US20070042230A1 - Magnetic powder suitable for low-noise media - Google Patents

Magnetic powder suitable for low-noise media Download PDF

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US20070042230A1
US20070042230A1 US11/494,550 US49455006A US2007042230A1 US 20070042230 A1 US20070042230 A1 US 20070042230A1 US 49455006 A US49455006 A US 49455006A US 2007042230 A1 US2007042230 A1 US 2007042230A1
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magnetic
magnetic powder
noble metal
powder
iron
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Kenji Masada
Yuzo Ishikawa
Hiroshi Kimura
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Dowa Electronics Materials Co Ltd
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Dowa Holdings Co Ltd
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Publication of US20070042230A1 publication Critical patent/US20070042230A1/en
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Priority to US12/986,198 priority Critical patent/US8110048B2/en
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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
    • H01F1/06—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 in the form of particles, e.g. powder
    • H01F1/065—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 in the form of particles, e.g. powder obtained by a reduction
    • 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
    • G11B5/68—Record carriers characterised by the selection of the material comprising one or more layers of magnetisable material homogeneously mixed with a bonding agent
    • G11B5/70—Record carriers characterised by the selection of the material comprising one or more layers of magnetisable material homogeneously mixed with a bonding agent on a base layer
    • G11B5/706—Record carriers characterised by the selection of the material comprising one or more layers of magnetisable material homogeneously mixed with a bonding agent on a base layer characterised by the composition of the magnetic material
    • G11B5/70605—Record carriers characterised by the selection of the material comprising one or more layers of magnetisable material homogeneously mixed with a bonding agent on a base layer characterised by the composition of the magnetic material metals or alloys
    • G11B5/70615—Record carriers characterised by the selection of the material comprising one or more layers of magnetisable material homogeneously mixed with a bonding agent on a base layer characterised by the composition of the magnetic material metals or alloys containing Fe metal or alloys
    • 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
    • G11B5/68—Record carriers characterised by the selection of the material comprising one or more layers of magnetisable material homogeneously mixed with a bonding agent
    • G11B5/70—Record carriers characterised by the selection of the material comprising one or more layers of magnetisable material homogeneously mixed with a bonding agent on a base layer
    • G11B5/706—Record carriers characterised by the selection of the material comprising one or more layers of magnetisable material homogeneously mixed with a bonding agent on a base layer characterised by the composition of the magnetic material
    • G11B5/70626—Record carriers characterised by the selection of the material comprising one or more layers of magnetisable material homogeneously mixed with a bonding agent on a base layer characterised by the composition of the magnetic material containing non-metallic substances
    • 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
    • G11B5/68—Record carriers characterised by the selection of the material comprising one or more layers of magnetisable material homogeneously mixed with a bonding agent
    • G11B5/70—Record carriers characterised by the selection of the material comprising one or more layers of magnetisable material homogeneously mixed with a bonding agent on a base layer
    • G11B5/714—Record carriers characterised by the selection of the material comprising one or more layers of magnetisable material homogeneously mixed with a bonding agent on a base layer characterised by the dimension of the magnetic particles

Definitions

  • This invention relates to an iron system magnetic powder for use in high recording density magnetic recording media, particularly to a magnetic powder composed of fine particles that enables production of magnetic recording tape exhibiting outstanding low-noise and high C/N (carrier-to noise) properties.
  • the particles get smaller, it becomes more and more difficult for the particles to continue to exist as independent particles.
  • extreme refinement of the particle size makes the powder susceptible to sintering during the reduction stage of the production process. Sintering increases the average particle volume, which is undesirable because the larger sintered particles become a source of noise, and also degrades the magnetic properties of the powder by deforming the particle shape.
  • the powder is used to produce magnetic tape, the enlarged particles degrade dispersibility and cause loss of surface smoothness.
  • the magnetic powder therefore becomes unsuitable for use in high recording density media. While a magnetic powder needs to have good magnetic properties to be suitable for a high-density recording medium, it also has to exhibit good powder properties during the tape manufacturing process, such as dispersibility, average particle volume, particle size distribution, specific surface area, tap density and so forth.
  • JP 2000-6147A (Ref. 1), which is a ferromagnetic metal powder whose properties include: major axis length of 30-120 nm, axial ratio of 3-8, Hc of 79.6 ⁇ 318.5 kA/m(1,000-4,000 Oe), and ⁇ s of 100 ⁇ 180 Am 2 /kg(100-180 emu/g).
