JPS6025011A - Magnetic head - Google Patents

Abstract

PURPOSE:To obtain a magnetic head having high efficiency by constituting the 1st core to be disposed on the upper stream side of an Fe-Si-Al crystalline alloy and the 2nd core to be disposed on the down stream side of a soft magnetic material having higher magnetic permeability than the 1st core. CONSTITUTION:A soft magnetic material having higher B10 than the 2nd core 23 is used for the 1st core 22 and the sectional area at the tip part 25 where the magnetic flux flows is made narrower than that of the tip part 26 of the core 23 to permit easier magnetic saturation. On the other hand, a soft magnetic material having higher mue than the core 22 is used for the core 23. The magnetic flux of the magnetic field near the part 26 changes sharply as shown by the broken line in the figure. The smaller demagnetizing effect for the record is required for such magnetic flux distribution when a magnetic tape 21 passes and a magnetic head having high efficiency is obtd. An Fe-Si-Al crystalline alloy is adequate as the core 22 and an amporphous alloy of Co-Fe-Si-B or the like is adequate as the core 23. A composite material formed by dispersing uniformly and three-dimensionally at least one kind of the 2nd phase particles in an ultraquickly cooled alloy matrix consisting of an amorphous, crystalline or mixed phases thereof is adequate as the core 23.

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a magnetic head such as a composite magnetic head, and particularly to a core material constituting a magnetic circuit thereof.

Sendust, an iron-silicon-aluminum crystalline alloy made mainly of iron with small amounts of silicon and aluminum added, is used as a core material for magnetic heads because it has a higher saturation magnetic flux density than ferrite materials. is used as.

The magnetic head using this Sendust core also has various excellent characteristics, but the object of the present invention is to provide a magnetic head with even higher efficiency and lower signal distortion.

To achieve this object, the present invention provides magnetic recording.In order to achieve this object, the present invention provides a first core disposed on the upstream side in the transport direction of the magnetic recording medium, and a first core disposed on the downstream side in the transport direction of the magnetic recording medium. A second core disposed in
The groove bottom is made of a soft magnetic material with higher magnetic permeability than the core.

As the first core, an iron-silicon-aluminum crystalline alloy such as sendust, which has iron as a main component and contains small amounts of silicon and aluminum, is suitable.

An amorphous alloy is suitable for the second core. Examples of amorphous alloys include cobalt-iron-silicon-boron alloy, nickel-silicon-boron alloy, iron-molybdenum-carbon alloy, copper-zirconium alloy, and zirconium-boron alloy.
Niobium-silicon alloy.

Iron-boron alloy, iron-niobium-silicon-copper alloy, iron-molybdenum-silicon-boron alloy, cobalt-niobium-boron alloy, etc. are used.

Further, as the second core, a composite material is preferably used, in which at least one second phase particle is uniformly dispersed three-dimensionally in an ultra-quenched alloy matrix consisting of an amorphous, crystalline, or mixed phase thereof. It is.

Examples of the alloy base material constituting the ultra-quenched alloy matrix include cobalt-based alloys such as cobalt-iron alloys containing cobalt as a main component, iron-silicon-boron alloys containing iron as a main component, iron-molybdenum alloys, etc. Nickel-based alloys such as iron-based alloys, nickel-silicon-boron alloys containing nickel as a main component, and various alloys such as copper-zirconium alloys and zirconium-niobium alloys are used.

Examples of the second phase particles include C, WC, Tic, and N.
Carbon or carbides such as bC, nitrides such as NbN and Ta N, C, rz O=+, CeO2+MgO+Z
r0z, YZ O3, WOg'+ Th0z.

AQ20:l, Fez O? I, ZnO, 5iOz
Oxides such as borides such as BN, silicates such as SiC, metals such as Fe, Mo, and W are used.

As mentioned above, the first core is made of, for example, Sendust, but since the method of making this core is well known, the explanation thereof will be omitted here.

Next, an example of manufacturing the second core material will be described.

