WO2003079332A1 - Magnetic recording medium and magnetic recording cartridge - Google Patents
Magnetic recording medium and magnetic recording cartridge Download PDFInfo
- Publication number
- WO2003079332A1 WO2003079332A1 PCT/JP2003/001910 JP0301910W WO03079332A1 WO 2003079332 A1 WO2003079332 A1 WO 2003079332A1 JP 0301910 W JP0301910 W JP 0301910W WO 03079332 A1 WO03079332 A1 WO 03079332A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- magnetic
- iron
- magnetic powder
- powder
- layer
- Prior art date
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- H01F1/0036—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties showing low dimensional magnetism, i.e. spin rearrangements due to a restriction of dimensions, e.g. showing giant magnetoresistivity
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- 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
- H01F1/0551—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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- 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
- H01F1/059—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and Va elements, e.g. Sm2Fe17N2
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- G—PHYSICS
- G11—INFORMATION STORAGE
- G11B—INFORMATION STORAGE BASED ON RELATIVE MOVEMENT BETWEEN RECORD CARRIER AND TRANSDUCER
- G11B23/00—Record carriers not specific to the method of recording or reproducing; Accessories, e.g. containers, specially adapted for co-operation with the recording or reproducing apparatus ; Intermediate mediums; Apparatus or processes specially adapted for their manufacture
- G11B23/02—Containers; Storing means both adapted to cooperate with the recording or reproducing means
- G11B23/04—Magazines; Cassettes for webs or filaments
- G11B23/08—Magazines; Cassettes for webs or filaments for housing webs or filaments having two distinct ends
- G11B23/107—Magazines; Cassettes for webs or filaments for housing webs or filaments having two distinct ends using one reel or core, one end of the record carrier coming out of the magazine or cassette
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- G—PHYSICS
- G11—INFORMATION STORAGE
- G11B—INFORMATION STORAGE BASED ON RELATIVE MOVEMENT BETWEEN RECORD CARRIER AND TRANSDUCER
- G11B5/00—Recording by magnetisation or demagnetisation of a record carrier; Reproducing by magnetic means; Record carriers therefor
- G11B5/62—Record carriers characterised by the selection of the material
- G11B5/73—Base layers, i.e. all non-magnetic layers lying under a lowermost magnetic recording layer, e.g. including any non-magnetic layer in between a first magnetic recording layer and either an underlying substrate or a soft magnetic underlayer
- G11B5/735—Base layers, i.e. all non-magnetic layers lying under a lowermost magnetic recording layer, e.g. including any non-magnetic layer in between a first magnetic recording layer and either an underlying substrate or a soft magnetic underlayer characterised by the back layer
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- G—PHYSICS
- G11—INFORMATION STORAGE
- G11B—INFORMATION STORAGE BASED ON RELATIVE MOVEMENT BETWEEN RECORD CARRIER AND TRANSDUCER
- G11B5/00—Recording by magnetisation or demagnetisation of a record carrier; Reproducing by magnetic means; Record carriers therefor
- G11B5/74—Record carriers characterised by the form, e.g. sheet shaped to wrap around a drum
- G11B5/78—Tape carriers
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/11—Magnetic recording head
- Y10T428/1107—Magnetoresistive
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/29—Coated or structually defined flake, particle, cell, strand, strand portion, rod, filament, macroscopic fiber or mass thereof
- Y10T428/2982—Particulate matter [e.g., sphere, flake, etc.]
- Y10T428/2991—Coated
Definitions
- the effective thickness of the magnetic layer is about 1 Z3, which is the shortest recording wavelength used in the system.
- the thickness of the magnetic layer is small. Is required to be about 0.1 // m.
- cassettes also referred to as cartridges
- the magnetic layer is inevitable. Need to be thinner.
- the magnetic flux generated from the magnetic head must be reduced to a small area, and since the magnetic head has also been reduced in size, the amount of generated magnetic flux must be reduced.
- the MR head uses a magnetoresistive element that can provide high output even with a small magnetic flux in the reproducing head. You need to use .
- Magnetic recording media compatible with MR heads include those described in, for example, JP-A-11-238225, JP-A-2000-40217, and JP-A-2000-40218.
- the magnetic flux (the product of the residual magnetic flux density and the thickness) is set to a specific value or less to prevent the distortion of the output of the MR head and to prevent the magnetic layer surface from being sunk.
- the asperity of the MR head is reduced by setting it below a certain value.
- the track servo method includes an optical track servo method (JP-A-11-213384, JP-A-11-339254, and JP-A-2000-293836) and a magnetic servo method, and either method is adopted.
- a magnetic tape cartridge also referred to as a force-setting tape
- a single-reel type single reel having only one reel for winding a magnetic tape is used.
- a magnetic servo system As described above, there are a magnetic servo system and an optical servo system in the track servo system.
- a servo track band to be described later is formed on a magnetic layer by magnetic recording, and the magnetic layer is magnetically read and read. And perform tracking, the latter of which
- a ServoTrack node composed of a concave array is formed on the back coat layer by laser irradiation or the like, and this is optically read to perform Servotracking.
- the back coat layer is also provided with magnetism, and a magnetic servo signal is recorded on the back coat layer (for example, Japanese Patent Laid-Open No. 11-126327).
- the optical servo method there is also a method of recording an optical servo signal on a back coat layer using a material that absorbs light (for example, Japanese Patent Application Laid-Open No. 11-126328).
- the recording head is composed of a magnetic induction type head, and the reproducing head is composed of an MR head.
- the MR head for the servo track that reads the servo signal
- the recording / playback head moves in the width direction of the tape, and the data track (for example, 8 x 2 pairs of recording / playback heads).
- the data track for example, 8 x 2 pairs of recording / playback heads.
- the improvement of magnetic powder and medium manufacturing technology has almost reached the limit at present.
- the particle size in the major axis direction is practically limited to about 100 nm as long as needle-like magnetic powder is used. The reason for this is that if the particles are made finer than this, the specific surface area becomes extremely large, and not only does the saturated magnetic field decrease, but also it becomes extremely difficult to disperse the magnetic powder in the binder resin.
- coercive force due to technological innovations in magnetic heads, recording is possible even on media with even higher coercive force.
- the coercive force be as high as possible in order to prevent a decrease in output due to recording and reproduction demagnetization as long as recording and erasing can be performed with the head. Therefore, the most effective and practical method for improving the recording density of a magnetic recording medium is to increase the coercive force of the magnetic recording medium.
- the thickness of the magnetic layer is limited. This is because, due to the longitudinal orientation, the needle-like particles are arranged such that the needle-like direction is parallel to the in-plane direction of the medium on average, but the distribution of the particles has a distribution, so that the needle-like direction is aligned with the medium surface. This is because some particles are arranged vertically. The presence of such particles impairs the surface smoothness of the medium and causes noise. Such problems become more serious as the thickness of the magnetic layer becomes thinner.
- barium ferrite magnetic powder is known to be a fine magnetic powder having a plate-like particle shape and a particle size of about 50 nm (for example, Japanese Patent Publication No. Japanese Patent Publication No. 03232, Japanese Patent Publication No. 6-18062, etc.).
- the shape and particle size of the barium ferrite magnetic powder are more suitable for obtaining a thin-layer coating type magnetic recording medium than that of the acicular magnetic powder.
- the saturation magnetization is at most about 7.5 / i Wb / g because of the fact that the magnetic powder of the powder of a ferrite powder is an oxide, and 12.6 / Wb Z, such as a needle-like metal or alloy magnetic powder.
