JPH0991684A - Magnetic recording medium - Google Patents

Abstract

PROBLEM TO BE SOLVED: To obtain a magnetic recording medium having satisfactory short- wavelength output and S-N ratio, excellent in overwriting characteristics and applicable to a high density digital recording system by specifying the compsn. of ferromagnetic metal particles contained in a magnetic layer. SOLUTION: Ferromagnetic metal particles contained in a magnetic layer formed on a nonmagnetic substrate are conditioned so that ferromagnetic metal particles having 0.05-0.12μm average major axis size and an acicularity ratio of >=8 account for <=5.0% of all the ferromagnetic metal particles or ferromagnetic metal particles having a higher acicularity ratio than the constituent crystallites of the particles account for <=17% of all the ferromagnetic metal particles. In other way, a nonmagnetic layer contg. inorg. non-magnetic powder and a binder is interposed between a nonmagnetic substrate and a magnetic layer contg. ferromagnetic metal particles conditioned as mentioned above and the dry thickness of the magnetic layer is regulated to 0.05-1.0μm.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a magnetic recording medium such as a magnetic tape and, more particularly, to a coating type in which a magnetic coating material mainly composed of ferromagnetic metal particles and a binder is coated on a non-magnetic support to form a magnetic layer. The present invention relates to a magnetic recording medium excellent in output and C / N in a short wavelength region in relation to the magnetic recording medium of (1).

[0002]

2. Description of the Related Art In magnetic recording technology, a medium can be repeatedly used, signals can be easily digitized, and a system can be constructed by combining with peripheral equipment.
Since it has excellent features not found in other recording methods, such as the ability to easily modify signals,
It has been widely used in various fields including computer applications.

In order to meet the demands for downsizing of equipment, improvement of quality of recording / reproducing signal, lengthening of recording, increase of recording capacity, etc., a recording medium has recording density, reliability and durability. It has always been desired to further improve.

For example, in audio and video applications, in order to cope with the practical use of a digital recording method for improving the sound quality and image quality and the development of a recording method compatible with high-definition TV, it is more important than the conventional system. A magnetic recording medium capable of recording and reproducing a short wavelength signal and having excellent reliability and durability even when the relative speed between the head and the medium is increased has been demanded. In addition, it is desired that a large-capacity digital recording medium be developed in order to store an increasing amount of data for computer applications.

In order to achieve high-density recording of a coating type magnetic recording medium, iron or an alloy magnetic powder mainly composed of iron is used in place of the magnetic iron oxide powder conventionally used,
Improving the magnetic properties of the magnetic layer by improving the magnetic substance such as miniaturization of the magnetic powder and improving its packing and orientation, improving the dispersibility of the ferromagnetic powder, and enhancing the surface property of the magnetic layer. From the viewpoint of the above, various methods have been studied and proposed.

For example, a method of using ferromagnetic metal particles or hexagonal ferrite in a ferromagnetic powder for enhancing magnetic properties is disclosed in JP-A-58-122623 and JP-A-61-7.
4137, Japanese Patent Publication No. 62-49656, Japanese Patent Publication No. 60-50323, US462953, U
S46666770, US4543198, etc. are disclosed.

JP-A-1-18961 discloses a metal magnetic powder having a major axis diameter of 0.05 to 0.2 μm and an axial ratio of 4 to 8,
Specific surface area of 30-55 m ² / g, coercive force of 1300 Oe
As mentioned above, the ferromagnetic powder having a saturation magnetization of 120 emu / g or more is disclosed, and the fine metal powder having a small specific surface area is provided. Further, JP-A-60-11300 and JP-A-60-21307 disclose a method for producing fine α-iron oxyhydroxide needle crystals suitable for ferromagnetic powder, particularly ferromagnetic metal particles. However, in the latter case, the major axis length is 0.12 to 0.2.
Hc1450-1 from Goethite with 5 μm and axial ratio 6-8
It is disclosed that ferromagnetic metal particles of 600, σ _S 142-155 emu / g are produced.

Further, in JP-A-6-340426 and JP-A-7-109122, hematite nucleus crystals, iron hydroxide, monodisperse spindle type hematite particles using specific ions, and the hematite particles are reduced. The extremely fine ferromagnetic powder obtained is disclosed.

Further, in order to enhance the dispersibility of the ferromagnetic powder, various surfactants (for example, Japanese Patent Laid-Open No. 52-15660).
No. 6, JP-A-53-15803, JP-A-53-15803
It is disclosed in Japanese Patent Laid-Open No. 116114. ) Or various reactive coupling agents (for example,
9-59608, JP-A-56-58135, JP-B-62-28489 and the like. ) Is proposed.

Further, Japanese Patent Application Laid-Open No. 1-239819 discloses a magnetic powder in which particles of magnetic iron oxide are sequentially coated with a boron compound, an aluminum compound or an aluminum compound and a silicon compound, and magnetic properties and dispersibility are disclosed. To improve. Further, in JP-A-7-22224, the content of the group 1a element of the periodic table is 0.05% by weight or less, and if necessary, 0.1 to 30 atomic% with respect to the total amount of metal elements. Aluminum, and 0.1 to 10 atomic% of the rare earth element relative to the total amount of metallic elements, and the residual amount of the Group 2a element of the periodic table is 0.1% by weight.
The following ferromagnetic metal particles are disclosed to provide a high-density magnetic recording medium having good storage stability and magnetic properties.

Further, in order to improve the surface property of the magnetic layer,
A method (for example, disclosed in Japanese Patent Publication No. 60-44725) of improving the surface forming treatment method of the magnetic layer after coating and drying has been proposed.

In the metal powder for magnetic recording, the particle shape is needle-like and imparts shape anisotropy to obtain the target coercive force. It is well known to those skilled in the art that it is necessary to miniaturize the ferromagnetic metal particles to reduce the surface roughness of the obtained medium for high density recording. However, the acicular ratio of the metal powder for magnetic recording decreases with miniaturization, and the desired coercive force cannot be obtained. Recently, a DVC system for digitizing and recording a video signal has been proposed, and a high performance ME tape and a high performance MP tape are used. Since the coercive force of the MP tape used for DVC is 2000 Oe or more, it is necessary to use ferromagnetic metal particles having a large coercive force and a fine particle size distribution. Further, since the recording method overwrites the signal, it is desired that the overwrite characteristic is good.

The present applicant has previously proposed a ferromagnetic metal particle suitable for a DVC system and a magnetic recording medium using the same (Japanese Patent Application No. 6-139683). This invention uses a magnetic layer having a coercive force of 2000 to 3000 Oe and a thickness of 0.05 to
The present invention provides a magnetic recording medium in which the surface roughness is controlled to 0.3 μm and the surface roughness is controlled to 1 to 3 nm, and a specific reversal magnetization component ratio is defined.

The present invention is a series of the above applications, and further aims to provide means for improving the uniformity of performance and quality of magnetic recording media.

[0015]

SUMMARY OF THE INVENTION The present invention has been made in view of the above problems of the prior art, and has a short wavelength output and S
It is an object of the present invention to provide a magnetic recording medium which has a good / N and an excellent overwrite characteristic and which can be applied to a high density digital recording system.