Figures 1 and 2 are principle explanatory diagrams for explaining the first manufacturing example, Figure 1 is a diagram for explaining the process of making an ingot, and Figure 2 is a diagram for explaining the process of making an ingot. It is a figure for explaining the process of making a core material.

In FIG. 1, an alloy base material 1 constituting an ultra-quenched alloy matrix is heated and melted in a vacuum high-frequency melting furnace 2, and is injected into a mold 3 in an injector 1.Meanwhile, second phase particles 4 are The powder is forcibly added to the molten alloy base material 1 while being injected into the mold 3 by the thermal spray powder feeder 5, and is cooled and solidified as it is to form an ingot in which the second phase particles 4 are uniformly dispersed. is obtained. Second phase particles 4
For the injection dispersion, an injection medium made of an inert gas such as argon gas filled in the cylinder 6 is used.

In order to avoid deterioration of the alloy base material 1 during injection dispersion, it is preferable to use an inert gas such as argon gas as the injection medium.
It's stiff. As a powder feeder for supplying the second phase particles 4, it is possible to always uniformly supply the two-phase powder 4, the injection conditions such as injection pressure can be adjusted to a relatively low level, and the nozzle has excellent heat resistance. Plasma melting n・■
A powder feeder is suitable.

Methods for producing ribbon-like materials using the ultra-quenching method include the roll method, twin roll method, and centrifugation method. These ultra-quenching methods can produce metastable materials that are not in the equilibrium phase diagram, such as amorphous phases, non-equilibrium crystalline layers, or equilibrium crystalline phases, by controlling quenching conditions such as selection of alloy composition or quenching rate. is obtained.

FIG. 2 shows the manufacturing process of creating a ribbon-shaped core material by the twin roll method. The ingot 8 in which the second phase particles are uniformly dispersed is placed in a heat tube 7 made of quartz glass with a nozzle at the lower end, and the inside of the tube is sufficiently replaced with an inert gas 9 such as argon gas. . A high-frequency melting furnace 10 is installed around the outer periphery of the heat-resistant tube 7, and the ingot 1 and 8 are remelted in the melting furnace 104 to such an extent that the second phase particles are not dissolved. Thereafter, the piston 11 is operated to bring the nozzle tip of the heat-resistant tube 7 as close as possible to the joint between the two rolls 12, 12 rotating at high speed, and the gas pressure inside the heat-resistant tube 7 is rapidly increased.

Due to the pressure increase, the remelted ingot 8 is gradually fed from the nozzle as a uniform continuous jet to the joint of the rolls 12. Since the rolls 12, 12 are rotating at high speed and are always in pressure contact, when the molten metal is ejected, it is instantaneously cooled and solidified to obtain a continuous ribbon-shaped core material 13.

FIG. 3 is an enlarged sectional view of this core material 13, in which extremely fine second phase particles 4 are three-dimensionally uniform in a super-quenched alloy matrix 14 consisting of amorphous, crystalline, or a mixed phase thereof. Distributed. The thickness, width, etc. of the core material 13 can be adjusted by varying the circumferential speed and pressing force of the roll 12, the temperature of the melt, the ejection speed, etc.

The twin roll method explained using Fig. 2 has the advantage that the obtained core material has a uniform thickness, has low surface roughness on both sides, and can be easily manufactured into a relatively thick material. Although the twin roll method was used in this manufacturing example, a single roll method may be applied instead.

FIG. 4 is a diagram illustrating the principle of a second manufacturing example of the core 1o according to the present invention.

In a heat-resistant tube 7 made of quartz glass having a nozzle at the lower end,
1. Ultra-quenched alloy 7 trisix. Place an ingot of the alloy base material l to be formed, and replace the inside of the tube with an inert gas 9 such as argon gas.6 Heat-resistant tubes 7 are placed in a high-frequency rotary-force T furnace 4 on the outer periphery.
is installed, and the ingot of the alloy base material 1 is melted in the i8 melting furnace 4 to such an extent that the second phase particles 4, which will be described later, are not melted. Thereafter, the piston 11 is actuated to bring the nozzle tip of the heat-resistant tube 7 as close as possible to the upper peripheral surface of the roller 6 that is rotating at high speed, and the inert gas pressure inside the heat-resistant tube 7 is rapidly increased. The molten alloy mother 441 is supplied to the surface of the roll 6 from a nozzle as a thin uniform continuous jet due to the pressure increase.