- the magnitude of the magnetic anisotropy in the shape anisotropy is represented by 2 ⁇ s, and when the acicular ratio (particle length / particle diameter) of the magnetic powder is about 5 or more, The coefficient is approximately 2 ⁇ , but the coefficient decreases sharply when the needle ratio is less than 5, and the anisotropy disappears when the ratio is spherical. That is, as long as a magnetic material such as Fe metal or a Fe-Co alloy is used as the magnetic powder, the shape of the magnetic powder is theoretically a needle. The actual situation is that the shape must be changed.
- the particle shape is close to a spherical shape with the minimum specific surface area.
- a magnetic recording medium comprising: at least one magnetic layer containing: a binder resin; and a back layer formed on the other surface of the nonmagnetic support.
- the magnetic powder contained in the uppermost magnetic layer of the magnetic layer is a rare earth-iron-based magnetic powder composed of a rare earth element and an iron or iron-based transition element, which is essentially spherical or elliptical.
- a magnetic recording medium having a number average particle diameter of about 50 nm and an average axis ratio of 1 or more and 2 or less, and wherein the total thickness of the magnetic recording medium is less than 6 ⁇ m.
- the thickness of the uppermost magnetic layer (hereinafter, simply referred to as “magnetic layer”) is more preferably 0.09 / m or less because high-density magnetic recording can be performed.
- the essentially spherical or elliptical rare earth ferrous magnetic powder one having a particle size equal to or less than the thickness of the uppermost layer is used.
- the rare-earth iron-based magnetic powder having the above specific configuration is essentially a spherical or elliptical ultrafine magnetic powder, a magnetic recording medium using the same has a high coercive force and a high magnetic flux density. Obtained easily.
- essentially spherical or elliptical refers to a substance having an uneven surface as shown in a photograph such as FIG. , And "spherical or elliptical” having slight deformation.
- the magnetic recording medium using the rare-earth iron-based magnetic powder which is essentially spherical or elliptical and has a very small particle size as described above, has a small magnetic interaction between the magnetic powders. It has also been found that rapid magnetization reversal becomes possible and the magnetization reversal area becomes narrower, so that better recording characteristics can be obtained compared to a conventional magnetic recording medium using needle-shaped magnetic powder.
- the magnetic recording medium of the present invention is particularly effective when the magnetic layer has a thickness force S of 0.09 ⁇ m or less, but the magnetic layer has a small thickness. ! / In the medium, the effect of demagnetization due to the demagnetizing field was reduced, and it was found that excellent recording characteristics were exhibited even at a coercive force of about 80 kA / m (10050e). .
- FIG. 1 is a perspective view showing the structure of a general magnetic tape cartridge of the present invention.
- FIG. 2 is a sectional view of the magnetic tape cartridge of FIG.
- FIG. 3 is a transmission electron micrograph (magnification: 250,000 times) of the neodymium ferrous magnetic powder produced in Example 1.
- FIG. 4 is an X-ray diffraction pattern of the yttrium monoiron nitride magnetic powder produced in Example 8.
- FIG. 5 is a transmission electron micrograph (magnification: 200,000 times) of the yttrium-iron nitride-based magnetic powder produced in Example 8.
- FIG. 6 is a transmission electron micrograph (magnification: 200,000 times) of the yttriamu iron nitride-based magnetic powder produced in Example 10.
- FIG. 7 is a diagram for explaining a magnetic servo system which is an example of a track support system used for a magnetic tape. Data tracks and servo bands are alternately arranged on a magnetic recording surface (magnetic layer) of the magnetic tape. It is a schematic diagram which shows the state provided in.
- the origin of the coercive force is based on the shape magnetic anisotropy due to the acicular shape, the acicular ratio can be reduced only to at least about 5 at the minimum. This is because the coercive force is reduced due to reduced coercivity.
- the present inventors have synthesized various magnetic powders aiming at improvement of magnetic properties from a viewpoint different from the conventional magnetic powders based on shape magnetic anisotropy, and obtained their magnetic properties.
- the anisotropy was investigated.
- rare earth-iron based magnetic powders containing at least rare earth and iron as constituent elements have a large crystal magnetic anisotropy, so that they do not need to be needle-shaped, and are essentially spherical or elliptical. It was found that even a magnetic powder can exert a large coercive force in one direction.
- the essentially elliptical magnetic powder referred to in the present invention means that the ratio of the major axis diameter to the minor axis diameter is 2 or less (preferably 1.5 or less). This is essentially different from the conventional magnetic powder for magnetic recording media in its shape.
- Examples of the essentially spherical or elliptical magnetic powder of the present invention include rare earth-iron-boron magnetic powder (Japanese Patent Application Laid-Open No. 2001-181754) and rare earth-iron magnetic powder (Japanese Patent Application Laid-Open No. 2002-56518). There is such a rare earth ferrous magnetic powder.
- the rare earth element used in these magnetic powders is at least one element selected from the group consisting of yttrium, ytterbium, cesium, praseodymium, samarium, lanthanum, europium, neodymium, tenorium, and the like.
- Nid samarium
- Tb teslevium
- Y yttrium
- an essentially spherical iron nitride-based magnetic powder containing no rare earth element but having a BET specific surface area of 10 m 2 Zg or more with an Fe 16 N 2 phase as a main phase Japanese Patent Laid-Open No. 2000-277311) ) are known. The inventors have improved this magnetic powder to produce the rare-earth iron nitride-based magnetic powder of the present invention that is optimal as a high-density magnetic recording medium.
- the main improvement is that, as described below, the rare earth element, which has a high sintering prevention effect, high coercive force effect, and high stability (corrosion resistance) improving effect, is mainly present in the outer layer of the magnetic powder.
- a coercive force as high as 200 kAZm or more
- a BET specific surface area suitable for high-density recording It is a chemically stable fine particle magnetic powder.
- the saturation magnetization of the magnetic powder is controlled to 10 to 20 // Wb / g by making the rare earth element predominantly present in the outer layer of the magnetic powder and performing oxidation stabilization treatment, and the paint dispersibility ⁇ Rare earth mono-nitride magnetic powder with excellent oxidation stability.
- the rare earth-iron nitride based magnetic powder obtained in this manner has a coercive force of 200 kAZm or more, is fine particles, and has high dispersibility and magnetic stability when preparing a magnetic paint.
- Rare-earth iron-boron magnetic powder, rare-earth iron-based magnetic powder do not contain rare-earth element! /, Compared with iron nitride-based magnetic powder having Fei 6 N 2 phase as main phase, especially the present invention It is suitable as a magnetic powder for the uppermost magnetic layer.
- Such an essentially spherical or elliptical rare earth-iron-iron or iron-nitride-based magnetic powder is applied to a thin-layer coated magnetic recording medium, especially a coated magnetic recording medium having a total thickness of less than 6 ⁇ m.
- a coated magnetic recording medium having a total thickness of less than 6 ⁇ m.
- the rare-earth iron-based magnetic powder mainly containing metallic iron or an iron alloy in a part of the core has the highest saturation magnetization when the core is made of an iron-cobalt alloy.
- the content of iron and cobalt in the magnetic powder, expressed as the atomic ratio of cobalt Z iron, is preferably 3/97 to 40/60! / ,.