[0016]

An object of the present invention is to provide a magnetic recording medium in which a magnetic layer containing at least ferromagnetic metal particles is provided on a non-magnetic support, and the ferromagnetic metal particles have an average major axis length of 0. The ratio of the ferromagnetic metal particles having an acicular ratio of 8 or more is 5.0% or less of the total amount of the ferromagnetic metal particles, or the acicular ratio of the crystallites constituting the ferromagnetic metal particles. 4 or more ferromagnetic metal particles account for 17.0% or less of the entire ferromagnetic metal particles, and an inorganic non-magnetic powder mainly between the non-magnetic support and the magnetic layer. A magnetic recording medium provided with a non-magnetic layer containing a binder, wherein the magnetic layer has a dry thickness of 0.
It can be achieved by the above-mentioned magnetic recording medium characterized by having a thickness of 05 to 1.0 μm.

In the present invention, the "ferromagnetic metal particle" means a particle which constitutes the maximum outer shape of the particle due to the size and morphology of the starting material. The largest outer shape that constitutes the particle is taken as the average major axis length and the average acicular ratio of the ferromagnetic metal particle. That is, the average major axis length of ferromagnetic metal particles is
The average length of the major axis constituting the particles is shown, the average minor axis length is the average length of the minor axes constituting the particles, and the average acicular ratio is the average major axis length. It refers to the value divided by the minor axis length. The crystallite means each crystal of the metal particles constituting the ferromagnetic metal particles. The particles forming the outer shape of the metal particles, that is, the ferromagnetic metal particles are not necessarily composed of one crystal, but are composed of a plurality of crystals. When a particle photograph is taken with a high-resolution transmission electron microscope, the particles that make up the largest outer shape of the particles are called ferromagnetic metal particles, and the lattice image can be obtained by finer observation.
The unit from which the lattice image can be obtained is the crystallite. The acicular ratio of the crystallite is a value obtained by dividing the major axis length of the crystallite by the minor axis length.

In the present invention, when controlling the average major axis length of the ferromagnetic metal particles to be 0.05 to 0.12 μm, the ferromagnetic metal particles having an acicular ratio of 8 or more are 5.0% of the whole ferromagnetic metal particles. Or less, and / or controlling the ferromagnetic metal particles having the acicular ratio of the crystallites constituting the ferromagnetic metal particles of 4 or more to 17.0% or less of the entire ferromagnetic metal particles, As a result, it is possible to provide a magnetic recording medium having a short wavelength output and a good S / N and excellent overwrite characteristics.

In the present invention, the average major axis length of the ferromagnetic metal particles is preferably 0.05 to 0.10 μm. The ferromagnetic metal particles preferably have an acicular ratio of 3.0 to 7.0,
More preferably, the needle-like ratio is 3.0 to 6.0, preferably 80 to 100%, and more preferably 90 to 1%.
It is controlled to occupy 00%. Further, the acicular ratio of the crystallite is preferably 2.0 to 5.0, more preferably
The total amount of ferromagnetic metal particles of 2.5 to 4.0 is preferably 7
It is controlled to occupy 5 to 100%, more preferably 85 to 100%.

If the major axis length of the ferromagnetic metal particles is smaller than 0.05 μm, not only the desired coercive force cannot be obtained, but also it is difficult to disperse when a magnetic coating is prepared and the orientation of the magnetic coating is improved even if the magnetic field is oriented. The effect is unlikely to appear. Further, it becomes difficult to secure high saturation magnetization required for high density recording due to the influence of the oxide film formed for stabilization. If the major axis length of the ferromagnetic metal particles is larger than 0.12 μm and the acicular ratio distribution of the ferromagnetic metal particles and the acicular ratio distribution of the crystallites do not satisfy the above, Hc
The distribution is greatly deteriorated (high Hc components, especially Hc 3000 Oe or more components are increased), which is not preferable for overwrite characteristics, and the surface roughness of the magnetic recording medium becomes large.

The coercive force Hc of the magnetic layer of the present invention is usually 1
800-3000 Oe, preferably 1900-2800
Oe, more preferably 2200 to 2500 Oe, and the Bm (maximum magnetic flux density) of the magnetic layer is usually 3500 to
5500 Gauss (G), preferably 3900-5500
G. If Hc and Bm are smaller than the lower limit value, a short wavelength output cannot be sufficiently obtained, and if they are larger than the upper limit value, the head used for recording is saturated, so that the output cannot be secured.

In the present invention, it is difficult to obtain a high coercive force in the past and it is difficult to reduce the high coercive force component. Focusing on and controlling this, high Hc and Hc
The distribution is improved. Conventionally, the morphology of the starting material is insufficiently controlled, and when the ferromagnetic metal particles are used, the number and shape of the crystallites constituting the ferromagnetic metal particles are not controlled. I think the improvement was insufficient.

In the present invention, the method for controlling the ferromagnetic metal particles is not particularly limited, and any method can be used, but the following method is preferably exemplified. It is possible to control the nucleation number of a metal (eg, Fe) from a metal oxide (eg, FeO) when a starting material having a uniform particle size is subjected to a sintering prevention treatment and then reduced. Examples of the starting material include monodisperse goethite and monodisperse hematite.

The average major axis length of the starting material is 0.05 to 0.2.
It is preferably 0 μm and the acicular ratio is 4 to 15. When using a raw material with an average major axis length of less than 0.05 μm, Hc, σs
It is difficult to set the target range. When a raw material having an average major axis length of more than 0.20 μm is used, the volume of ferromagnetic metal particles produced is too large, and thus it is difficult to secure the surface roughness required for high-density recording when a magnetic tape is produced. If the acicular ratio is less than 4, the coercive force of the ferromagnetic metal particles is small, and the effect of the magnetic field orientation treatment performed to improve the characteristics of the magnetic tape is poor. I can not use it. When the acicular ratio is 15 or more, it is difficult to control the acicular ratio of the crystallite and the coercive force distribution is widened. In particular, the high coercive force component increases and the overwrite characteristic is poor.

Further, as the means for controlling the ferromagnetic metal particles, the following methods and the like can be mentioned. Mainly to specify the elemental composition inside the ferromagnetic metal particles. Particularly in the case of ferromagnetic metal particles mainly composed of Fe, F
Identify the trace elements that interact with e. As the trace element, Ca, Co, Ni, Cr and the like are preferable. It is preferable that the trace element is added at the time of producing goethite or hematite and / or after the production, it is added by surface treatment. In a method of reducing an oxide of a ferromagnetic metal element to ferromagnetic metal particles, pretreatment before reduction, for example, dehydration conditions such as goethite, annealing conditions and the reduction conditions,
For example, select temperature, reducing gas, reducing treatment time, etc.

Specifically, each condition for treating the trace element-containing goethite obtained above is as follows. As the dehydration conditions, it is possible to perform dehydration under a nitrogen atmosphere in a rotary electric furnace at 250 to 400 ° C., preferably 300 to 400 ° C. for 0.5 to 2 hours, preferably 0.5 to 1 hour. The annealing conditions include a static reduction furnace in a nitrogen atmosphere at 500 to 800 ° C., preferably 550 to 550 ° C.
It may be carried out at 700 ° C. for 1 to 5 hours, preferably 2 to 3 hours. After the dehydration treatment and before the annealing treatment, a step of washing the hematite obtained by the dehydration treatment with water to remove the soluble alkali metal may be provided.

The reducing conditions are as follows: a static reducing furnace in a hydrogen atmosphere at 350 to 500 ° C., preferably 425 to 48.
0 ° C., 0.25 to 1 hour, preferably 0.25 to 0.5
After reducing treatment for an hour and then replacing the atmosphere with nitrogen,
450-650 ° C, preferably 500-600 ° C, 0.
Heating for 5 to 3 hours, preferably 1 to 2 hours, then switching to pure hydrogen, and reducing treatment at the above temperature for 3 to 5 hours can be mentioned.