The second phase particles 4 are forcibly added to the jet stream of the alloy base material 1 from the heat-resistant tube 7 together with a jetting medium such as argon gas by a powder feeder 5 for plasma spraying. The alloy base material 1 in a molten state to which the second phase particles 4 have been added is rapidly solidified while being stretched on a roll 12 to obtain a continuous ribbon-shaped core material 13.

Similarly to the core material 13 obtained in this way, as shown in FIG. .

The single roll method explained using FIG. 4 has the advantage that a relatively wide and thin film can be easily obtained. In this production example, a single roll method was used, but a twin roll method may be applied instead.

FIG. 5 is a principle explanatory diagram for explaining a third manufacturing example of the core material according to the present invention.

An ingot of the alloy base material 1 constituting the ultra-quenched alloy matrix is placed in a heat-resistant tube 7 made of quartz glass having a nozzle at the lower end, and the inside of the tube is sufficiently replaced with an inert gas 9 such as argon gas. A high-frequency melting furnace 10 is installed around the outer periphery of the heat-resistant tube 7, and the ingot of the alloy base material 1 is melted by the melting furnace 10 to such an extent that second phase particles 4, which will be described later, are not melted.

Thereafter, the piston 11 is actuated to rapidly increase the inert gas pressure within the heat-resistant tube 7, and the molten alloy base material 1 is transferred to the molten metal reservoir 15 disposed below.

The second phase particles 4 are forcibly added to the jet stream of the alloy base material 1 from the heat-resistant tube 7 from the plasma spray powder feeder 5 . A high frequency melting furnace 16 is also installed on the outer periphery of this molten metal reservoir 15.
is attached, and the molten state of the alloy base material 1 is maintained.

In this way, the alloy base material 1 containing the second phase particles 4 is
The roll 12.
The core material 13 is supplied as a thin, uniform continuous jet to the joints of the core material 12, and is ultra-quenched in the same manner as in the production example described above to obtain a continuous ribbon-shaped core material 13.

Similar to the core material 13 shown in FIG. 3, extremely fine second phase particles 4 are three-dimensionally uniformly dispersed in the ultra-quenched alloy matrix 14. Note that although a twin roll method was used in this manufacturing example, a single roll method may be applied instead.

When making an ingot of the alloy base material constituting the ultra-quenched alloy matrix, or when remelting the ingot for ultra-queue cooling, the second phase particles are not used in the molten state without using the jet dispersion method described above. It is also possible to simply add it to the alloy matrix, stir it with high frequency, and then ultra-quench it to three-dimensionally disperse the second phase particles in the alloy matrix.

However, this method has limitations on the types of second phase particles that can be applied and the amount that can be dispersed. In particular, the second phase particles are, for example, C
In the case of metal oxides such as rzO9 and CeOz, iron,
The wettability of molten metals such as cobalt and nickel tends to be dispersed in very small amounts and unevenly distributed in the surface layer of the super-quenched alloy matrix.

The interfacial phenomenon that occurs when the second phase particles are added to and dispersed in the alloy base material in the molten state can be considered in the following two stages. That is, in the first step, the second phase particles come into contact with the molten alloy base material, and at this time, the liquid phase of the molten alloy base material, the same phase of the second phase particles, and argon gas (inert gas) etc. It is a three-phase gas phase system. The second stage is a stage in which the second phase particles are suspended in the molten alloy matrix, in which case the liquid phase of the molten alloy matrix and the second
It is a two-phase system of in-phase particles.

Furthermore, the three-phase interfacial phenomena described above can be roughly divided into three types: adhesion wetting, expansion wetting, and immersion wetting. If the work when adhesion wetting occurs is Wa+the work when extended wetting occurs is Ws, and the work when immersion wetting occurs is Wi, then the definition is as follows.