  • JP 10-69629A (Ref. 2) teaches a magnetic powder for achieving superior magnetic properties of a high quality that is composed of Fe containing 5-50 at. % of Co, 0.1-30 at. % of Al, 0.1-10 at. % of rare earth elements (defined to include Y), not more than 0.05 wt % of Periodic Table group 1a elements and not more than 0.1 wt % of Periodic Table group 2a elements and has Hc of 95.5 ⁇ 238.8 kA/m(1,200-3,000 Oe) and as of 100 ⁇ 200 Am 2 /kg (100-200 emu/g).
  • WO 03/079333A1 (pamphlet; Ref. 4) teaches a rare earth element-iron nitride system magnetic powder composed of substantially spherical or ellipsoid particles and states that, despite being composed of fine particles of around 20 nm (average particle volume of 4,187 nm 3 ), the rare earth element-iron nitride system magnetic powder having Fe 16 N 2 as its main phase has a high coercive force of 200 kA/m (2,512 Oe) or greater and high saturation magnetization owing to its small BET specific surface area, so that the recording density of a coated-type magnetic recording medium can be dramatically enhanced by using the rare earth element-iron nitride system magnetic powder.
  • a high C/N is indispensable to the realization of high recording density, i.e., a tape is required that is low in noise (N) and high in output (C).
  • N noise
  • C high in output
  • a magnetic powder small in particle volume and excellent in magnetic properties is preferable for producing such a medium.
  • advances in magnetic head technology have led to the development of GMR and other high-sensitivity heads capable of reading data recorded at low magnetization.
  • the particle size of metal magnetic powders currently used in practical applications is around 45-60 nm (average particle volume: 5,000-8,000 nm 3 ).
  • the average particle volume required by a low-noise medium is 4,000 nm 3 or less, preferably 3,000 nm 3 or less, but no practical magnetic powder of such adequately small average particle volume has yet been developed.
  • Sintering is prevented chiefly by 1) changing the composition of the starting powder (increasing the amount of sintering inhibitor used) and 2) lowering the reduction temperature to which the metallic iron is exposed.
  • the first method of increasing the amount of nonmagnetic sintering inhibitor is undesirable because it increases noise by reducing the number of magnetic particles per unit volume.
  • the second method is undesirable because lowering the reduction temperature not only has the desired effect of reducing sintering but also simultaneously lowers the particle reduction rate, which leads to problems such as that the proportion of the grain boundary rises because crystal grain growth within the particles is inhibited and the magnetic properties are markedly degraded by the occurrence of magnetic poles and the like owing to increased irregularity of the particle surfaces.
  • This invention was accomplished in the light of these circumstances and is directed to achieving strong prevention of sintering during reduction without causing the aforesaid problems and, by this, to provide a magnetic powder that enables the design of low-noise, high-output, high C/N, high recording density media suitable for use with GMR and other high-sensitivity heads.
  • the inventors conducted detailed experiments with regard to starting powder composition and reduction conditions in order to achieve the aforesaid object. As a result, it was found that a magnetic powder which is excellent in magnetic properties and provides a low-noise medium when used in tape production can be obtained by, at the time of starting powder preparation, incorporating one or more noble metal elements in the starting powder in the form of solid solution or coating, reducing the result under suitable conditions and optionally nitriding the reduced powder, thereby strongly preventing sintering during the reduction.
  • this invention provides an iron system magnetic powder particularly, a magnetic powder comprised chiefly of Fe 16 N 2, wherein the powder contains a noble metal in an amount that the atomic ratio of total noble metal content to Fe is 0.01-10%.
  • the atomic ratio of element X (noble metal) to Fe means the ratio of the amount of element X contained in the powder to the amount of Fe contained therein expressed in atomic per cent. The ratio is calculated from the X amount (at. %) and the Fe amount (at. %) determined by quantitative analysis of the powder as 100 ⁇ (X amount [at. %])/(Fe amount [at. %]).
  • constituting element X is meant that element X was detected in quantitative analysis of the powder.
  • the form in which the element X is present can be in solid solution in the magnetic phase or as adhered to the particle surfaces.
  • the iron system magnetic powder of this invention is a magnetic powder composed chiefly of Fe and may, for instance, be ⁇ Fe, an alloy of Fe and Co (hereinafter called “Fe+Co alloy”), iron nitride (particularly one composed chiefly of Fe 16 N 2 ), or the result obtained by subjecting any of these to oxidation treatment.