The end of the reduction is determined by measuring the water content in the wastewater gas with a dew point meter. The method for producing the ferromagnetic metal particles is a known method, for example, JP-A-7-109122.
The methods described in JP-A-6-340426 and JP-A-6-340426 can be applied. The ferromagnetic metal element of the ferromagnetic metal particles is not particularly limited, but those containing Fe, Ni or Co as the main component (75% or more) are preferable. Co is particularly preferable because it can increase σs and can form a dense and thin oxide film. Co content is F
e is preferably 5 to 40 atomic%, more preferably 1
It is 0 to 30 atomic%. As described above, Co is partially doped into the raw material, and then a necessary amount is deposited on the surface and added to the raw material,
It is preferable to alloy by reduction.

The above-mentioned ferromagnetic metal particles usable in the present invention include Al, Si, S, Ti, V, Cr, Cu, Y and M in a weight ratio of 20% by weight or less in addition to predetermined metal atoms.
o, Rh, Pd, Ag, Sn, Sb, Te, Ba, S
r, W, Au, Pb, Bi, La, Ce, Pr, Nd,
It preferably contains atoms such as P, Mn, Zn, Sr, B, and Ca. In addition to controlling the shape of the starting material, these elements are effective in preventing sintering between particles, promoting reduction, and controlling the shape of the reduced ferromagnetic metal particles and the unevenness of the particle surface.

In order to finally reduce the monodisperse goethite or the monodisperse hematite to a metal, it is reduced with pure hydrogen. It is useful to anneal with αFe ₂ O ₃ in the middle of the process. Fe from αFe ₂ O ₃
When reducing to ₃ O ₄ or FeO, various reducing gases can be used instead of pure hydrogen. Since it is known that water is involved in sintering during the reduction, when the nuclei of the metal are formed, the nuclei of the metals are formed from the metal oxide, and then the crystallites are formed. It is necessary to remove the water generated by the process to the outside of the system in a short time or control the amount of water generated by the reduction. Such water control can be performed by controlling the partial pressure of the reducing gas or by controlling the amount of reducing gas.

The ferromagnetic metal particles of the present invention can be obtained by heating in an inert gas as described above to distribute the metal nuclei in the ferromagnetic metal particles and then reducing with hydrogen as described above. it can. As is well known, the ferromagnetic metal particles are gradually oxidized to form an oxide film on the surface of the particles in order to be chemically stable. The ferromagnetic metal particles may contain a small amount of hydroxide or oxide. If carbon dioxide gas is contained in the gas used during the gradual oxidation, it is adsorbed at the basic points on the surface of the ferromagnetic metal particles, and thus carbon dioxide gas may be contained.

Conventionally, metal magnetic powders have been produced using goethite (α-FeOOH) or hematite (α-Fe ₂ O ₃ ) as a starting material. It was great. That is, the average major axis length of the ferromagnetic metal particles was about 0.2 to 0.3 μm.
At the same time as deoxidation and reduction to metal, the outer shape of the particle contracted, and conventional metal particles obtained polycrystalline faint crystals as shown in FIG. Moreover, the crystallites had different sizes and shapes, and the number of crystallites was 4 to 10 or more. In the present invention, the outer shape of the particles caused by the size and morphology of the starting material is made small, and the conventional polycrystal state is aimed at a dense structure in which the crystallites are continuous as shown in FIG. 1 as much as possible.

In the present invention, the size distribution of the ferromagnetic metal particles having the structure shown in FIG. 1 is specified from the viewpoint of the acicular ratio and the crystallite acicular ratio. In the present invention, the number of crystallites of the ferromagnetic metal particles is usually 1.0 to 1.0 on average.
To 5.0, preferably 1.0 to 3.0, and the acicular ratio of the crystallites is usually 2.0 to 5.0, preferably 2.5 to 4.0 on average.

The saturation magnetization of the ferromagnetic metal fine powder of the present invention is usually 125 emu / g or more, preferably 130 emu / g.
g to 165 emu / g, more preferably 135 to 15
It is 0 emu / g. Immediately after reduction, JP-A-61-2232
It is also effective to treat the compound described in JP-A No. 7-75 or a coupling agent having various substituents and then gradually oxidize it, since the saturation magnetization of the ferromagnetic metal particles can be increased. The coercive force of the ferromagnetic metal particles is usually 1700 to 3000 Oe (Oersted), preferably 1800 to 3000 Oe, and more preferably 1900 to 2500 Oe.

The ferromagnetic metal powder of the present invention has a magnetization reversal mode close to an ideal fanning mode, and the inventor presumes that fine particles and high coercive force ferromagnetic metal particles of the present invention were obtained. ing. In the present invention, a particle photograph was taken with a high resolution transmission electron microscope, and the acicular ratio of crystallites was determined from the average major axis length of the ferromagnetic metal particles and the lattice image of the ferromagnetic metal particles. Such measurement was performed on about 200 particles to determine the average major axis length. The acicular ratio of the crystallite is obtained by tracing the outline of each crystallite of the high-resolution electron microscope photograph taken with an image analyzer to obtain the major axis length and the minor axis length (major axis length / minor axis length).
Was calculated.

The ferromagnetic metal powder may be previously treated with a dispersant, a lubricant, a surfactant, an antistatic agent, etc., which will be described later, before the dispersion. Specifically, Japanese Patent Publication No. 44-1
4090, Japanese Patent Publication No. 45-18372, Japanese Patent Publication No. 47-22062, Japanese Patent Publication No. 47-22513, Japanese Patent Publication No. 46-28466, Japanese Patent Publication No. 46-3.
No. 8755, No. 47-4286, No. 47-12422, No. 47-17284, No. 47-18509, No. 47-18
573, Japanese Patent Publication No. 39-10307, Japanese Patent Publication No. 48-39639, US Pat. No. 3,026,215,
No. 3031341, No. 3100194, No. 3242
No. 005, No. 3389014 and the like.

The water content of the ferromagnetic metal powder is preferably 0.01 to 2% by weight. It is desirable to optimize the water content depending on the type of binder described below.

The tap density of the ferromagnetic metal powder is 0.2 to
0.8 g / cc is desirable. If it is greater than 0.8 g / cc, the powder is not gradually oxidized uniformly when gradually oxidized, and thus it is difficult to safely handle the powder, or the magnetization of the obtained tape decreases with time. When the tap density is 0.2 g / cc or less, the dispersion tends to be insufficient.

The binder resin of the magnetic layer in the magnetic recording medium of the present invention may be a conventionally known thermoplastic resin, thermosetting resin, reactive resin or a mixture thereof. As a thermoplastic resin, the glass transition temperature is -1.
00 to 150 ° C, number average molecular weight of 1,000 to 20,000
0, preferably 10,000 to 100,000, and a degree of polymerization of about 50 to 1,000.

Examples of the binder resin include vinyl chloride, vinyl acetate, vinyl alcohol, maleic acid, acrylic acid, acrylic acid ester, vinylidene chloride, acrylonitrile, methacrylic acid, methacrylic acid ester, styrene, butadiene, ethylene and vinyl. There are polymers or copolymers containing butyral, vinyl acetal, vinyl ether, etc. as constituent units, polyurethane resins, and various rubber resins.