Wa=γsv−γ5L+γLV−(1)Ws=γ
sv-γSL-γLv ゛(2)Wi=γsv-γ5L
・=<3) However, in the formula, γsL: Solid phase-liquid phase interfacial tension γSL: Solid phase interfacial tension γLv: Liquid phase interfacial tension At the gas phase-solid phase and liquid phase-solid phase interface, the surface of the same phase Since it is considered that there is almost no deformation, the following equation (4) holds true if the contact angle with the liquid phase is θ.

γSV−γsL=γLv+cosθ−(4) Substituting this into the above equations (1), (2), and (3), respectively, gives the following equations.

Wa=γL (CO5θ+1) ... (5) Ws=
y L (Cogθ-1> −(6) Wi = γLv'
CO5θ −(7) In these equations, wettability occurs when W is positive.

As is clear from the above equations (5) to (7), in the first stage when the second phase particles come into contact with the molten alloy base material, the contact angle θ of the second phase particles with respect to the alloy base material is It has a lot to do with sexuality. For molten metals such as iron, cobalt and nickel.

Generally, metal oxides have a large contact angle θ and therefore have poor wettability.

Therefore, if the second phase particles are simply added to the molten alloy base material and stirred under high frequency, the so-called alloy base material and the
The phase particles do not fit well, and the second phase particles tend to be unevenly distributed on the surface layer side of the alloy base material. For this reason, when metal oxides are used as second phase particles, the amount that can be dispersed in one alloy base material is at most about 0.1% by volume, and the amount of one dispersion is extremely small. The effect of addition cannot be fully demonstrated.

In this regard, as mentioned above, when making an ingot of alloy base material,
Alternatively, when melting the ingot for ultra-quench cooling, if a method is adopted in which the second phase particles are added to the molten alloy base material using the injection dispersion method, the second phase particles will be added to the alloy by strong injection energy. It is mechanically pushed into the base material.

Therefore, even second phase particles with poor wettability to the alloy base material can be forcibly and uniformly dispersed, making it possible to
There is also a margin in the type of phase particles and the amount that can be dispersed, which greatly contributes to improving the properties and functions of the core material.

An example of the contact angle of the same phase with respect to the gold layer melt is shown in Table 1 below.

As is clear from this table, gold-Mt oxide generally has a larger contact angle than other similar phases, and metal melt Example 1 (CO7o, 5Fe4.5Six gBx o) g9.
s (WC)0.5(CO7o, 5Fe45si111
B10) 9 s (IIC) 1 (Coyo, 5Fe4
5si1 sBx o)se (VC)3(CO7o
,gFea,5si1sBx O)9s (VC)s
(CO7o, 5Fe4・5si1-i81o) so
(uc)lO A core material made of a second phase particle-dispersed ultra-quenched alloy having the above composition formula is prepared. The composition of the ultra-rapidly solidified alloy is shown in parentheses on the left in the above compositional formula, the numbers at the bottom right of each element indicate atomic %, and the second phase particle constituents are shown in parentheses in the compositional formula. The numbers at the bottom right of both parentheses each represent the volume percent of 9. The other examples also adopted the same display method as the smell.

Next, the specific creation procedure will be explained. First, in order to obtain the composition of the desired ultra-quenched alloy, the constituent metals G o are determined.

Fe, Si, B Go 420.9g, Fe 22.
Weigh 9 pieces each to give 5g, 42.7g of 5i, and 110g of B.

These are melted together in a vacuum high-frequency melting furnace 2 (see FIG. 2) to produce an alloy base material 1 in a molten state.

This alloy base material 1 is poured into a mold 3 as it is.