  • the iron system magnetic powder preferably exhibits powder magnetic properties of coercive force of 160 kA/m or greater, more preferably 180 kA/m or greater, and saturation magnetization as of 40 kA 2 /kg or greater.
  • noble metal elements are Au, Ag and platinum group elements which include Ru, Rh, Pd, Os, Ir and Pt.
  • Elements other than the main constituent Fe that can be contained include, in addition to noble metals, N and Co for incorporation in the magnetic phase and, as elements known to provide sinter inhibiting effect, Al or rare earth elements (defined to include Y).
  • the so-constituted magnetic powder can be produced by passing iron oxy-hydroxide or iron oxide containing noble metal at an atomic ratio of total noble metal content to Fe of 0.01-10% through a reduction process.
  • the magnetic powder is preferably provided as one having average particle volume V of 4,000 nm 3 or less, more preferably 3,000 nm 3 or less.
  • This invention provides an iron system magnetic powder obtained by a process that strongly inhibits sintering during reduction treatment at the time of production.
  • this magnetic powder is compared with a magnetic powder refined by addition of a large amount of Al or other element known to exhibit sinter inhibiting effect (hereinafter called “conventional sinter inhibiting element”), it is found to exhibit markedly improved Hc and as even at the same level of average particle volume.
  • the magnetic powder of the invention achieves a higher degree of particle refinement at the same level of conventional sinter inhibiting element addition.
  • magnetic recording media produced using the refined magnetic powder of the invention in the magnetic layer were found to exhibit pronounced noise reduction effect. This invention can therefore be expected to enable a great improvement in the recording density of magnetic recording media and help to improve the performance of electronic equipment equipped with such media.
  • FIG. 1 is a graph plotted to show the relationship between Hc and average particle volume of the magnetic powders of Examples 1-4 and Comparative Examples 1 and 2.
  • FIG. 2 a graph plotted to show the relationship between ⁇ s and average particle volume of the magnetic powders of Examples 1-4 and Comparative Examples 1 and 2.
  • the iron system magnetic powder of this invention is obtained by a process in which sintering during the reduction treatment is strongly inhibited by including noble metal in the starting powder prior to the stage of reduction treatment.
  • Al, rare earth elements (defined to include Y) and other conventional sinter inhibiting elements basically show no effect of substantially reducing reduction starting temperature. These conventional elements are therefore distinguished from the noble metals used in this invention in that they differ fundamentally in their effect. In this invention, good effect can be realized by concurrent use of Al, rare earth elements including Y and other conventional sinter inhibiting elements.
  • Noble metal elements usable in the invention include Au, Ag, Ru, Rh, Pd, Os, Ir and Pt. These elements work to lower the temperature at which reduction of the starting powder (iron oxy-hydroxide or iron oxide) commences.
  • the amount of added noble metal elements in the starting powder before reduction is preferably such that the atomic ratio of total added noble metal content to Fe in the final magnetic powder becomes 0.01-10%, more preferably 0.01-1.0%.
  • the amount added at this stage (at. % with respect to Fe) is approximately reflected in the noble metal content (at. % with respect to Fe) of the final magnetic powder. Either elemental or compound noble metal can be used.
  • magnetic powder composed chiefly of Fe 16 N 2 it suffices to subject the reduced powder to nitriding treatment.
  • noble metal-containing is defined to include the case where noble metal is present (in solid solution) in the starting powder particles, the case where it is present as adhered to the particle surfaces, and the case where it is present in both forms.
  • the noble metal-containing iron oxy-hydroxide in which noble metal is present in solid solution in the particles is prepared by entraining noble metal in the iron oxy-hydroxide production reaction when synthesizing iron oxy-hydroxide by the wet method.
  • a ferrous salt solution aqueous solution of FeSO 4 , FeCl 2 or the like
  • an alkali hydroxide aqueous solution of NaOH or KOH
  • the desired oxy-hydroxide containing noble metal present as dissolved state in the particles can be obtained by conducting the iron oxy-hydroxide production reaction in the presence of a nitrate or chloride of the noble metal.
  • Another method that can be used is to conduct a reaction for producing iron oxy-hydroxide by neutralizing a ferric salt (aqueous solution of FeCl 3 or the like) with NaOH or the like, again in the presence of a nitrate or chloride of the noble metal.