As the thermosetting resin or reactive resin, phenol resin, epoxy resin, polyurethane curable resin, urea resin, melamine resin, alkyd resin, acrylic reaction resin, formaldehyde resin, silicone resin, epoxy-polyamide resin. , A mixture of polyester resin and isocyanate prepolymer, a mixture of polyester polyol and polyisocyanate, a mixture of polyurethane and polyisocyanate, and the like.

In order to obtain more excellent dispersion effect of the ferromagnetic powder and durability of the magnetic layer in the above-mentioned binder resin, COOM, SO ₃ M, OSO ₃ M, P = O (OM) is added as necessary.
₂ , OP = O (OM) ₂ , (wherein M is a hydrogen atom or an alkali metal base), OH, NR ₂ , N ⁺ R
It is preferable to use one in which at least one polar group selected from ₃ (R is a hydrocarbon group), an epoxy group, SH, CN, etc. is introduced by copolymerization or addition reaction. The amount of such a polar group is 10 ^-1 to 10 ^-8 mol / g, preferably 10 ^-2 to 10 ^-6 mol / g.

The binder resin used in the magnetic recording medium of the present invention is used in the range of 5 to 50% by weight, preferably 10 to 30% by weight, based on the ferromagnetic metal powder.
It is preferable to use these in combination in the range of 5 to 100% by weight when using a vinyl chloride resin, 2 to 50% by weight when using a polyurethane resin, and 2 to 100% by weight of polyisocyanate.

Further, the filling degree of the ferromagnetic metal powder in the magnetic layer can be calculated from the maximum saturation magnetization amount σs and Bm of the used ferromagnetic metal powder (Bm / 4πσs), which is desirable in the present invention. Is 1.7 g / cc or more, more preferably 1.9 g / cc or more, and most preferably 2.1 g / cc or more.

In the present invention, when polyurethane is used, the glass transition temperature is -50 to 100 ° C. and the elongation at break is 1.
00-2000%, breaking stress 0.05-10 kg / c
m ² and the yield point are preferably 0.05 to 10 kg / cm ² .

Examples of the polyisocyanate used in the present invention include tolylene diisocyanate, 4,4'-diphenylmethane diisocyanate, hexamethylene diisocyanate, xylylene diisocyanate and naphthylene-
1,5-diisocyanate, o-toluidine diisocyanate, isophorone diisocyanate, isocyanates such as triphenylmethane triisocyanate,
Products of these isocyanates and polyalcohols, and polyisocyanates formed by condensation of isocyanates can be used. Commercially available trade names of these isocyanates include Nippon Polyurethane Co., Ltd., Coronate L, Coronate HL,
Coronate 2030, Coronate 2031, Millionate MR, Millionate MTL, Takenate D-102, Takenate D-102, Takenate D-110N, Takenate D
-200, Takenate D-202, manufactured by Sumitomo Bayer,
There are death module L, death module IL, death module N, death module HL and the like, and these can be used alone or in combination of two or more by utilizing the difference in curing reactivity.

The magnetic layer of the magnetic recording medium of the present invention usually has various functions such as a lubricant, an abrasive, a dispersant, an antistatic agent, a dispersant, a plasticizer and an antifungal agent. The material to have is contained according to the purpose.

The lubricant used in the magnetic layer of the present invention is a dialkyl polysiloxane (where alkyl is 1 to 1 carbon atoms).
5), dialkoxy polysiloxane (alkoxy has 1 to 4 carbon atoms), monoalkyl monoalkoxy polysiloxane (alkyl has 1 to 5 carbon atoms, alkoxy has 1 to 4 carbon atoms), phenyl polysiloxane, fluoro Silicon oil such as alkyl polysiloxane (where alkyl is 1 to 5 carbon atoms); Conductive fine powder such as graphite; Inorganic powder such as molybdenum disulfide and tungsten disulfide; Polyethylene, polypropylene, polyethylene vinyl chloride copolymer, poly Plastic fine powder of tetrafluoroethylene or the like; α-olefin polymer; saturated fatty acid that is solid at room temperature (carbon number 10 to 22); unsaturated aliphatic hydrocarbon that is liquid at room temperature (carbon with n-olefin double bond at the end) Compound having about 20 carbon atoms; a monobasic fatty acid having 12 to 20 carbon atoms Fatty acid esters consisting of 3 to 12 monovalent alcohol prime, fluorocarbons and the like can be used.

Among the above, saturated fatty acids and fatty acid esters are preferable, and it is more preferable to use both in combination. Alcohols used as raw materials for fatty acid esters include ethanol, butanol, phenol, benzyl alcohol, and 2
-Methylbutyl alcohol, 2-hexyldecyl alcohol, propylene glycol monobutyl ether, ethylene glycol monobutyl ether, dipropylene glycol monobutyl ether, diethylene glycol monobutyl ether, monoalcohols such as s-butyl alcohol, ethylene glycol, diethylene glycol,
Examples include polyhydric alcohols such as neopentyl glycol, glycerin, and sorbitan derivatives. Similarly, fatty acids include acetic acid, propionic acid, octanoic acid, 2-ethylhexanoic acid, lauric acid, myristic acid, stearic acid, palmitic acid, behenic acid, arachidic acid, oleic acid, linoleic acid, linolenic acid, elaidic acid, palmitoleic acid. And aliphatic carboxylic acids or mixtures thereof.

Specific examples of the fatty acid ester include butyl stearate, s-butyl stearate, isopropyl stearate, butyl oleate, amyl stearate, 3-methylbutyl stearate, 2-ethylhexyl stearate, 2-hexyl decyl. Stearate, butyl palmitate, 2-ethylhexyl myristate,
Mixture of butyl stearate and butyl palmitate, butoxyethyl stearate, 2-butoxy-1-propyl stearate, ester of dipropylene glycol monobutyl ether with stearic acid, diethylene glycol dipalmitate, hexamethylene diol myristic acid Examples thereof include various ester compounds such as those esterified to diester, and glycerin oleate.

Further, in order to reduce the hydrolysis of fatty acid ester that often occurs when the magnetic recording medium is used under high humidity, branched / straight chain, cis / trans and other isomer structures of branched fatty acids and alcohols as raw materials, and branched positions are used. Is made. These lubricants are added in the range of 0.2 to 20 parts by weight with respect to 100 parts by weight of the binder.

The following compounds may be further used as the lubricant. That is, silicone oil, graphite, molybdenum disulfide, boron nitride, fluorinated graphite, fluoroalcohol, polyolefin, polyglycol, alkyl phosphate, tungsten disulfide and the like.

As the abrasive used in the magnetic layer of the present invention, commonly used materials are α, γ alumina, fused alumina, corundum, artificial corundum, silicon carbide, chromium oxide (Cr ₂ O ₃ ), diamond and artificial. Diamond, garnet, emery (main components: corundum and magnetite), αFe ₂ O _3, etc. are used. These abrasives have a Mohs hardness of 6 or more. Specific examples include AKP-10, AKP-12, AKP-15, manufactured by Sumitomo Chemical Co., Ltd.
20AKP-30, AKP-50, AKP-1520,
AKP-1500, HIT-50, HIT60A, HI
T70, HIT80, HIT-100, Nippon Kagaku Kogyo KK, G5, G7, S-1, chromium oxide K, Uemura Kogyo UB40B, Fujimi Abrasives WA8000, WA10
000, Toda Kogyo TF100, TF140, TF1
80 etc. can be raised. Average particle size is 0.05-3 μm
Is effective, and is preferably 0.05-
It is 1.0 μm.