- this metallic iron or iron alloy has no shape anisotropy, the coercive force is low. However, if iron contains 0.2 to 20 atoms ⁇ 1 ⁇ 2 rare earth element, the coercive force becomes Increase significantly. In particular, if the rare-earth element is mainly present in the outer layer portion including the core portion, a higher coercive force can be achieved. '
- the present inventors have studied the particle size of the rare-earth iron-based magnetic powder, and have found that when the average particle size is 5 to 50 nm, excellent magnetic properties of the magnetic layer can be achieved. I found it. With conventional needle-shaped magnetic powders, the maintenance of high coercive force was almost limited to an average particle size of about 100 nm in the major axis direction, but the magnetic powder of the present invention is mainly Because of the origin of coercive force in crystal anisotropy, it is possible to make extremely fine particles with an average particle size of up to 5 nm, and it is possible to exhibit excellent magnetic properties even with such fine particles .
- a particularly preferred average particle size is 8 nm or more, and more preferably 10 nm or more.
- the average particle size of the magnetic powder must be 50 nm or less, preferably 40 nm or less, and more preferably 30 nm or less. With such a setting, extremely high filling property can be obtained, and excellent saturation magnetic flux density can be achieved. It is particularly important that the average particle size is 50 nm or less, particularly preferably 30 nm or less, when the thickness of the magnetic layer is 0.09 / im or less.
- the metal species that forms an alloy with iron includes Mn, Zn, Ni, Cu, and Co.
- the amount of the above transition metal element is 5 to 50 atoms with respect to iron. / 0 , more preferably 10 to 30 atomic%.
- 0 0 content is preferably 1 0 atomic% or less.
- the bonding due to the magnetic interaction of a plurality of types of magnetic anisotropy is further strengthened and unified inside the particles, and as a magnetic powder for a high-performance magnetic recording medium.
- An optimum coercive force of 80 to 400 kA / m is obtained.
- the particle shape of the rare-earth iron-based magnetic powder will be described from the viewpoint of the dispersibility of the magnetic paint and the characteristics for forming a thin magnetic layer.
- the specific surface area inevitably increases, and interaction with the binder resin occurs. It becomes difficult to obtain a uniform dispersion when dispersing in a binder resin, and when diluted with a large amount of organic solvent for thin layer coating, aggregation of magnetic powder is likely to occur, and orientation And surface smoothness deteriorates. For this reason, there is a limit to the particle size of the magnetic powder that can be used as a coating type magnetic recording medium.
- the rare-earth iron-based magnetic powder used in the present invention not only has a small particle size, but also has a particle shape essentially spherical or elliptical, and can have a shape close to spherical. Therefore, the phenomenon that particles protrude from the surface of the magnetic layer unlike the needle-like magnetic powder does not occur, and when the undercoat layer is provided, the magnetic powder protrudes into the undercoat layer compared to the needle-like magnetic powder. And a magnetic layer having extremely good surface smoothness can be formed. Further, when the thickness of the magnetic layer is reduced, the magnetic flux from the magnetic layer is reduced, and as a result, there is a problem that the output is reduced.
- the magnetic powder used in the present invention has an essentially spherical particle shape. Since it is possible to take an elliptical shape and a shape close to a sphere, it is easier to fill the magnetic powder into the magnetic layer at a higher level than a needle-like magnetic powder, and as a result, it is easy to obtain a high magnetic flux density. It also has a great advantage. Further, with respect to the saturation magnetization, the metal or alloy magnetic powder generally has a larger specific surface area as the particle size decreases, and the proportion of the surface oxide layer that does not contribute to the saturation magnetization increases, contributing to the saturation magnetization. The magnetic part becomes smaller. In other words, as the particle size becomes smaller, the saturation magnetic field becomes smaller.
- the above-mentioned essentially spherical or elliptical rare earth iron-based magnetic powder used in the present invention has a saturation magnetization, a coercive force, a particle size, and a particle shape which are all essential for obtaining a thin magnetic layer.
- a magnetic recording medium having an average thickness of the magnetic layer of 0.09 ⁇ m or less is manufactured using the magnetic recording medium, particularly excellent recording / reproducing characteristics can be obtained.
- the saturation magnetization is 10 to 25 ⁇ W. bg (79.6 to 199.0 Am 2 / kg) is preferred, and 10 to 20 / i W b / g (79.6 to 159.2 Am 2 / kg) is more preferred. .
- the coercive force and saturation magnetization of the magnetic powder are defined as It means the value after correction with the reference sample when measured with an applied magnetic field at 25 ° C and an applied magnetic field of 1273.3 kA / m (16 kOe) using a dynamometer.
- the ratio of the binder resin to perform kneading in 1 7-0 wt% with respect to the magnetic powder As a post-step of the kneading step, a continuous twin-screw kneader or other diluting equipment is used to add and mix the binder resin solution and / or solvent at least once and knead and dilute, and to rotate fine media such as a sand mill.
- the paint is dispersed by a dispersion process using a die dispersion device.
- Nonmagnetic particles used in the undercoat layer include titanium oxide, iron oxide, and aluminum oxide; preferably, iron oxide alone or a mixed system of iron oxide and aluminum oxide is used. Normally, non-magnetic iron oxide with a major axis length of 0.05 to 0.2 / im and a minor axis length of 5 to 200 nm is mainly used, and the particle size is 0.1 to 0.1 ⁇ m if necessary. ⁇ carbon black, particle size 0:! ⁇ 0.5 // m The non-magnetic particles and the carbon black do not particularly have a sharp particle size distribution, and when the thickness of the undercoat layer is 1.0 m or more, it does not cause much problem.
- plate-like aluminum oxide particles having a number average particle diameter of 10 nm to 100 nm are used as ultrafine aluminum oxide particles having a small particle size distribution and suitable for the undercoat layer.
- the plate-shaped iron oxide particles may be used alone, or a mixture of the plate-shaped iron oxide particles and the plate-shaped aluminum oxide particles may be used.
- the plate-like aluminum oxide particles having a particle diameter of 10 nm to L00 nm used in the present invention have two main features. One is that it is a plate of super-alumina particles, so that even in a thin layer coating of 0.9 m or less, the thickness unevenness is small and the surface smoothness does not decrease.
- the second feature is that the coating film is formed in a state where the plate-shaped particles overlap, The effect of reinforcing the coating in the plane direction is great, and at the same time, the dimensional stability due to changes in temperature and humidity increases.
- the product of the residual magnetic flux density in the tape longitudinal direction and the thickness of the magnetic layer is preferably 0.0018 to 0.05 Tm, more preferably 0.0036 to 0.05 ⁇ Tm, and 0.004 to 0.05 / iTm. Is more preferred. If this product is less than 0.0018 ⁇ Tm, M
- the content of nitrogen relative to iron is preferably 1.0 to 20 atomic%, more preferably 1.0 to 12.5 atomic%, and still more preferably 3 to 12.5 atomic%.
- the content of the rare earth element is too small, the contribution of the magnetic anisotropy based on the rare earth element is reduced, and coarse particles are easily generated by sintering or the like during reduction, and the particle size distribution is deteriorated. If the amount of rare earth elements is too large, unreacted rare earth elements in addition to rare earth elements that contribute to magnetic anisotropy increase, and magnetic properties, especially saturation magnetization, are likely to be excessively reduced.
- the saturation magnetization of the rare-earth iron mononitride magnetic powder of the present invention is more preferably 80 to: 160 Am 2 / kg (80 to 160 emu / g, 10.0 to 20.1 / xWb / g),
- the coercive force is 80 to 400 kAZm (1005 ⁇ 5024 Oe) is preferred.
- k A / m (1, 50 OO e) or more is more preferable, 159.2 k A / m (200 00 e) or more is more preferable, 180 k A / m (2261 Oe) or more is more preferable, and 200 k AZm (251 20 e) or more is most preferable. Further, it is more preferably at most 318.5 kA / m (400 OOe), further preferably at most 278.6 kA / m (35 OOe).