  • a ferric salt aqueous solution of FeCl 3 or the like
  • Another method that can used to incorporate noble metal is to produce the iron oxy-hydroxide first and then coat its particle surfaces with the noble metal.
  • the aforesaid method of synthesizing iron oxy-hydroxide is carried out to produce iron oxy-hydroxide without conducting an operation for incorporating noble metal in solid solution.
  • Inclusion of solid solution Al is optional.
  • a noble metal nitrate or chloride and an Al-containing salt are added to a dispersed solution of the iron oxy-hydroxide and the particle surfaces are coated with the noble metal by the method of neutralization with an alkali or the method of evaporating off water from the dispersion. If desired, this coating operation can be conducted after noble metal has been dissolved into the particles in solid solution. It is also possible to deposit noble metal on the iron oxy-hydroxide particle surfaces by shining light from a mercury lamp or the like onto the particles to conduct photoreduction.
  • Coating with Al, rare earth elements (defined to include Y) and other conventional sinter inhibiting elements can be performed together with the noble metal coating. This can be achieved by adding an aqueous solution of a water-soluble Al salt, rare earth elements, yttrium and so forth.
  • Compounds usable as the aforesaid noble metal nitrate and chloride include platinic chloride hexahydrate, palladium nitrate, palladium chloride, rhodium nitrate, rhodium chloride, ruthenium chloride, iridium chloride, osmium chloride, gold chloride tetrahydrate, and silver nitrate.
  • Al-containing salt that is the source of Al can be used, for example, water-soluble Al salt or aluminate.
  • the Co-containing salt that is the source of Co can be used, for example, cobalt sulfate or cobalt nitrate.
  • the rare earth elements and yttrium can be used sulfates or nitrates of the corresponding elements.
  • the amount of added noble metal is preferably such that the atomic ratio of the noble metal content to Fe in the magnetic powder becomes 0.01-10%.
  • An atomic ratio of 0.01-1.0% is particularly preferable.
  • the total amount thereof is made to fall within these ranges.
  • the atomic ratio of noble metal to Fe is less than 0.01%, the effect of reducing reduction temperature sometimes cannot be stably obtained.
  • the atomic ratio of the noble metal content to Fe is greater than 10%, the proportion of nonmagnetic content increases. This makes it impossible to obtain good magnetic properties.
  • most noble metals are expensive, so that increasing the amount used adds to the cost of magnetic powder production.
  • the most realistic range of the atomic ratio of the noble metal content to Fe is therefore 0.01-1.0%, within which a strong reduction temperature decreasing effect can be obtained.
  • the so-obtained iron oxy-hydroxide containing noble metal is passed through filtering and water-washing processes and then dried at a temperature not higher than 200° C. to obtain a usable starting powder.
  • the iron oxy-hydroxide can be subjected to a dewatering treatment at 200-600° C. or a reduction treatment in a hydrogen atmosphere of 5-20% water concentration, thereby converting the iron oxy-hydroxide particles to modified iron oxide particles that can be used as the starting material.
  • the starting powder is required to be a compound containing iron, oxygen and hydrogen, it is otherwise not particularly limited and may, for example, be goethite, hematite, magnetite or wustite. In this specification, such an oxy-hydroxide or oxide of iron is called a “starting powder.”
  • the starting powder is reduced to ⁇ Fe or Fe+Co alloy.
  • the dry method employing hydrogen (H 2 ) is generally applied for the reduction treatment, and can be conducted a temperature of 250-500° C.
  • a temperature of 250-400° C. is particularly preferable because, owing to the addition of noble metal, the reduction rate does not decrease appreciably even if the reduction temperature is lowered.
  • the reduction temperature is lower than 250° C., the reduction may be insufficient, in which case the magnetic properties are markedly degraded.
  • the nitriding speed becomes extremely slow.
  • An excessively high reduction temperature is undesirable because the particles tend to experience shape deterioration and inter-particle sintering even when a conventional sinter inhibiting element such as Al is incorporated as a countermeasure, so that the average particle volume increases and dispersibility declines.
  • the best effect is therefore realized in a temperature range not exceeding 400° C.
  • the temperature can be raised to implement multi-stage reduction for enhancing crystallinity.