The total amount of these abrasives is 1 to 20 parts by weight, preferably 1 to 15 parts by weight, based on 100 parts by weight of the magnetic material. If it is less than 1 part by weight, sufficient durability cannot be obtained, and if it is more than 20 parts by weight, the surface property and filling degree are deteriorated. These abrasives may be dispersed in a binder in advance and then added to the magnetic paint.

The magnetic layer of the magnetic recording medium of the present invention may contain conductive particles as an antistatic agent in addition to the non-magnetic powder. However, in order to maximize the saturation magnetic flux density of the uppermost layer, it is preferable to add as little as possible to the uppermost layer and to add it to a coating layer other than the uppermost layer. It is particularly preferable to add carbon black as an antistatic agent in terms of reducing the surface electric resistance of the entire medium. As the carbon black that can be used in the present invention, furnace for rubber, thermal for rubber, black for color, conductive carbon black, acetylene black and the like can be used. Specific surface area 5 to 500 m ² / g, DBP oil absorption 10 to 1500 ml / 100 g, particle size 5 mμ
~ 300mμ, pH 2 ~ 10, water content 0.1 ~ 10
%, And the tap density is preferably 0.1 to 1 g / cc. Specific examples of the carbon black used in the present invention include BLACKPEARLS 200 manufactured by Cabot Corporation.
0, 1300, 1000, 900, 800, 700, V
ULCAN XC-72, manufactured by Asahi Carbon Co., # 80, #
60, # 55, # 50, # 35, manufactured by Mitsubishi Kasei Kogyo, #
3950B, # 3250B, # 2700, # 2650,
# 2600, # 2400B, # 2300, # 900, #
1000, # 95, # 30, # 40, # 10B, MA2
30, MA220, MA77, manufactured by Columbia Carbon Co., CONDUCTEX SC, RAVEN 150,
50, 40, 15, Ketjen Black EC, Ketjen Black ECDJ-500, and Ketjen Black ECDJ-600 manufactured by Lion Aguzo. Carbon black may be surface-treated with a dispersing agent or the like, carbon black may be oxidized, or grafted with a resin, or may be used in which a part of the surface is graphitized. Before adding the carbon black to the magnetic paint, the carbon black may be dispersed in a binder in advance. When carbon black is used for the magnetic layer, it is preferable to use 0.1 to 30% by weight based on the magnetic material. Further, when a non-magnetic layer is provided, it is preferably contained in the inorganic non-magnetic powder in an amount of 3 to 20% by weight.

Generally, carbon black functions not only as an antistatic agent, but also for reducing the coefficient of friction, imparting light-shielding properties, improving film strength, etc. These differ depending on the carbon black used. Therefore, these carbon blacks used in the present invention may be used in different types, amounts, and combinations depending on the purpose based on the above-mentioned properties such as particle size, oil absorption, conductivity, and pH. Is of course possible. Carbon black that can be used can be referred to, for example, "Carbon Black Handbook" edited by Carbon Black Association.

The non-magnetic layer in the case of forming the non-magnetic layer between the magnetic layer and the non-magnetic support of the magnetic recording medium of the present invention (hereinafter, referred to as
The lower layer) is a layer in which an inorganic non-magnetic powder is mainly dispersed in a binder resin. Various types of inorganic non-magnetic powder can be used for the non-magnetic layer. For example, α-alumina, β-alumina having an α conversion rate of 90% or more,
γ-alumina, silicon carbide, chromium oxide, cerium oxide, α-iron oxide, corundum, silicon nitride, titanium carbide, titanium oxide, silicon dioxide, boron nitride, zinc oxide, calcium carbonate, calcium sulfate, barium sulfate alone Or used in combination. The particle size of these inorganic non-magnetic powders is preferably 0.01 to 2μ, but if necessary, inorganic non-magnetic powders having different particle sizes may be combined, or a single inorganic non-magnetic powder may be used to broaden the particle size distribution. It can also be effective. The inorganic non-magnetic powder used may be surface-treated in order to increase the interaction with the binder resin used and improve the dispersibility. The surface-treated product may be treated with an inorganic substance such as silica, alumina, or silica-alumina, or may be treated with a coupling agent. Tap density is 0.3-2g / c
c, water content is 0.1 to 5% by weight, pH is 2 to 11, and specific surface area is preferably 5 to 100 m ² / g. The inorganic non-magnetic powder may be needle-shaped, spherical, dice-shaped, or plate-shaped. Specific examples of the inorganic non-magnetic powder used in the present invention include AKP-20 and AKP manufactured by Sumitomo Chemical Co., Ltd.
-30, AKP-50, HIT-50, Nippon Kagaku Kogyo KK, G5, G7, S-1, Toda Kogyo TF-10.
0, TF-120, TF-140, TT0 made by Ishihara Sangyo Co., Ltd.
55 series, ET300W, TTT3 manufactured by Titanium Industry Co., Ltd.
0, needle-like hematite particles and the like, which are intermediate raw materials for magnetic iron oxide and ferromagnetic metal powder prepared by the iron oxide reduction method.

The layer structure of the magnetic recording medium of the present invention is basically not limited as long as it has at least the above magnetic layer or the above nonmagnetic layer on a nonmagnetic support.
A magnetic layer or a non-magnetic layer having another structure can be provided. For example, when a ferromagnetic layer is formed instead of the non-magnetic layer, the ferromagnetic material may be iron oxide ferromagnetic material, cobalt modified iron oxide ferromagnetic material, CrO ₂ , hexagonal ferrite, various metal ferromagnetic materials. Various materials having a body dispersed in a resin can be used. These ferromagnetic layers are also called lower layers.

Forming two or more coating layers on a non-magnetic support is also effective in producing a magnetic recording medium having a high recording density, and the simultaneous coating method produces an ultrathin magnetic layer. It is especially excellent because it can be done. As a specific method of the wet-on-wet method as the simultaneous application method,

(1) First, the lower layer is coated by a gravure coating, roll coating, blade coating, or extrusion coating apparatus that is generally used for magnetic paints, and while the layer is still wet, for example, Japanese Patent Publication No. 1 -46186, JP-A-60-238179 and JP-A-2-2
Japanese Patent Publication No. 65672 discloses a method for coating an upper layer by a non-magnetic support pressure type extrusion coating apparatus,

(2) By a coating head having two slits for passing a coating liquid as disclosed in JP-A-63-88080, JP-A-2-17971 and JP-A-2-265672. , A method of applying the lower layer coating solution and the upper layer coating solution almost simultaneously,

(3) A method of coating the upper layer and the lower layer almost at the same time by using the extrusion coating apparatus with a backup roll disclosed in JP-A-2-174965.

When applying by the wet-on-wet method, the flow characteristics of the coating liquid for the magnetic layer and the coating liquid for the non-magnetic layer should be as close as possible so that the interface between the coated magnetic layer and the non-magnetic layer is not disturbed. It is possible to obtain a magnetic layer having a uniform thickness and less variation in thickness. Since the flow characteristics of the coating liquid strongly depend on the combination of the powder particles and the binder resin in the coating liquid,
In particular, it is necessary to pay attention to the selection of the non-magnetic powder used for the non-magnetic layer.