- the BET specific surface area of the rare earth iron mononitride magnetic powder of the present invention is preferably 40 to 100 m 2 Zg. If the BET specific surface area is too small, the particle size increases, so that when applied to a magnetic recording medium, the particle noise tends to increase, and the surface smoothness of the magnetic layer decreases, and the reproduction output tends to decrease. On the other hand, if the BET specific surface area is too large, it is difficult to obtain a uniform dispersion in the magnetic paint due to agglomeration of the magnetic powder, and when applied to a magnetic recording medium, the orientation and the surface smoothness tend to decrease. .
- the rare-earth iron-nitride-based magnetic powder of the present invention has excellent characteristics as a magnetic powder for a magnetic recording medium, but also has excellent storage stability, and When the magnetic recording medium is stored in a high-temperature and high-humidity environment, its magnetic properties such as saturation magnetization do not deteriorate much, so it is suitable for high-density recording magnetic recording media.
- the high magnetic anisotropy of the Fe 16 N 2 phase is added to the magnetic anisotropy of the compound containing the rare earth element.
- it is considered that it shows a unique performance not found in the conventional magnetic powder. If the rare earth element is predominantly present in the outer layer (surface) of the magnetic powder, a higher coercive force can be easily obtained due to the surface magnetic anisotropy, and the shape maintaining effect of the magnetic powder during reduction etc. It is thought to be based on many factors, such as sharpening of the particle size distribution.
- the rare-earth iron nitride magnetic powder of the present invention it is not excluded that the rare-earth element is present inside the magnetic powder, but even in that case, the magnetic powder has a multilayer structure of an inner layer and an outer layer.
- the configuration is such that it mainly exists in the outer layer (surface) of the magnetic powder.
- the F e phase of the inner layer (core portion) and F e 16 N 2 phase, all the internal phase need not be the F e 16 N 2 phase, F e 16 N 2 phase and alpha-F e It may be a mixed phase. Rather, by adjusting the ratio of the Fe 16 N 2 phase to the a- Fe phase, There is an advantage that the desired coercive force can be easily set.
- rare earth element examples include the above-mentioned yttrium, ytterbium, cesium, praseodymium, lanthanum, samarium, europium, neodymium, and tenorebium.
- yttrium, samarium or neodymium is preferable because at least one of them is selected because it has a large effect of improving the coercive force and a large effect of maintaining the particle shape during reduction.
- an element such as phosphorus, silicon, aluminum, carbon, calcium, and magnesium may be contained together with such a rare earth element.
- an element selected from silicon and aluminum having an effect of preventing sintering in combination with a rare earth element it is possible to obtain a good dispersibility, and to obtain a higher coercive force.
- an iron-based oxidized substance such as hematite, magnetite, and goethite or a hydroxyl-based oxidized substance is used as a starting material.
- the average particle size of the raw material is a force to be selected in consideration of a volume change at the time of reduction / nitridation, usually about 5 'to 100 nm. ⁇
- a rare earth element is deposited on this starting material.
- the starting material is dispersed in an aqueous solution of an alkali or an acid, and the salt of the rare earth element is dissolved in the starting material.
- a hydroxide or hydrate containing the rare earth element is precipitated in the raw material powder by a neutralization reaction or the like. It should be done.
- the amount of the rare earth element is from 0.05 to 20 atomic%, preferably from 0.2 to 20 atomic%, more preferably from 0.5 to 15 atomic%, more preferably from 0.5 to 20 atomic%, based on the iron in the magnetic powder. 1.
- a compound composed of an element having an effect of preventing sintering, such as silicon and aluminum, is dissolved, and the raw material powder is immersed therein.
- the elements may be deposited simultaneously or sequentially.
- Additives such as a reducing agent, a pH buffer, and a particle size control agent may be mixed in order to carry out these deposition treatments efficiently. In these deposition processes, these elements may be deposited after the rare earth element has been deposited.
- the rare earth element or the raw material on which the rare earth element and other elements are deposited as necessary is reduced by heating in a hydrogen stream.
- the reducing gas is not particularly limited.
- a reducing gas such as carbon monoxide gas may be used.
- the rare earth-iron nitride based magnetic powder of the present invention is obtained.
- a gas containing ammonia In addition to ammonia gas alone, a mixed gas using hydrogen gas, helium gas, nitrogen gas, argon gas or the like as a carrier gas may be used. Nitrogen gas is particularly preferable because it is inexpensive.
- the nitriding temperature is preferably 100 to 300 ° C. If the nitriding temperature is too low, nitriding does not proceed sufficiently, and the effect of increasing the coercive force is small. If too high, nitride is excessively accelerated, increases the proportion of such F e 4 N and F e 3 N phase is rather decreased coercive force, - further pulling an excessive reduction of the saturation magnetization when Okose hungry.
- Rare-earth iron-boron magnetic powder mainly containing metallic iron or iron alloy in part of the core
- the heat-treated product is washed with water to remove excess boron, dried, and reduced by heating at 400 to 800 ° C. in a reducing atmosphere such as hydrogen to obtain a rare earth-iron-boron system.
- a magnetic powder is obtained.
- Other elements may be included to improve corrosion resistance and the like, but even in this case, the amount of rare earth and boron in the whole magnetic powder is 0.2 to 20 atomic% and 0.5 with respect to iron, respectively. It is desirably about 30 at%.
- an aqueous solution containing iron ions or, if necessary, transition metal ions such as Mn, Zn, Ni, Cu, and Co is mixed with an alkaline aqueous solution.
- a co-precipitate of iron or the above-mentioned transition metal is formed.
- iron sulfate or iron nitrate is used as a raw material for iron ions or transition metal ions.
- a rare earth salt such as neodymium or samarium and a boron compound are added to the coprecipitate, and the mixture is heated at 60 to 4 ° C. to obtain a rare earth containing boron and iron (or iron).
- Rare-earth iron-based magnetic powder mainly containing metallic iron or iron alloy in part of core The method for producing rare-earth iron-based magnetic powder mainly containing metallic iron or iron alloy in part of core is as follows. In other words, in an aqueous solution containing at least a rare-earth ion, spherical or elliptical particles such as magnetite or cobalt ferrite particles Are dispersed, and the alkali solution of the necessary number of moles to convert the rare earth ion into hydroxide is added to form a rare earth hydroxide on the surface layer of the magnetite or cobalt ferrite particles and then filtered. It has been found that the desired magnetic powder can be obtained by drying and reducing by heating.
- non-magnetic plate-like fine particles and the method for producing the same will be described in detail by taking plate-like alumina as an example.
- the present inventors have newly developed plate-like particles (fine particles) such as aluminum oxide particles satisfying the above requirements.
- plate-like particles such as aluminum oxide particles satisfying the above requirements.
- the desired shape and particle size are adjusted by the hydrothermal reaction treatment in which the heat treatment is performed in the temperature range of 0 ° C.
- the problem here is that the anoreminium hydroxide, which dissolves in both alkaline and acidic solutions and forms a precipitate only at near neutral pH, is a hydrate. It is a unique property. However, in order to form an aluminum hydroxide or hydrate having a desired shape and particle size by a hydrothermal reaction, it is necessary to use an alkaline solution. The present inventors have made intensive studies to overcome this property having a trade-off relationship, and as a result, have found that a target reaction proceeds only at a specific pH.
- the plate shape means a plate shape ratio (maximum diameter / thickness) of more than 1, preferably a plate shape ratio of more than 2 and 100 or less. Furthermore, 3 or more and 50 or less are more preferable, and 5 or more and 30 or less are more preferable. If the plate ratio is 2 or less, for example, when used in the undercoat layer, particles may rise from the application surface and may damage the head, guide, etc.If it exceeds 100, the particles will be broken during coating production May be done.