  • the ammonia method set out in JP 11-340023A can be utilized. This method enables production of iron nitride powder composed chiefly of Fe 16 N 2 by keeping the reduced powder in a stream of nitrogen-containing gas, typically ammonia, at a temperature of not higher than 200° C. for several tens of hours.
  • the oxygen content of the gas used in the nitriding treatment is preferably several ppm or less.
  • the nitriding treatment temperature, time and atmosphere should be controlled to make the atomic ratio of the N content of the magnetic powder to Fe 5-30%, more preferably about 10-30%.
  • the N/Fe atomic ratio is less than 5%, the nitriding effect of enhancing magnetocrystalline anisotropy to realize good magnetic properties is not exhibited to a sufficient degree.
  • the atomic ratio exceeds 30%, excessive nitriding occurs to degrade the magnetic properties by producing phases other than the desired Fe 16 N 2 .
  • the amount of Fe in the magnetic powder was determined using a COMTIME-980 Hiranuma Automatic Titrator manufactured by Hiranuma Sangyo Co., Ltd.
  • the amounts of Al, rare earth elements (defined as including Y), Pt, Pd, Rh, Ru, Ir, Os, Au, Ag and Cu in the magnetic powder were determined using an IRIS/AP High-resolution Inductively Coupled Plasma Atomic Emittion Spectrometer manufactured by Nippon Jarrell-Ash. These determinations were in mass percentages, which were converted to the atomic percentages of the elements, from which the atomic ratio of element X to Fe (X/Fe atomic ratio) was calculated.
  • Magnetic properties (coercive force Hc, saturation magnetization as, and squareness ratio SQ): A vibrating sample magnetometer (VSM) manufactured by Digital Measurement Systems Corp. was used to perform the measurements in an externally applied magnetic field of max. 796 kA/m.
  • VSM vibrating sample magnetometer
  • the solid component was separated from the liquid by filtering, washed with water and dried in air at 110° C.
  • This powder was, as a starting material, reduced in hydrogen gas at 350° C. for 0.5 hour (reduction stage 1). Next, it was heated in the hydrogen gas to 650° C. and held at this temperature for 0.5 hour (reduction stage 2). It was then cooled to 100° C., at which temperature the gas was changed from hydrogen to ammonia, and thereafter heated to 127° C.
  • Nitriding was conducted for 20 hours at this temperature in the ammonia gas. After the nitriding treatment, the temperature was lowered to 70° C. and the gas was changed to nitrogen gas to which was then added an amount of air so as to impart an O 2 concentration of 0.01-2% and subject the surface of the powder to slow oxidation. The powder was then taken out into the air.
  • the obtained powder was found by X-ray diffraction analysis to be a magnetic powder composed chiefly of Fe 16 N 2 (also in Examples 2 to 4 and Comparative Examples 1 and 2) and to be composed of elliptical particles.
  • the composition, average particle volume, magnetic properties and the like of this mainly Fe 16 N 2 magnetic powder are shown in Table 1.
  • Example 1 was repeated except that the amount of Ru added as a noble metal was changed to 0.5 at. %.
  • the properties of this mainly Fe 16 N 2 magnetic powder are shown in Table 1.
  • the properties of this mainly Fe 16 N 2 magnetic powder are shown in Table 1.
  • Example 1 was repeated except that element added as the noble metal was changed to Pd and the amount added was changed to 1.0 at. %.
  • the properties of this mainly Fe 16 N 2 magnetic powder are shown in Table 1.
  • Example 1 was repeated except that no noble metal was added and the stage 1 reduction temperature was changed to 450° C.
  • the properties of this mainly Fe 16 N 2 magnetic powder are shown in Table 1.
  • the solid component was separated from the liquid by filtering, washed with water and dried in air at 110° C., and then the powder obtained was subjected to the same reduction process as Example 1.
  • the properties of this mainly Fe 16 N 2 magnetic powder are shown in Table 1.
  • TABLE 1 Bulk properties Composition Ave Reduction promoter Reduction conditions Nitriding parti- element Stage 1 Stage 1 Stage 2 Stage 2 conditions cle Hc ⁇ s Added Al Y N temp time temp time Temp Time vol BET kA/ kA 2 / Element as At. % At. % At. % At. % At. % ° C. hr ° C. hr ° C.