The non-magnetic support of the present magnetic recording medium is usually
1 to 100 μm, preferably 3 to 20 μm, and the thickness of the nonmagnetic layer is 0.5 to 10 μm, preferably 1 to 4 μm. When a magnetic layer is provided on the non-magnetic layer, the thickness of the magnetic layer is usually 0.05 to 3.0 μm, preferably 0.0
5 to 1.0 μm. Further, layers other than the magnetic layer and the non-magnetic layer can be formed according to the purpose. For example, an undercoat layer for improving adhesion may be provided between the nonmagnetic support and the lower layer. This thickness is 0.0
It is 1 to 2 μm, preferably 0.05 to 0.5 μm.
Further, a back coat layer may be provided on the side of the non-magnetic support opposite to the side of the magnetic layer. This thickness is 0.1-2 μm,
Preferably it is 0.3 to 1.0 μm. Known undercoat layers and back coat layers can be used. In the case of a disk-shaped magnetic recording medium, the above layer constitution can be provided on one side or both sides.

The non-magnetic support used in the present invention is not particularly limited, and those commonly used can be used. Examples of materials forming the non-magnetic support include polyethylene terephthalate, polyethylene, polypropylene, polycarbonate, polyethylene naphthalate, polyamide, polyamide imide, polyimide, polysulfone, films of various synthetic resins such as polyethersulfone, and aluminum foil. , And metal foils such as stainless steel foil.

In order to effectively achieve the object of the present invention, the surface roughness of the non-magnetic support is 0.03 μm or less, preferably 0.02 μm, as the centerline average surface roughness Ra (cutoff value 0.25 mm). Hereafter, it is more preferably 0.01 μm or less. Further, it is preferable that these non-magnetic supports not only have a small center line average surface roughness but also that they have no coarse protrusions of 1 μm or more. The surface roughness shape can be freely controlled by the size and amount of the filler added to the non-magnetic support as needed. Examples of these fillers include oxides and carbonates of Ca, Si, Ti and the like, and organic resin fine powders of an acrylic resin and the like. The F-5 value in the web running direction of the nonmagnetic support used in the present invention is preferably 5 to 50 kg / mm ² ,
The F-5 value in the web width direction is preferably 3 to 30 kg / m.
m ² and the F-5 value in the longitudinal direction of the web is generally higher than the F-5 value in the web width direction, but this is not the case especially when the strength in the width direction needs to be increased.

The heat shrinkage of the support in the web running direction and the width direction at 100 ° C. for 30 minutes is preferably 3% or less, more preferably 1.5% or less, and the heat shrinkage at 80 ° C. for 30 minutes. It is preferably 1% or less, more preferably 0.
It is 5% or less. Breaking strength is 5-100Kg in both directions
/ Mm ² and an elastic modulus of 100 to 2000 kg / mm ² are desirable.

The organic solvent used in the present invention may be any ratio of ketones such as acetone, methyl ethyl ketone, methyl isobutyl ketone, diisobutyl ketone, cyclohexanone, isophorone and tetrahydrofuran, methanol, ethanol, propanol, butanol, isobutyl alcohol and isopropyl alcohol. Alcohols such as methylcyclohexanol, esters such as methyl acetate, butyl acetate, isobutyl acetate, isopropyl acetate, ethyl lactate, and glycol acetate; glycol ethers such as glycol dimethyl ether, glycol monoethyl ether, and dioxane; benzene; Aromatic hydrocarbons such as toluene, xylene, cresol, chlorobenzene, methylene chloride, ethylene chloride, carbon tetrachloride, Chloroform, ethylene chlorohydrin, dichlorobenzene, chlorinated hydrocarbons and the like, N,
Those such as N-dimethylformamide and hexane can be used. These organic solvents are not necessarily 100% pure, and may contain impurities such as isomers, unreacted substances, by-products, decomposition products, oxides, and water in addition to the main components. These impurities are preferably 30% or less, more preferably 10% or less. If necessary, the type and amount of the organic solvent used in the present invention may be changed between the magnetic layer and the non-magnetic layer. A solvent with a high solubility parameter for the magnetic layer that uses a solvent with high volatility for the non-magnetic layer to improve the surface properties, uses a solvent with high surface tension (cyclohexanone, dioxane, etc.) for the non-magnetic layer, and improves coating stability Examples of such methods include increasing the filling degree by using, but it goes without saying that the present invention is not limited to these examples.

The magnetic recording medium of the present invention is kneaded and dispersed in an organic solvent together with the ferromagnetic metal powder, the binder resin, and other additives if necessary, and the magnetic coating material is coated on a non-magnetic support. It is obtained by orienting and drying if necessary.

The process for producing the magnetic coating material for the magnetic recording medium of the present invention comprises at least a kneading process, a dispersing process, and a mixing process provided before and after these processes, if necessary. Each step may be divided into two or more steps. Ferromagnetic metal powder, binder, carbon black, abrasive, antistatic agent, lubricant used in the present invention,
All raw materials such as a solvent may be added at the beginning or during any step. Further, individual raw materials may be added in two or more steps in a divided manner. For example, polyurethane may be divided and supplied in a kneading step, a dispersing step, and a mixing step for adjusting the viscosity after dispersion.

Various kneading machines are used for kneading and dispersing the magnetic paint. For example, two-roll mill, three-roll mill, ball mill, pebble mill, tron mill, sand grinder, Szegvari, attritor, high speed impeller disperser, high speed stone mill, high speed impact mill, disper, kneader, high speed mixer, homogenizer, ultra A sonic disperser or the like can be used.

In order to achieve the object of the present invention, it goes without saying that conventionally known manufacturing techniques can be used as a part of the steps, but a strong kneading force such as a continuous kneader or a pressure kneader is used in the kneading step. It is preferable to use the one that has. When a continuous kneader or a pressure kneader is used, all or part of the ferromagnetic metal powder and the binder (however, 30% or more of the total binder is preferable) and 15 to 500 parts by weight based on 100 parts by weight of the ferromagnetic metal powder. The kneading is performed within the range. Details of these kneading treatments are described in JP-A-1-106338 and JP-A-64-79274. In the present invention, JP-A-62-212
By using the simultaneous multi-layer coating method as shown in 933, more efficient production can be achieved.

The residual solvent contained in the magnetic layer of the magnetic recording medium of the present invention is preferably 100 mg / m ² or less, more preferably 10 mg / m ² or less, and the residual solvent contained in the magnetic layer is contained in the non-magnetic layer. It is preferably less than the residual solvent contained.

The porosity of the magnetic layer in both the lower layer and the upper layer is preferably 30% by volume or less, more preferably 10% by volume.
It is the following. The porosity of the nonmagnetic layer is preferably larger than that of the magnetic layer, but may be small as long as the porosity of the nonmagnetic layer is 5% by volume or more.

The magnetic recording medium of the present invention can have a lower layer and an upper layer, but it is easily presumed that the physical properties of the lower layer and the upper layer can be changed according to the purpose. For example, the elastic modulus of the upper layer is increased to improve running durability, and at the same time, the elastic modulus of the lower layer is made lower than that of the magnetic layer to improve the contact of the magnetic recording medium with the head.

By such a method, the magnetic layer coated on the support is subjected to a treatment for orienting the ferromagnetic metal powder in the layer, if necessary, and then the formed magnetic layer is dried. If necessary, the magnetic recording medium of the present invention is manufactured by performing a surface smoothing process or cutting into a desired shape. The above composition for the upper layer or the composition for the lower layer is dispersed together with a solvent, and the obtained coating solution is coated on a non-magnetic support and oriented and dried to obtain a magnetic recording medium.