- the Young's modulus in the longitudinal direction is more preferably 0.65 to 0.75 in the Z width direction.
- the specific range of Young's modulus in the longitudinal direction / Young's modulus in the width direction of 0.60 to 0.80 is better if it is less than 0.60 or more than 0.80.
- the output variation (flatness) between the entry side and the exit side of the track of the magnetic head becomes large. This variation becomes minimum when the Young's modulus in the longitudinal direction and the Young's modulus in the Z width direction are around 0.70.
- the ratio of the Young's modulus in the longitudinal direction / Young's modulus in the width direction is preferably 0.70 to 1.30, although the reason is not clear.
- Non-magnetic supports satisfying such characteristics include a biaxially stretched aromatic polyamide base film and an aromatic polyimide film.
- carbon black may be added for the purpose of improving conductivity.
- the carbon black preferably has a particle diameter of 10 nm to 100 nm.
- conventionally known oxidized particles such as iron oxide and aluminum oxide may be added. In that case, it is preferable to use fine particles as much as possible.
- the same binder resin as the magnetic layer is used for the undercoat layer.
- the neodymium iron-boron magnetic powder obtained had a neodymium content of 2.4 atomic% with respect to iron and a boron content of 9.1 atomic% with respect to iron, as measured by X-ray fluorescence.
- Fig. 3 shows a transmission electron micrograph (250,000 times) of this neodymium iron-boron magnetic powder. As can be seen from this photograph, the magnetic powder was almost spherical or elliptical particles with an average particle size of 25 nm (axial ratio: 1.2).
- Plate-like alumina powder (average particle size: 50 nm) 10 parts Plate-like I T O powder (average particle size: 40 nm) 90 parts Stearic acid 2.0 parts Biel chloride-hydroxypropyl acrylate copolymer 8.8 ⁇
- Butyl stearate 1 part Silk mouth hexanone 70 parts Methinole ethyl ketone 50 parts Toluene 20 parts (3)
- Plate-like alumina powder (average particle size: 50 nm) 10 parts Plate-like ITO powder (average particle size: 40 nm) • 5 parts Methynoleic acid phosphate (MAP) '2 parts Tetrahydrofuran (THF) 20 parts Methynorethinole ketone Z cyclohexanone (MEK / A) 9 parts
- the kneading step components are preliminarily mixed at a high speed, the mixed powder is kneaded with a continuous twin-screw kneader, and (2) the dilution step component And dilute it in at least two or more stages using a continuous twin-screw kneader! /, And disperse it in a sand mill with a residence time of 45 minutes, add (3) the ingredients in the compounding process, stir and filter. , Magnetic paint.
- N-N counter magnet 5 kG was installed in front of the magnetic orientation treatment nozzle dryer, and two N-N counter magnets (5 kG) were placed in the dryer from 75 cm in front of the finger corrosion drying position of the coating film. The installation was performed at cm intervals. The coating speed was 100 minutes. ⁇ Paint component for back coat layer>
- Plate-like ITO powder (average particle size: 40 nm) 80 parts Carbon black (average particle size: 25 nm) 10 parts Plate-like iron oxide powder (average particle size: 5 Onm) 10 parts Ethrocellulose 45 parts Polyurethane resin (_S0 3 after dispersing the Na group-containing) 30 parts cyclohexanone 260 parts toluene 260 parts of methyl E chill ketone 525 parts the above backcoat layer coating material components to the consequent opening as residence time of 45 minutes in a sand mill, a polyisobutylene Xia sulfonate 1 5 parts added Then, a coating material for a back coat layer was prepared and filtered, and then applied to the opposite side of the magnetic layer of the magnetic sheet prepared above so that the thickness after drying and force rendering became 0.5 ⁇ , followed by drying.
- Example 2 A computer tape of Example 2 was produced in the same manner as in Example 1, except that the magnetic powder was changed to that of the following synthesis method. .
- the resultant was reduced by heating at 450 ° C. for 4 hours to obtain a neodymium iron-cobalt-boron magnetic powder. Then, it is cooled to room temperature with hydrogen gas flowing, switched to a nitrogen-Z oxygen mixed gas, and the temperature is raised again to 60 ° C, and stabilized for 8 hours in a nitrogen-Z oxygen mixed gas flow. After that, it was taken out into the air.
- the resulting neodymium iron-cobalt-boron magnetic powder had a neodymium content of 1.9 atoms with respect to iron as measured by X-ray fluorescence. / 0 , the content of cobalt with respect to iron was 40.1 atomic%, and the content of boron with respect to iron was 7.5 atomic%.
- this magnetic powder was almost spherical or elliptical particles, as in Example 1, and the average particle size was 20 nm. Also, 1 2 7 3.
- the saturation magnetization measured by applying a magnetic field of 3 kAZm was 19.7 / Wb / g (157 emu / g), and the coercive force was 174.3 kA / m (2190 Oe). there were.
- the magnetic powder was synthesized in the same manner as in Example 1, and the computer tape of Example 3 was produced in the same manner as in Example 1 except that the particle diameter was changed to 15 nm.
- Example 4 Among the components of the magnetic paint, 10 parts by weight of plate-like alumina powder (average particle size: 50 nm) and 5 parts by weight of plate-like ITO powder (average particle size: 40 nm) were added to granular alumina powder (average particle size: (80 nm) 10 parts by weight of carbon black (average particle size: 75 nm) A tape for a computer of Example 4 was produced in the same manner as in Example 1 except that the weight was changed to 2 parts by weight. .
- Example 5 80 parts by weight of 80 parts by weight of plate-like ITO powder (particle size: 40 nm) and 80 parts by weight of 10 parts by weight of carbon black (particle size: 25 nm) Iron oxide (particle diameter: 5 nm) 10 parts by weight was changed to 0 parts by weight, and carbon black (particle diameter: 0.35 zm) 10 parts by weight, granular iron oxide (particle diameter: 0 0.4 ⁇ )
- a computer tape of Example 5 was produced in the same manner as in Example 4, except that 10 parts by weight was added.
- a computer tape of Example 6 was produced in the same manner as in Example 1, except that the composition of the undercoat paint component of Example 1 was changed as follows.
- Polyester polyurethane resin (Containing one S 0 3 N a group: 0. 7x1 0 4 eq Z g) • Polyester polyurethane resin 4.4 parts
- Example 7 • The tape for a computer of Example 7 was prepared in the same manner as in Example 1 except that the composition of the undercoat paint component of Example 1 and ⁇ the paint component for the backcoat layer> were changed as described below. Was prepared.
- Carbon black (average particle size: 25 nm) 80 parts Carbon black (average particle diameter: 0.35 / m) 10 parts of granular iron oxide powder (average particle diameter: 50 nm) 10 parts Interview nitrocellulose 45 parts Polyurethane resin (S 0 3 N a 30 parts Cyclohexanone 260 parts Tonolen 260 parts Methylethyl ketone .525 parts Example 8
- Example 1 In synthesizing the ultrafine magnetic powder of Example 1, a rare earth mononitride magnetic powder was used instead of the neodymium iron-boron magnetic powder. An example using yttrium as the rare earth will be described below.
- the mixture was stirred for 20 minutes to generate magnetite particles.
- the magnetite particles were placed in an autoclave and heated at 200 ° C for 4 hours. After the hydrothermal treatment, it was washed with water.
- the magnetite particles were spherical or oval with a particle size of 25 nm.
