturation magnetization value σs of 147 emu/g, a coercive force Hc of 2710 Oe and BHmax of 7.4 MGOe.
Goethite particles having a minor axis diameter of 15 nm, a major axis diameter of 30 nm and a specific surface area of 197 m2/g were produced from ferric chloride, sodium hydroxide and sodium carbonate by the same method as defined in Example 1. The resulting goethite particles were separated by filtration using a nutshe, and repulped using a disper so as to prepare a slurry having a concentration of 5 g/L in pure water. The resulting slurry was held at a pH value of 7.0 using a dilute nitric acid solution, and a water glass solution comprising SiO2 in an amount of 5% by weight was dropped thereto at 40° C. over 5 hr such that the Si content in the SiO2-coated goethite particles was 10000 ppm. The resulting particles were separated again by filtration using a nutsche, and washed with pure water such that the pure water was used in an amount of 200 mL per 5 g of the sample. Successively, the obtained particles were dried at 55° C. using a vacuum dryer, and only aggregated particles having a particle size of not more than 10 μm were extracted using an atomizer mill and a vibrating sieve. The Si content in the thus obtained sample was 9800 ppm.
Next, the above obtained sample particles were subjected to reducing treatment and then to nitridation treatment by the same method as defined in Example 1 except that the gas used upon the nitridation treatment was replaced with a mixed gas comprising an ammonia gas, a nitrogen gas and a hydrogen gas at a mixing ratio of 7:2.8:0.2, and the nitridation treatment was carried out at 140° C. for 17 hr while flowing the mixed gas at a flow rate of 8 L/min in total.
As a result of subjecting the resulting sample particles to XRD and ED analysis, it was confirmed that the sample particles exhibited an Fe16N2 single phase, and primary particles thereof had a minor axis diameter of 19 nm, a major axis diameter of 28 nm and a specific surface area of 201 m2/g. As a result of measurement of magnetic properties of the sample particles, it was confirmed that the sample particles had a saturation magnetization value σs of 159 emu/g, a coercive force Hc of 2658 Oe and BHmax of 7.0 MGOe.
The sample was obtained by the same method as defined in Example 2 except that the surface of the respective goethite particles was first coated with yttria in an amount of 700 ppm in terms of Y element and then coated with alumina in an amount of 3000 ppm in terms of aluminum element. The reducing treatment was carried out by the same method as defined in Example 1. In addition, the nitridation treatment was carried out at 142° C. for 15 hr while flowing an ammonia gas at a flow rate of 5 L/min. As a result, it was confirmed that the obtained sample has a Y content of 689 ppm and an Al content of 2950 ppm.
As a result of subjecting the resulting particles to XRD and ED analysis, it was confirmed that the particles exhibited an Fe16N2 single phase, and primary particles thereof had a minor axis diameter of 18 nm, a major axis diameter of 30 nm and a specific surface area of 205 m2/g. As a result of measurement of magnetic properties of the obtained particles, it was confirmed that the particles had a saturation magnetization value σs of 151 emu/g, a coercive force Hc of 2688 Oe and BHmax of 7.1 MGOe.
Ferrous nitrate and ferric nitrate were weighed such that an Fe ratio therebetween was 0.97:2 and dissolved to prepare a solution, and magnetite having a major axis diameter of 13 nm, a minor axis diameter of 13 nm and a specific surface area of 156 m2/g was produced from the resulting solution and sodium hydroxide. The thus obtained magnetite particles were coated with silica in an amount of 4000 ppm in terms of Si by the same method as defined in Example 1. As a result of analyzing the resulting particles, it was confirmed that the Si content in the magnetite was 3780 ppm. As a result of subjecting the magnetite to XRD analysis, it was confirmed that the magnetite comprised a trace amount of α-Fe2O3 as an impurity. The thus obtained magnetite particles were subjected to washing, drying, pulverization and sieving by the same method as defined in Example 1, and thereafter subjected to reducing treatment and then to nitridation treatment by the same method as defined in Example 2.
As a result of subjecting the resulting particles to XRD and ED analysis, it was confirmed that the particles exhibited an Fe16N2 single phase, and primary particles thereof had a minor axis diameter of 14 nm, a major axis diameter of 14 nm and a specific surface area of 173 m2/g. As a result of measurement of magnetic properties of the obtained particles, it was confirmed that the particles had a saturation magnetization value σs of 145 emu/g, a coercive force Hc of 2258 Oe and BHmax of 6.3 MGOe.