On the other hand, WC fine powder (second phase particles 4) is filled in advance in a #I powder mill 5 for plasma spraying, and is injected into the mold injection stream of the alloy base material 1 by high pressure argon gas from a cylinder 6. be done. The injection amount of the WC fine powder is adjusted by the powder feeder 5 so that the volume % of the alloy base material 1 is expressed by the above-mentioned compositional formula. The temperature of the alloy base material 1 when injected into the M-type 3 is such that it maintains its molten state and
The temperature of the WC fine powder, which is a phase particle, is adjusted so that it does not melt, that is, about 1200°C.

The WC fine powder that is forcibly injected toward the mold injection flow of the molten alloy base material 1 is dispersed in the alloy base material 1 in a finely divided state without becoming a soul, and the distance between the particles is short. .

In this way, the fine WC powder dispersed in a fine state without coarsening has a slow floating speed in the alloy base material 1, so that it may segregate when the alloy base material 1 solidifies in the mold 3. The single-dispersion state is stable. For this reason, Go-Fe-8i with uniformly dispersed WC powder
An ingot 8 made of a -B alloy is obtained.

Next, as shown in FIG. 2, this ingot 8 is placed in a heat-resistant tube 7 made of quartz glass, the inside of the tube is sufficiently replaced with argon gas 9, and then the ingot 8 is melted in a high-frequency melting furnace 10. At this time as well, the temperature is maintained at a level that does not dissolve the WC fine powder, that is, about 1200°C. Then piston 11
is activated to bring the lower end nozzle of the heat-resistant tube 7 as close as possible to the joint between the two rollers 12 and 12 rotating at high speed, and the argon gas pressure inside the heat-resistant tube 7 is rapidly increased to remove the ingot 8 from the nozzle. Roll 12.1 as a uniform continuous jet
2 joints. Since the rolls 12 and 12 rotate at high speed while being cooled and are constantly pressed against each other, the ejected alloy base material is instantly cooled and solidified to a width of 40 am and a thickness of 30 μm.

A ribbon-shaped core material 13 having a length of 5 m is obtained.

When the surface and the cut surface in the thickness direction of this core material 13 were observed using a scanning electron microscope, it was found that the fine WC powder was aggregated with each other at short intervals in the ultra-quenched alloy matrix, resulting in coarse particles. They are uniformly dispersed individually as fine particles without forming into particles, and there are no pores at all. This confirmed that the WC fine powder was three-dimensionally uniformly dispersed in the alloy matrix. Furthermore, it was confirmed by X-ray diffraction that this ultra-quenched alloy matrix alloy was amorphous.

This core material 13 is continuously punched into a predetermined shape, and a predetermined number of sheets are laminated to form a second core.

Example 2 (Niy, e Six o B x z) @y
(WC)s(Niy s Six o B :L 2
)! z (WC)e(Niy e Six o B
x z ) 8z (WC)x.

A core material made of a second phase particle-dispersed ultra-quenched alloy having the above composition formula is prepared.

Next, the specific creation procedure will be explained. First, the constituent metal N i to obtain the desired composition of the ultra-quenched alloy.

Si, B&Ni 459 g, 5128 g + 813 g were weighed, respectively, and these 4 L were melted in a vacuum high-frequency melting furnace to create an alloy base material, which was poured into a G-type.

WC fine powder (second phase particles) is injected from a plasma spray powder feeder together with low-pressure argon gas into the flow of the alloy base material 1, and then cooled to uniformly disperse the WC fine powder. - Making an ingot made of B-based alloy.

If the temperature of the alloy base material is adjusted to approximately 120°C when the WC fine powder is sprayed and dispersed, the added WC fine powder will not dissolve in the alloy base material and will be uniformly dispersed as fine particles. Ru.

The ingot is placed in a heat-resistant tube placed directly above one roll, and the inside of the tube is sufficiently replaced with argon gas. Then, a high frequency melting furnace installed around the outer circumference of the heat-resistant tube melts the
The alloy is heated and maintained at 00°C, and only the alloy base material is remelted. Thereafter, the argon gas pressure within the heat-resistant tube is rapidly increased, and the molten alloy base material containing fine WC powder is jetted from the lower nozzle of the heat-resistant tube onto a roll rotating at 2000 r, p, m.