The elastic modulus of the magnetic layer at 0.5% elongation is preferably 100 to 2000 kg in both the web coating direction and the width direction.
/ Mm ² , and the breaking strength is desirably 1 to 30 kg / c.
m ² , the elastic modulus of the magnetic recording medium is preferably 100 to 1500 kg / mm ^{2 in} both the web coating direction and the width direction, the residual elongation is preferably 0.5% or less, and the thermal shrinkage at any temperature of 100 ° C. or less is desirable. Is 1% or less, more preferably 0.5% or less, and most preferably 0.1% or less.

The magnetic recording medium of the present invention may be a tape for video use, audio use, or a floppy disk or magnetic disk for data recording.
This is particularly effective for a medium for digital recording in which the loss of a signal due to the occurrence of dropout is fatal.
Further, by making the lower layer a non-magnetic layer and setting the thickness of the uppermost layer to 1 μm or less, it is possible to obtain a high-density and large-capacity magnetic recording medium having high electromagnetic conversion characteristics and excellent overwrite characteristics.

[0079]

【Example】

The novel features of the present invention will be specifically described in the following examples, but the present invention is not limited thereto.

Production Example 1 Production Examples 1-1 to 7 (Production of Ferromagnetic Metal Powder) In a 150 l tank equipped with a stirrer, 35 mol of 1.7 mol / l sodium carbonate and 2.0 mol / l were added.
To a mixed solution of 15 liters of sodium hydroxide, 0.4 liter of an aqueous solution of 0.5 mol / l of sodium phosphate was added, and while bubbling nitrogen, bubbling nitrogen in another tank dissolved ferrous sulfate and cobalt sulfate. 40 l of an aqueous solution (Fe ²⁺ concentration: 1.35 mol / l, Co concentration: 0.24 mol / l) was added and mixed. After stirring for 10 minutes, the temperature of the suspension was adjusted to 20 ° C., and a precipitate containing ferrous iron was produced.
Air was introduced instead of nitrogen to oxidize the precipitate to generate goethite nuclei. Fe ²⁺ concentration in the suspension is 0.5 mol /
When it reached 1, the air oxidation was discontinued and replaced with nitrogen, the temperature of the suspension was heated to 35 ° C. and maintained for 2 hours, and then 1.1 l of sodium aluminate 1.1 mol / l aqueous solution was added.
After that, nitrogen was changed to air and the oxidation reaction proceeded to produce spindle-shaped goethite. The obtained particles were filtered and washed with water. When a part of it was dried and a transmission electron micrograph was taken to determine the average particle size, the average major axis length was 0.12 μm and the average acicular ratio was 9.5. Also, in nitrogen at 120 ° C for 3
The specific surface area after heating and dehydration for 0 minutes was 125 m ² / g.

The obtained goethite was made into a 2% slurry in water and stirred so that each addition amount of Co and / or Ca shown in Table 1 (indicated by atomic% relative to 100 atomic% of iron) and an aqueous solution of cobalt sulfate were added. An aqueous calcium solution was added and neutralized with an aqueous sodium hydroxide solution to deposit a cobalt compound and a calcium compound on the surface of the particles. The slurry was filtered and made into a 2% water slurry again, and an aqueous solution of aluminum sulfate was added (Table 1 shows atomic% of Al relative to 100 atomic% of iron). After adding aluminum sulfate and stirring for 20 minutes, a sodium hydroxide aqueous solution was added to neutralize the slurry. After washing with filtered water, a 2% slurry was added and an aqueous neodymium nitrate solution was added (Table 1 shows 100 atomic% of iron.
(Indicated by atomic% of Nd), the pH was adjusted to 8.5 with an aqueous sodium hydroxide solution. It was filtered, washed with water to obtain a 5% water slurry, and heated at 130 ° C. for 30 minutes. After that, the cake obtained by filtering and washing with water was passed through a molding machine and then dried to obtain a spindle-shaped goethite that was subjected to a sintering prevention treatment. The obtained spindle-type goethite was heated in a rotary electric furnace in nitrogen at 450 ° C. for 1 hour to produce hematite. This hematite was dispersed in a water slurry using a sand grinder, washed with water to remove alkali metal ions changed to soluble, and the obtained cake was passed through a molding machine and dried to be used as a raw material for reduction.

The formed hematite was placed in a static reduction furnace and heated in nitrogen at 600 ° C. for 2 hours to enhance the crystallinity of hematite. The temperature was set to 450 ° C., and the gas was switched from nitrogen to hydrogen gas for 30 minutes of reduction. 550 ° C replaced with nitrogen
After heating for 1 hour at 480 ° C., it was switched to pure hydrogen and reduced at 480 ° C. for 5 hours. After switching to nitrogen and cooling to room temperature, change the mixing ratio of air and nitrogen to change the oxygen concentration to 0.5% and gradually oxidize at 50 ° C or lower while monitoring the temperature of the metal powder, and when the heat generation subsides, the oxygen concentration is set to 1%. It was gradually oxidized for 10 hours. Thereafter, air was conveyed while vaporizing distilled water so that the water content was 1% with respect to the metal powder, and the humidity was adjusted and stabilized.

The magnetic characteristics of the obtained ferromagnetic metal particles were measured with a vibrating sample type magnetometer (manufactured by Toei Industry Co., Ltd.) in an external magnetic field of 10 KOe. Taking a high-resolution transmission electron micrograph of the obtained ferromagnetic metal particles, the average major axis length (μm) of the ferromagnetic metal particles,
Average acicular ratio, and ratio of particles with acicular ratio of 8 or more [ΔN
(%)], The average number of crystallites, the average acicular ratio, and the proportion [Δn (%)] of particles having an acicular ratio of 4 or more were determined. In addition, the product was dehydrated in nitrogen at 250 ° C. for 30 minutes, and the specific surface area (S _BET ) was measured with Cantersob (manufactured by Canterchrome) and shown in Table 1.

Production Example 2 Using the elements described in Table 1, the reducing hematite was obtained through the same steps as in Production Example 1, and placed in a static reduction furnace for 60 minutes at 350 ° C. in nitrogen. The mixture was heated and dehydrated, the temperature was adjusted to 450 ° C., the gas was changed from nitrogen to pure hydrogen, and reduction was continuously performed for 6 hours. From this point onward, the same processing as in Production Example 1 was performed. The obtained ferromagnetic metal particles were evaluated in the same manner as in the above Production Example, and the results are shown in Table 1.

[0086]

[Table 1]