Goethite particles having a minor axis diameter of 17 nm, a major axis diameter of 110 nm and a specific surface area of 123 m2/g were produced by the same method as defined in Example 1. The resulting goethite particles were heat-treated in air at 300° C. for 1 h to obtain hematite particles. Successively, the thus obtained hematite particles were subjected to reducing treatment at 295° C. for 4 hr in a flow of 100% hydrogen gas, and then cooled in the furnace to 100° C. while flowing hydrogen therethrough. The flowing gas was changed from the hydrogen gas to a 100% ammonia gas, and the ammonia gas was flowed at a rate of 4 L/min. The resulting particles were heated to 150° C. at a temperature rise rate of 5° C./min and subjected to nitridation treatment at 150° C. for 10 hr.
As a result of subjecting the resulting particles to XRD and ED analysis, it was confirmed that the particles exhibited an Fe16N2 single phase, and primary particles thereof had a minor axis diameter of 32 nm, a major axis diameter of 53 nm and a specific surface area of 86 m2/g. As a result of measurement of magnetic properties of the particles, it was confirmed that the particles had a saturation magnetization value σs of 166 emu/g, a coercive force Hc of 1940 Oe and BHmax of 9.1 MGOe.
The silica-coated goethite particles obtained by the same method as defined in Example 1 were subjected to reducing treatment at 650° C. for 20 hr, and then to nitridation treatment at 160° C. for 12 hr while flowing an ammonia gas therethrough at a rate of 4 L/min.
As a result of subjecting the resulting particles to XRD and ED analysis, it was confirmed that the particles exhibited a mixed phase of α-Fe, Fe16N2, Fe3N and Fe4N, and primary particles thereof had a minor axis diameter of 34 nm, a major axis diameter of 85 nm and a specific surface area of 105 m2/g. As a result of measurement of magnetic properties of the particles, it was confirmed that the particles had a saturation magnetization value σs of 136 emu/g, a coercive force Hc of 1235 Oe and BHmax of 3.4 MGOe.
Goethite particles having a minor axis diameter of 24 nm, a major axis diameter of 240 nm and a specific surface area of 88 m2/g were produced from ferric chloride and sodium hydroxide. The resulting goethite particles were coated with silica in an amount of 4000 ppm in terms of Si by the same method as defined in Example 1. As a result of analyzing the resulting particles, it was confirmed that the Si content therein was 3530 ppm. Next, the obtained particles were successively subjected to washing, drying, pulverization and sieving by the same method as defined in Example 1, and thereafter subjected to reducing treatment and then to nitridation treatment. The nitridation treatment was carried out at 160° C. for 24 hr while flowing a mixed gas comprising an ammonia gas, a nitrogen gas and a hydrogen gas at a mixing ratio of 7:0.3:2.7 at flow rate of 8 L/min in total.
As a result of subjecting the resulting particles to XRD and ED analysis, it was confirmed that the particles exhibited a mixed phase of α-Fe, Fe16N2, Fe3N and Fe4N, and primary particles thereof had a minor axis diameter of 30 nm, a major axis diameter of 207 nm and a specific surface area of 99 m2/g. As a result of measurement of magnetic properties of the particles, it was confirmed that the particles had a saturation magnetization value σs of 108 emu/g, a coercive force Hc of 1745 Oe and BHmax of 2.9 MGOe.
Goethite particles having a minor axis diameter of 35 nm, a major axis diameter of 157 nm and a specific surface area of 78 m2/g were produced from ferric chloride and sodium hydroxide. The resulting goethite particles were coated with silica in an amount of 9000 ppm in terms of Si by the same method as defined in Example 1. As a result of analyzing the resulting particles, it was confirmed that the Si content therein was 8600 ppm. Next, the obtained particles were successively subjected to washing, drying, pulverization and sieving by the same method as defined in Example 1, and thereafter subjected to reducing treatment and then to nitridation treatment by the same method as defined in Example 1.
As a result of subjecting the resulting particles to XRD and ED analysis, it was confirmed that the particles exhibited a mixed phase of α-Fe, Fe16N2, Fe3N and Fe4N, and primary particles thereof had a minor axis diameter of 43 nm, a major axis diameter of 126 nm and a specific surface area of 97 m2/g. As a result of measurement of magnetic properties of the particles, it was confirmed that the particles had a saturation magnetization value σs of 106 emu/g, a coercive force Hc of 1368 Oe and BHmax of 2.1 MGOe.
In the process for producing the ferromagnetic particles according to the present invention, it is possible to readily produce the Fe16N2 particles having a large BHmax value. Therefore, the production process of the present invention is suitable as the process for producing ferromagnetic particles.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2009-243834 | Oct 2009 | JP | national |
| Number | Date | Country | |
|---|---|---|---|
| Parent | 13503215 | Jun 2012 | US |
| Child | 15059906 | US |