When ejected, it instantly cools and solidifies to a width of 40mm.

A ribbon-shaped core material with a thickness of 30 μm and a length of 5 m is obtained.

When the surface and the cross section in the thickness direction of this core material were observed with a scanning electron microscope, it was found that the WC fine powder was uniformly dispersed as fine particles in the ultra-quenched alloy matrix, as in the previous example. In addition, this ultra-quenched alloy matrix is
It was confirmed by diffraction that it was amorphous.

This core material is continuously punched into a predetermined shape, and a predetermined number of sheets are laminated to form a second core.

Example 3 (CO7o, 5Fe4.5siz sBx O)99.
9 (CrzOs) o, l (Coy o, 5Fe4.5
511gB1'o)e s4 (Crz(h)o,a
(Coyo, 5Fea, 5six gei o)9
s, s (CrzO:I) o, s (Coy o) Fe(
ssii gBlo)s g(CrzOs)z(Coy
o, 5FeaSsixsBxo)9y (CrzO3)
+4 A core material made of a second phase particle dispersed ultra-quenched alloy having the above compositional formula is used.

Example 4 (Coyo, gFe4sSi1sBzo)99. e
a (CaO2)0.1(Cot o, g, FeA, s
5i1s Blo )99.7 (Ce0z )0.
3(CO7o,gFe45Six 5BIO)9s
,s (Ce0z)o,g(Cot o,gFe(ss
ils Olo)9 g(Ce0z)x(Coy
o, 5Fe45sxx sBx o)s y (Ce0
z)i A core material made of a second phase particle-dispersed ultra-quenched alloy having the above compositional formula is used.

Example 5 (Co7o,sFe4.s5i1sBio)g
9,9 (WO3)o, 1(CO7o, 5Fe4.5s
iz sBz O)99.7 (WO:+)o3(C
oy o, s Fea, s Six c+ B10)
91M (WO3)O,S(Co7o,sFe+,5s
i1sB10)9 g, (WO:l)1(Coyo
, +; Fea, 5Six 581 0)9 7' (W
ool ): 1 A core material made of a second phase particle-dispersed ultra-quenched alloy having the above compositional formula is used.

Example 6 (Coy O, 5Fe4.s Sil sBio)
s9,9 (ZrOz)o4(Coto,5Fe
4',s SiI S'BI O)9 s,y (Zr
Oz)o,s(Co70.!l FeasSils
th O)99! I(ZrOz) a, s(Coy o
5Fea, 5six gBz o)'s s (Zr
O2) 1(Cot o, 5Fe44si1 sBlo
)9-, ``(ZrOz):l A core material made of a second phase particle-dispersed ultra-quenched alloy having the above compositional formula is used.

Example 7 (Coy o gFe(ssix !5Bx O)9
g, s (Y2 0:+) o, IC-Coy o F-
Fea, 5si1 sBlo)e 9. −, (Y2
03) 0.11 (Coyo, 5FeA, 5siz s
B□ o) 9 s, 5 (Y2 0:l). 5 (CO7
o, 5Fe(ssiz sBx O)911' CY
z Oy+ )z(Co7o, 5Fea, 5sixsB
1o) 9A CYzO3)s A core material made of a second phase particle-dispersed ultra-quenched alloy having the above compositional formula is used.

Example 8 (Niy day Si lo B I Z) go
'(ThOz)x.

(Ni7s 5i1o Bx 2 ) e o (ThO
z)z.

A core material made of a second phase particle-dispersed ultra-quenched alloy having the above compositional formula is used.

Example 9 (Niy g Six o B 1s ) s s (T
ic)s(Niy t-5i1o B x II)s
o (T'1C)x.

A core material made of a second phase particle-dispersed ultra-quenched alloy having the above compositional formula is used. In addition, at the Scanning Electron Microscope AM Festival, Ti
C is 3 in the Ni-5t-B super-quenched alloy matrix.
It was confirmed that the alloy matrix was dimensionally uniformly dispersed, had no pores, and was amorphous by X-ray diffraction.