Example 1 Production of Magnetic Recording Medium (Examples 1-1 to 7, Comparative Example 1) A magnetic tape having a multilayer structure using the ferromagnetic metal particles obtained in Production Examples 1 and 2 is prepared. Therefore, the following magnetic layer composition and non-magnetic layer composition were prepared. In the following prescriptions, all indications of "part" indicate "part by weight". (Composition of the magnetic layer) ferromagnetic metal particles (Table 2 described) 100 parts binder resin a vinyl copolymer 12 parts chloride (-SO ₃ Na groups and containing 1 × 10 ^-4 eq / g polymerization degree: 300 Polyester polyurethane resin 5 parts (neopentyl glycol / caprolactone polyol / MDI = 0.9 / 2.6 / 1 (molar ratio), -SO ₃ Na group containing 1 × 10 ^-4 eq / g) alpha-alumina (average particle diameter 0. 13 μm) 5.0 parts Carbon black (average particle size 40 nm) 1.0 part Butyl stearate 1 part Stearic acid 2 parts Mixed solvent of methyl ethyl ketone and cyclohexanone 1: 1 200 parts (composition of non-magnetic layer) Spherical titanium oxide 80 parts (Specific surface area by BET method 70 m ² / g average particle diameter 0.024 μm pH 7.5 aluminum treatment Al ₂ O ₃ / TiO ₂ 6.5 wt%) Carbon black 20 parts (average primary particle size 17 nm, DBP and oil amount 80 ml / 100 g surface area by BET method 240 m ² / g pH 5.5) Binder resin vinyl chloride copolymer 12 parts (-SO ₃ Na group 1 x 10 ^-4 eq / g content Degree of polymerization 300) Polyester polyurethane resin 7 parts (Basic skeleton: 1,4-BD / phthalic acid / HMDI = 2/2/1 molar ratio Molecular weight: 10200 Hydroxyl group: 0.23 x 10 ^-3 eq / g containing -SO ₃ Na group: 1 × 10 ^-4 eq / g containing) butyl stearate 1 part stearic acid 2.5 parts Methyl ethyl ketone and cyclohexanone 1: 1 magnetic layer composition of the mixed solvent 200 parts the above and nonmagnetic Each layer composition was kneaded with a kneader and then dispersed using a sand grinder. Add 5 parts to the coating liquid for the non-magnetic layer and 6 parts to the coating liquid for the magnetic layer, and further add methyl ethyl ketone and cyclohexanone 1:
20 parts of 1 mixed solvent was added and filtered using a filter having an average pore size of 1 μm to prepare coating solutions for the non-magnetic layer and the magnetic layer.

The obtained coating liquid for the non-magnetic layer was applied so that the thickness after drying was 1.8 μm, and immediately thereafter, while the coating layer for the non-magnetic layer was still in a wet state, Then, wet simultaneous multilayer coating was performed on a polyethylene terephthalate support having a thickness of 7 μm so that the magnetic layer had a thickness of 0.15 μm, and while both layers were still in a wet state, they were passed through an aligning device for longitudinal alignment. At this time, the oriented magnet is passed through a rare earth magnet (5,000 gauss of surface magnetic flux), then passed through a solenoid magnet (5,000 gauss of magnetic flux), dried until the orientation does not return in the solenoid, and further dried the magnetic layer. Wound up. After that, calendering was performed with a 7-stage calender made of metal rolls at a roll temperature of 90 ° C. to obtain a web-shaped magnetic recording medium, which was slit into a width of 8 mm to prepare an 8 mm video tape sample. Table 2 shows the magnetic characteristics of the obtained sample measured with a vibrating sample magnetometer, the high Hc component, the surface roughness, the output of 1/2 Tb measured using a drum tester, the C / N, and the overwrite characteristic. Fuji DC film Super DC tape was used as the standard for electromagnetic conversion characteristics.

The overwrite characteristic was measured by the following method. Using a drum tester, the relative speed of the TSS head (head gap 0.2 μm, track width 14 μm, saturation magnetic flux density 1.1 Tesla) was 10.2 m / sec,
The optimum recording current is determined from the input / output characteristics of 1/2 Tb (λ = 0.5 μm), and this current is 1/90 Tb (λ = 22.5 μm).
The overwrite characteristic was measured from the erasing rate of 1/90 Tb when the signal of m) was recorded and overwriting was performed at 1/2 Tb.

The magnetic characteristics were measured in parallel with the orientation direction by using a vibrating sample magnetometer (manufactured by Toei Industry Co., Ltd.) with an external magnetic field of 5 kOe. In addition, SQ shows a squareness ratio. The high Hc component was measured by the following method. Set the orientation of the measurement sample of the magnetic recording medium in the same direction as the magnetic field in a vibrating sample magnetometer manufactured by Toei Industry Co., Ltd., apply -10 kOe and DC saturate, then return the magnetic field to zero and remanent magnetization ( -Mrmax) is measured. After applying a magnetic field of 3000 Oe in the opposite direction, returning the magnetic field to zero and measuring the residual magnetization Mr, 10 kOe was applied and DC saturation was applied in the opposite direction, and the residual magnetic field was set to zero.
To measure. It was calculated by the following formula from the obtained residual magnetization.

High Hc component (%) = 100 × (Mrmax−Mr) /
(Mrmax-(-Mrmax)) The magnitude of the magnetic field applied in the opposite direction can be set arbitrarily,
From the viewpoint of detection sensitivity, 3000 Oe is adopted in the present application. The high Hc component represents a component that causes magnetization reversal at a set applied magnetic field or more. Further, the results of Example 1 and Comparative Example 1 are plotted and shown in FIGS. 3 and 4.

For the surface roughness, a 250 μm square sample area was measured using an optical interference three-dimensional roughness meter “TOPO-3D” manufactured by WYKO (Arizona, USA). In calculating the measured values, corrections such as tilt correction, spherical surface correction, and cylinder correction are performed in accordance with JIS-B601, and the center plane average roughness Ra is calculated.
I was defined as the surface roughness value.

[0093]

[Table 2]

[0094]

The average major axis length of the ferromagnetic metal particles is 0.05.
Even if the particle size is as small as 0.12 μm, which is unprecedented, the ferromagnetic metal particles having an acicular ratio of 8 or more can be obtained by controlling the particle size of the crystallites of the starting materials when the particle sizes of the starting materials are well aligned and the metal nuclei are generated. A ferromagnetic metal particle having a high coercive force and an excellent coercive force distribution can be prepared by controlling the ferromagnetic metal particles having an acicular ratio of 4 or more of crystallites of 0% or less to be 17.0% or less. .

The magnetic recording medium using such ferromagnetic metal particles has an excellent overwrite characteristic, reflecting that the output of short wavelength and C / N are excellent and the coercive force distribution is excellent. .

[Brief description of drawings]

FIG. 1 is a diagram for explaining ferromagnetic metal particles used in the present invention.

FIG. 2 is a diagram for explaining conventional ferromagnetic metal particles.

FIG. 3 is a plot of the values of high Hc component (%) with respect to the ratio (%) = ΔN in which the acicular ratio of particles is 8 or more in Example 1 and Comparative Example 1.

FIG. 4 is a plot of the values of high Hc component (%) with respect to the ratio (%) = Δn in which the crystallite acicular ratio is 4 or more in Example 1 and Comparative Example 1.

[Explanation of symbols]

 1 Ferromagnetic metal particle 2 Crystallite

Claims (3)

[Claims] 1. A magnetic recording medium in which a magnetic layer containing at least ferromagnetic metal particles is provided on a non-magnetic support, wherein the ferromagnetic metal particles have an average major axis length of 0.05 to 0.12 μm.
And the ferromagnetic metal particles having an acicular ratio of 8 or more occupy 5.0% or less of all the ferromagnetic metal particles or the acicular ratio of crystallites constituting the ferromagnetic metal particles is 4 or more. A magnetic recording medium, wherein the metal particles account for 17.0% or less of the whole ferromagnetic metal particles. 2. The ferromagnetic metal particles have an average major axis length of 0.
The ratio of the ferromagnetic metal particles having an acicular ratio of 8 or more is 5.0% or less of the whole ferromagnetic metal particles, and the acicular ratio of the crystallites constituting the ferromagnetic metal particles is 4 or more. 17.0% of the total ferromagnetic metal particles are
The magnetic recording medium according to claim 1, wherein: 3. A magnetic recording medium comprising a non-magnetic layer mainly containing an inorganic non-magnetic powder and a binder between the non-magnetic support and the magnetic layer, wherein the dry thickness of the magnetic layer is 0.
The magnetic recording medium according to claim 1, wherein the magnetic recording medium has a thickness of 05 to 1.0 μm.