  • the magnetic powders of the Examples produced by subjecting a starting powder containing a prescribed amount of noble metal to reduction treatment at a low reduction temperature of 350° C. were obtained as fine magnetic powders having an average particle volume of not greater than 4,000 nm 3 . Moreover, owing to the high degree to which they were reduced, the magnetic powders exhibited excellent magnetic properties, namely, Hc of 160 kA/m or greater and ⁇ s of 40 kA 2 /kg or greater.
  • the average particle volume of the magnet powder of Comparative Example 1 came to exceed 4,000 nm 3 because the absence of noble metal in the starting powder prior to reduction and the use of the ordinary reduction temperature of 450° C. made adequate sinter prevention impossible.
  • Comparative Example 2 even though no noble metal was included in the starting powder prior to reduction and the ordinary reduction temperature of 450° C. was used, a passably small average particle volume was nevertheless achieved thanks to the inclusion of a large amount of the conventional sinter inhibiting element of Al.
  • the magnetic powder of Comparative Example 2 did not enable fabrication of a magnetic recording medium exhibiting the excellent properties obtainable using an invention magnetic powder.
  • the iron nitride system magnetic powder of Example 1 was used to fabricate a magnetic tape of double-layer structure including a magnetic layer and a nonmagnetic layer and the electromagnetic conversion characteristics of the tape were evaluated.
  • the magnetic coating fluid was prepared by blending 100 parts by mass of the magnetic powder with the other components set out below in the indicated number of parts by mass.
  • the nonmagnetic coating fluid was prepared by blending 80 parts by mass of nonmagnetic powder with the other components set out below in the indicated parts by mass. Each mixture was kneaded and dispersed to obtain a coating fluid using a kneader and a sand grinder.
  • the coating fluid for forming the magnetic layer and the coating fluid for forming the nonmagnetic layer (underlayer) were applied onto a base film composed of an aramid support to obtain the desired underlayer thickness of 2.0 ⁇ m and magnetic layer thickness of 0.10 ⁇ m.
  • the magnetic layer was oriented while still damp by exposure to a magnetic field, whereafter drying and calendering were conducted to obtain a double-layer structure magnetic tape.
  • Magnetic coating material composition Magnetic powder 100 parts by mass Carbon black 5 parts by mass Alumina 3 parts by mass Vinyl chloride resin (MR110) 15 parts by mass Polyurethane resin (UR8200) 15 parts by mass Stearic acid 1 part by mass Acetylacetone 1 part by mass Methyl ethyl ketone 190 parts by mass Cyclohexanone 80 parts by mass Toluene 110 parts by mass
  • Nonmagnetic coating material composition Nonmagnetic powder ( ⁇ -Fe 2 O 3 ) 85 parts by mass Carbon black 20 parts by mass Alumina 3 parts by mass Vinyl chloride resin (MR110) 15 parts by mass Polyurethane resin (UR8200) 15 parts by mass Methyl ethyl ketone 190 parts by mass Cyclohexanone 80 parts by mass Toluene 110 parts by mass
  • the magnetic properties and the magnetic conversion properties (noise, output, C/N ratio) of the obtained magnetic tape were measured.
  • C/N ratio measurement a drum tester was attached to the recording head and a digital signal was recorded at a recording wavelength of 0.35 ⁇ m. At this time, an MR head was used to measure the reproduced signal and noise was measured as demodulation noise.
  • the noise, output and C/N ratio in the case of using the magnetic powder of Comparative Example 1 was defined as 0 dB. The results of the evaluations are shown in Table 2.
  • Example 5 was repeated except that the magnetic powders of Examples 2-4 were used. The results of the same evaluations as carried out in Example 5 are shown in Table 2.
  • Example 5 was repeated except that the magnetic powders obtained in Comparative Examples 1 and 2 were used. The results of the same evaluations as carried out in Example 5 are shown in Table 2. TABLE 2 Magnetic Magnetic conversion measurements Example No. powder used Output (dB) N(dB) C/N (dB) Example 5 Example 1 ⁇ 0.3 ⁇ 2.3 2.0 Example 6 Example 2 ⁇ 0.3 ⁇ 3.0 2.7 Example 7 Example 3 ⁇ 0.5 ⁇ 3.7 3.2 Example 8 Example 4 ⁇ 0.2 ⁇ 2.0 1.8 Comparative Comparative 0.0 0.0 0.0 Example 3 Example 1 Comparative Comparative ⁇ 4.4 ⁇ 4.6 0.2 Example 4 Example 2

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