- the magnetite particles (1 Og) were dispersed in 500 cc of water for 30 minutes using an ultrasonic disperser. Add 2.5 g of yttrium nitrate to this dispersion and dissolve
- the powder obtained by depositing the hydroxide of yttrium on the surface of the magnetite particles was heat-reduced at 450 ° C. for 2 hours in a hydrogen stream to obtain a yttrium-iron iron-based magnetic powder.
- the temperature was lowered to 150 ° C. over about one hour while flowing hydrogen gas.
- the gas was switched to ammonia gas, and nitriding was performed for 30 hours while maintaining the temperature at 150 ° C.
- the temperature was lowered from 150 ° C to 90 ° C with the ammonia gas flowing, and at 90 ° C, the gas was switched from the ammonia gas to a mixed gas of oxygen and nitrogen, and the stabilization treatment was performed for 2 hours.
- the temperature was lowered from 90 ° C to 40 ° C, and the temperature was kept at 40 ° C for about 10 hours, and then taken out into the air.
- the yttrium iron nitride-based magnetic powder thus obtained was measured for its yttrium and nitrogen contents by fluorescent X-ray to find that it was 5.3 atomic% and 10.8 atomic respectively. /. Met.
- a profile showing the Fe 16 N 2 phase was obtained from the X-ray diffraction pattern.
- Figure 4 is shows the X-ray diffraction patterns of the yttrium mononitride iron magnetic powder, a diffraction peak based on F e 1S N 2, a diffraction peak based on alpha-Fe is observed, this Ittoriumu It was found that the nitrided iron-based magnetic powder was composed of a mixed phase of Fe 16 N 2 phase and ⁇ -Fe phase.
- Figure 5 is a transmission electron micrograph (magnification: 200,000) of this magnetic powder.
- the specific surface area determined by the BET method was 53.2 m 2 Zg.
- the saturation magnetization of this magnetic powder measured by applying a magnetic field of 1,270 kA / m (16 kOe) was 135.2 Am 2 / kg (135.2 emuZg), and the coercive force was 226.9 k A / m (2, 85 OOe). Furthermore, after storing this magnetic powder at 60 ° C and 90% RH for one week, the saturation magnetization was measured in the same manner as described above. As a result, it became 11.2 Am 2 / kg (118.2 emu / g). The retention of saturation magnetization before storage was 87.4%.
- a magnetic paint was produced in the same manner as in Example 1 using the rare-earth iron-nitride-based magnetic powder produced as described above.
- the rare-earth iron mononitride-based magnetic powder used was prepared by scaling up the preparation method of the present example by 100 times.
- a computer tape was produced in the same manner as in Example 1 except that the composition of the lower layer was changed as shown in Table 1.
- Vinyl chloride-hydroxypropyl acrylate copolymer 14 parts (Contains S0 3 Na group: 0.7x10 " 4 equivalents / g)
- polyester polyurethane resin (PU) PU
- Potted iron oxide powder (average particle size: 100 nm, axial ratio 5). 68 parts Granular alumina powder (average particle size: 80 nm) 8 parts Carbon flag (average particle size: 25 nm) 24 parts Stearic acid 2 .0 part butyl chloride-hydroxypropyl acrylate copolymer 8.8U
- Polyester polyurethane resin 4.4 parts
- Carbon black (average particle size: 25 nm) 80 parts Carbon black (average particle size: 0.35 / zm) 10 parts Granular iron oxide powder (average particle size: 50 nm) 10 minutes
- Nitrocellulose 4 5 parts of the polyurethane resin (an S 0 3 N a group containing) 3 0 parts cyclohexanone 2 6 0 ⁇ toluene 2 6 0 parts of methyl E chill ketone-5 2 5 parts the method of evaluation cyclohexane was carried out as follows . .
- Scan Length was measured at 5 ⁇ by a scanning white light interferometry using a general-purpose three-dimensional surface structure angular analyzer, New York 500, manufactured by ZYGO.
- the measurement field of view is 350 / mx260 / zm.
- the center line average surface roughness of the magnetic layer was determined as Ra.
- Magnetic properties were measured using a vibrating magnetometer as in the case of magnetic powder.
- C value measured with an external magnetic field of 1273.3 kAZm. This is a corrected value when measuring 20% of magnetic recording media pasted together and punched to a diameter of 8 mm.
- the anisotropic magnetic field distribution is obtained by measuring the differential curve in the second quadrant (demagnetization curve) of the hysteresis curve of the tape, and dividing the magnetic field corresponding to the half-value width of this differential curve by the value of the coercive force of the tape.
- a hard ram tester was used to measure the electromagnetic conversion characteristics of the tape.
- the drum tester has an electromagnetic induction type head (track width 25 / im, gap 0.1 m) and an MR head (8 ⁇ ), recording was performed with an inductive head, and playback was performed with an MR head. Both heads are installed at different locations with respect to the rotating drum, and tracking can be adjusted by operating both heads up and down. An appropriate amount of the magnetic tape was drawn out of the state wound in the cartridge, discarded, discarded, 6 Ocm was cut out, further processed into a width of 4 and wound around the outer periphery of the rotating drum.
- a function generator wrote a square wave with a wavelength of 0.2 // m, and read the output of the MR head into a spectrum analyzer.
- the carrier value of 0.2 ⁇ m was defined as the medium output C.
- the integrated value of the value obtained by subtracting the output and system noise from the spectral component corresponding to the recording wavelength of 0.2 / m or more is used as the noise.
- the value N was used. Further, the ratio between the two was taken as C / N, and the relative value to the value of the comparative example 1 'tape used as a reference for both C C / N was determined.
- Thermal expansion coefficients are 20 ° C 60% RH and 4 ° C '60%. It was determined from the difference in sample length from RH. The coefficient of humidity expansion was determined from the difference in sample length between 20 ° C 30% ⁇ 1 and 20 ° 070 RH.
- the off-track amount was recorded using a modified LTO drive at a temperature of 20 ° C and a humidity of 45% RH (recording wavelength: 0,55 ⁇ ), and was recorded at a temperature of 20 ° C and a humidity of 45% RH. It was determined from the ratio of the reproduction output when reproducing at 35 ° C and a humidity of 70% RH.
- the recording head and the reproducing head those with track I widths of 20 ⁇ m and 12 ⁇ m were used, respectively.
- Table 1 summarizes the magnetic tape characteristics of Examples 1 to 8 and Comparative Example, and the conditions employed in each Example and Comparative Example.
- Example 1 Example 2
- Example 3 pit ⁇ Nd-Fe-B Nd-Fe-Co-B Nd-Fe-B Magnetic powder
- Granular iron oxide (0.4 ⁇ ) 1 ⁇ plate iron oxide (50nm) 10 10 10 plate ITO (40nm) 80 80 80 Magnetic layer thickness ( ⁇ ) 0.06 0.06 0.06 0.06 Undercoat layer thickness ( ⁇ ) 0.6 0.6 0.6 Support thickness ( ⁇ ) 3.3 3.3 3.3 3.3 3.3
- Example 4 Example 5
- Example 6 Elemental composition Nd-Fe-B Nd-Fe-B Nd-Fe-B Magnetic powder
- Plate-like iron oxide 50 nm
- Plate-like ITO 40 nm
- Magnetic layer thickness m 0.06 0.06 0.06
- Undercoat layer thickness Om 0.06 0.6 0.6
- the magnetic sheet was cut into 1Z7 inch width, assembled into a DDS cassette, and using a DDS drive (C1554A) in the same manner as in Examples 9 to 15 and Comparative Examples 2 to 5.
- the block error rate was measured.
- the computer magnetic tape (magnetic recording medium) having a total thickness of less than 6 / im using the rare-earth iron-based magnetic powder for the uppermost magnetic layer is the pot-like metal magnetic powder of Comparative Example 1 Compared with the computer tape used for the magnetic layer, it has better electromagnetic conversion characteristics (C, C / N).
- a computer magnetic tape (Example 8) using an essentially spherical or elliptical rare earth iron mononitride magnetic powder for the uppermost magnetic layer has excellent electromagnetic conversion characteristics (C, C / N).
- a linear recording type in which an essentially spherical or elliptical rare-earth iron-based magnetic powder containing a plate-shaped non-magnetic powder is used for the undercoat layer and the Z or back coat layer for the uppermost magnetic layer.
- Computer magnetic tapes have good humidity and temperature stability, so the amount of off-track is small even when the temperature and humidity change.
- the yttrium iron mononitride magnetic powder was found to have a content of 4.8 atomic% and 10.1 atomic%, respectively, as measured by X-ray fluorescence. Further, from the X-ray diffraction pattern to obtain a profile indicative of the presence of F e 16 N 2 phase.
- This indium iron nitride-based magnetic powder was 14.6 atomic% and 9.5 atomic%, respectively, when the contents of it and nitrogen were measured by X-ray fluorescence. / 0 . Further, from the X-ray diffraction pattern to obtain a profile indicative of the presence of F e 16 N 2 phase.
- This magnetic tape was incorporated into a DDS cartridge to produce a computer tape.
- the content of yttrium and nitrogen in the yttrium-iron nitride based magnetic powder was measured by X-ray fluorescence and found to be 5.3 atomic% and 6.2 atomic%, respectively. Further, a profile indicating the presence of the Fe 16 N 2 phase was obtained from the X-ray diffraction pattern.
- the yttriamu iron nitride-based magnetic powder was spherical or elliptical particles, and the average particle size was 20 nm.
- the specific surface area determined by the BET method is 50.
- This magnetic tape was assembled into a DDS cartridge to produce a computer tape.
- the product of the coercive force and the residual magnetic flux density and the thickness of the magnetic layer measured in the direction of orientation of the magnetic tape, Br ⁇ ⁇ , were 266.6 kA / iri and 0.022 ⁇ zTm, respectively.
- This yttrium iron nitride-based magnetic powder was found to have 5.1 atoms each when its yttrium and nitrogen contents were measured by X-ray fluorescence. / 0 and 15.1 atomic%. Further, from the X-ray diffraction pattern to obtain a profile indicative of the presence of F e 16 N 2 phase.
- the particles were spherical or elliptical with an average particle size of 21 nm.
- the specific surface area determined by the BET method was 54.6 m 2 / g.
- the saturation magnetization measured by applying a magnetic field of 1,270 kA / m (16 KOe) is 123.3 Am 2 / kg (123.3 emu / g), and the coercive force is 226.1 kA / m (2, 84 OOe).
- the saturation magnetization was measured in the same manner as above. 2 kg (105.2 emu / g), and the retention of saturation magnetization before storage is 85.
- Example 1 In the synthesis of the ultrafine magnetic powder of Example 1, an oxide consisting only of iron was produced without adding neodymium nitrate. In the same manner as in Example 1 to this Mizusani ⁇ , adding boric acid, a d the mixture to obtain a homogeneous mixture of hydroxides and boric acid iron heat treatment under the same conditions as in Example 1, Further washing with water was carried out to take out the boron-bonded iron oxide particles. The oxidized particles were heat-reduced under the same conditions as in Example 1 and further subjected to a stabilization treatment.
- spherical or elliptical magnetite particles having a particle size of 25 nm were heated and reduced at 400 ° C. for 2 hours in a hydrogen stream without performing the yttrium deposition treatment.
- a magnetic powder was obtained.
- the temperature was lowered to 90 ° C, switched to a mixed gas of oxygen and nitrogen, and stabilized for 2 hours.
- the temperature was lowered to ° C, kept at 40 ° C for about 10 hours, and then taken out into the air.
- Observation of the shape of the magnetic powder thus obtained with a high-resolution analytical transmission electron microscope revealed spherical or elliptical particles having an average particle size of 0 ⁇ m.
- the specific surface area determined by the BET method was 15.6 m2 / g.
- 1, 2 7 ⁇ k A / m (1 6 kOe) saturation magnetization was measured by applying a magnetic field of 1 9 5.
- 2 e mu / g) the coercive force was 49.4 kA / m (62 OOe).
- the magnetic powder produced as described above was further scaled up by a factor of 100 to produce a magnetic paint, in the same manner as in Example 1.
- a magnetic paint Using this magnetic paint, an attempt was made to produce a magnetic tape having a magnetic layer having a thickness of 0.06 / zm in the same manner as in Example 9, but the thickness of the magnetic layer varied greatly. It has not been possible to produce a magnetic tape having a uniform magnetic layer thickness.
- the coercive force and the product of the residual magnetic flux density and the thickness of the magnetic layer, Br and ⁇ , measured in the orientation direction were also measured for this magnetic tape, and the measured values were 66.7 kA / m and 0. It was 024 ⁇ Tm.
- the content of nitrogen in the magnetic powder was measured by X-ray fluorescence, was 8.9 atom 0/0. Observation with a high-resolution analytical transmission electron microscope revealed that the particles were spherical or elliptical with a particle size of 75 nm.
- the specific surface area determined by the BET method was 14.9 m2 / g.
- X-ray diffraction pattern to obtain a profile indicating a F e 16 N 2 phase.
- the saturation magnetic field measured by applying a magnetic field of 1 2 7 3.9 A / m (l 6 kOe) is 18.6.4 A m 2 / kg (18.6.4 em uZ g), the coercive force was 183.1 kA / m-(2300 Oe).
- the production conditions of the magnetic powders of Examples 8 to 13 and Comparative Examples 2 to 4 are shown in Table 2. Further, the elemental composition (atomic% of rare earth element and nitrogen), the presence or absence of Fe 16 N 2 phase, the average particle size and the BET specific surface area of each magnetic powder of Examples 8 to 13 and Comparative Examples 2 to 4 were determined. Table 3 summarizes the results. Further, Table 4 summarizes the saturation magnetization, coercive force, and storage stability (saturation magnetization and retention after storage) of each of the magnetic powders of Examples 8 to 13 and Comparative Examples 2 to 4. ⁇
- Example 1 the yttrium iron mononitride-based magnetic powder shown in Example 8 as a magnetic powder (coercive force: 226.9 kA / m, saturation magnetization: 135.2 Am 2 / kg, particle size: 20 nm, particle shape:
- a magnetic paint was prepared in the same manner as in Example 1 using a spherical or elliptical shape, and the magnetic paint was subjected to a magnetic field orientation treatment, drying, and calendaring.
- the thickness of the magnetic layer after the calendering treatment was set to be 0.06 / 111 to 0.08 / m in Example 1. Further, the same plate-like oxide particles as those described in Example 1 such as plate-like alumina and plate-like ITO were used.
- Example 1 the yttrium-iron-nitride-based magnetic powder shown in Example 9 as the magnetic powder (coercive force: 211. Ok AZm, saturation magnetic field: 130.5 Am 2 / kg, particle size: 17 nm) , Particle shape: spherical or elliptical) Then, a magnetic paint was prepared, and the magnetic paint was subjected to magnetic field orientation treatment, drying, and calendaring. The thickness of the magnetic layer after the calendering treatment was set to be 0.08 m from 0.06 / 111 in Example 1. Further, the same plate-like oxide particles as those described in Example 1 such as plate-like alumina and plate-like ITO were used.
- Example 9 Each of the paints was applied in the same manner as in Example 1 using the magnetic paint, the undercoat paint, and the paint for the back coat layer thus produced, and a magnetic tape was produced under the same conditions as in Example 9.
- This magnetic tape was assembled into a DDS cartridge to produce a computer tape.
- the product of the coercive force and residual magnetic flux density and the thickness of the magnetic layer measured in the magnetic tape orientation direction, Br ⁇ ⁇ , were 280.6 kA / m and 0.024 ⁇ Tm, respectively.
- the product of the coercive force, the residual magnetic flux density and the thickness of the magnetic layer measured in the direction of orientation of the magnetic tape, Br ⁇ ⁇ , were 20.8 kA / m and 0.017 / z Tm, respectively.
- the magnetic properties of the magnetic tapes of Examples 9 to 15 and Comparative Examples 2 to 5 were as follows: coercive force (He), saturation magnetic flux density (Bm), squareness ratio (BrZBm), and anisotropic magnetic field.
- the distribution (Ha) was measured.
- the anisotropic magnetic field distribution is obtained by measuring the differential curve in the second quadrant (demagnetization curve) of the hysteresis curve of the tape, and dividing the magnetic field corresponding to the half-value width of this differential curve by the value of the coercive force of the tape. Indicated by In other words, the smaller the coercive force distribution of the magnetic powder, the smaller the dispersion of the magnetic powder in the tape and the better the orientation, the smaller the Ha becomes. Has good recording characteristics.
- the rare-earth iron-nitride magnetic powder of the present invention produced in Examples 8 to 13 has a thin magnetic layer thickness of 0.09 m or less. It can be seen that the particles have an essentially spherical or elliptical particle shape optimal for a magnetic recording medium and a particle size of 5 to 50 nm. Also such a spherical! Despite its elliptical shape, it has high coercive force and moderate saturation magnetization suitable for high-density recording, and at the same time has excellent storage stability of saturation magnetization. Understand.
- the rare earth iron mononitride-based magnetic powder of the present invention has a high magnetic anomaly even though it is spherical when used as a magnetic recording medium. Due to anisotropy, it shows excellent magnetic field orientation. Furthermore, the magnetic recording medium of the present invention shows an excellent anisotropic magnetic field distribution, which reflects the sharp coercive force distribution of the magnetic powder of the present invention. / Such small and / or anisotropic magnetic field distribution results in a smaller block error rate, which is an electromagnetic conversion characteristic, and results in a magnetic tape with better reliability.
- the excellent characteristics of the magnetic recording medium of the present invention as such a high-density recording medium are as follows.
- a rare earth-nitride-based magnetic powder containing iron nitride having a composition represented by Fe 16 N 2 was used as the magnetic powder. Sometimes it appears more prominently.
- the magnetic powders of Comparative Examples 2 to 4 have a shape close to spherical, but the particle size is as large as 50 nm or more, so that the magnetic layer thickness is essentially 0.09 ⁇ m or less. It cannot be used for magnetic recording media with Further, since the magnetic powders of Comparative Examples 2 and 3 do not contain a rare earth element, the coercive force is significantly smaller than that of the magnetic powder of the present invention.
- the magnetic powder of Comparative Example 4 can obtain a relatively high coercive force by using iron nitride.However, since it does not contain a rare earth element, it has a particle size of 5 to 50 nm suitable for high-density magnetic recording media. Replying to @Samsung
- the rare-earth iron-based magnetic powders shown in the examples have a high coercive force based on the uniaxial crystal magnetic anisotropy while having a spherical or elliptical shape, and are extremely fine particles. Despite the fact, it has the optimum saturation magnetization for high density recording.
- the rare-earth iron-based magnetic powder which contains iron nitride having a composition represented by Fe 16 N 2 , exhibits a higher coercive force, and exhibits a higher coercive force. It is optimal as a magnetic powder for high-density recording media.
- a computer magnetic tape of linear recording has a magnetic recording medium having excellent electromagnetic conversion characteristics (C, C / N) and excellent temperature and humidity stability.
- C, C / N electromagnetic conversion characteristics
- a magnetic recording medium and a magnetic recording cartridge for a computer or the like that can cope with a recording capacity of, for example, 1 TB or more.
- a backup taper for a computer or the like which has an excellent block rate and can cope with a high recording capacity, can be provided.
Description
Claims
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GB0421624A GB2403587B (en) | 2002-03-18 | 2003-02-21 | Magnetic recording medium and magnetic recording cartridge |
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Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
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JP2006216178A (ja) * | 2005-02-04 | 2006-08-17 | Hitachi Maxell Ltd | 磁気テープ |
JP2006331557A (ja) * | 2005-05-27 | 2006-12-07 | Hitachi Maxell Ltd | 磁気記録媒体 |
US7241501B2 (en) | 2003-11-27 | 2007-07-10 | Dowa Mining Co., Ltd. | Iron nitride magnetic powder and method of producing the powder |
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- 2003-03-18 GB GB0421623A patent/GB2403059B/en not_active Expired - Fee Related
-
2007
- 2007-03-19 US US11/688,179 patent/US7445858B2/en not_active Expired - Fee Related
- 2007-06-21 US US11/766,491 patent/US20080107921A1/en not_active Abandoned
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US7700204B2 (en) * | 2003-02-19 | 2010-04-20 | Hitachi Maxell, Ltd. | Magnetic recording medium containing particles with a core containing a FE16N2 phase |
US7241501B2 (en) | 2003-11-27 | 2007-07-10 | Dowa Mining Co., Ltd. | Iron nitride magnetic powder and method of producing the powder |
JP2006216178A (ja) * | 2005-02-04 | 2006-08-17 | Hitachi Maxell Ltd | 磁気テープ |
JP2006331557A (ja) * | 2005-05-27 | 2006-12-07 | Hitachi Maxell Ltd | 磁気記録媒体 |
JP2009259402A (ja) * | 2009-08-11 | 2009-11-05 | Hitachi Maxell Ltd | 磁気記録媒体および磁気テープカートリッジ |
CN104969308A (zh) * | 2013-02-06 | 2015-10-07 | 日清制粉集团本社股份有限公司 | 磁性粒子的制造方法、磁性粒子及磁性体 |
CN104969308B (zh) * | 2013-02-06 | 2018-04-03 | 日清制粉集团本社股份有限公司 | 磁性粒子的制造方法、磁性粒子及磁性体 |
Also Published As
Publication number | Publication date |
---|---|
GB2403059A (en) | 2004-12-22 |
AU2003211248A1 (en) | 2003-09-29 |
US20080107921A1 (en) | 2008-05-08 |
GB2403587B (en) | 2005-08-03 |
GB0421623D0 (en) | 2004-10-27 |
GB2403587A (en) | 2005-01-05 |
JP3886968B2 (ja) | 2007-02-28 |
GB2403059B (en) | 2005-07-27 |
US7291409B2 (en) | 2007-11-06 |
US20070159722A1 (en) | 2007-07-12 |
US20050276999A1 (en) | 2005-12-15 |
JP3886969B2 (ja) | 2007-02-28 |
JPWO2003079333A1 (ja) | 2005-07-21 |
US7445858B2 (en) | 2008-11-04 |
AU2003221416A1 (en) | 2003-09-29 |
US7267896B2 (en) | 2007-09-11 |
WO2003079333A1 (en) | 2003-09-25 |
US20040089564A1 (en) | 2004-05-13 |
GB0421624D0 (en) | 2004-10-27 |
JPWO2003079332A1 (ja) | 2005-07-21 |
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