Example 10 (Fe:i 91.4 MO9Cx, a) s s (
NbC)z(Fea 9.J Mos C1,a)s
s(NbC)s(Fe39.4 MogC3r,
)s o (NbC)i.

A core material made of a second phase particle-dispersed ultra-quenched alloy having the above compositional formula is used. In addition, by scanning electron microscopy observation, Nb
C is 3 in the Fe-Mo-C super-quenched alloy matrix.
Dimensionally uniform dispersion, no pores, and X-ray diffraction confirmed that the alloy matrix was a non-equilibrium γ-austenite single phase with an ultrafine grain structure. This nonequilibrium γ−
Since the austenite phase is a crystalline alloy, it has higher thermal stability than amorphous alloys.

Example 11 (Cua o Zra o )@o (SiC)+r
.

(Cua o Zr4 o )y' o (,5iC)
:+.

A core material made of a second phase particle-dispersed ultra-quenched alloy having the above compositional formula is used. In addition, by scanning electron microscopy observation, Si
It was confirmed that C was uniformly dispersed three-dimensionally in the Cu-Zr-based ultra-quenched alloy matrix, there were no pores, and that the alloy matrix was amorphous by X-ray diffraction.

Example 12 (Ni7e 5i1o Blz)so(BN)1゜(
Niy s 5i1o B12 )e o (BN)2
.

A core material made of a second phase particle-dispersed ultra-quenched alloy having the above compositional formula is used. Furthermore, by scanning electron microscopy observation, BN
was uniformly dispersed three-dimensionally in the super-quenched Ni-8i-B alloy matrix, there were many pores, and it was confirmed by X-ray diffraction that the alloy matrix was amorphous.

Example 13 (Zr4sNb4o 5ii5)s o(NbN)z.

A core material made of a second phase particle-dispersed ultra-quenched alloy having the above compositional formula is used. In addition, by scanning electron microscopy observation, Nb
It was confirmed that N was uniformly dispersed three-dimensionally in the Zr-Nb-8i-based ultra-quenched alloy matrix, there were no pores, and that the alloy matrix was amorphous by X-ray diffraction.

Example 14 (Coy o,s Fe4.s Six g B lo
)e s (C)l(CO7o, s Fe4.s 5
iii;B 1o )s s (C)g(C:oy o
5 Fe4. s Six's B x o ) s o
(C)x.

A core material made of a second phase particle-dispersed ultra-quenched alloy having the above compositional formula is used. Furthermore, scanning electron microscopy reveals that C is three-dimensionally uniformly dispersed in the Co-Fe-8i-B super-quenched alloy matrix, there are no pores, and X@ diffraction reveals that the alloy matrix is amorphous. It was confirmed.

Example 15 (Fes2Bxe)ss(Fe)i(Fe
s z B 18) s s (Fe)2 A core material made of a second phase particle-dispersed ultra-quenched alloy having the above compositional formula is used. Furthermore, scanning electron microscopy revealed that Fe is Fe -B
It was confirmed by X-ray diffraction that Alloy 71-Rix was an amorphous invar alloy, which was uniformly dispersed three-dimensionally in the ultra-quenched alloy matrix of the system.

Figure 6 is a particle size distribution diagram of the second phase particles in the ultra-quenched alloy matrix, where (a) is TiC and (b) is W.
(c) uses CrzOi, and (d) uses Zr0z as the second phase particles, and Co is deposited by the injection dispersion method.
yo, 5Fe4.5Six 5B 1o-based ultra-quenched alloy matrix, and the particle size was measured using an electron microscope. The average particle size of each of these second phase particles was about 0.06 μm. As is clear from these figures, about 70% of the dispersed second phase particles
The particle size of the above particles is less than about 0.1 μm,
In order to disperse the second phase particles in the form of ultrafine particles as described above, it is necessary to appropriately adjust the particle size of the second phase particles before addition and the conditions for spraying them.

The following Table 2 shows the ultra-quenched alloy matrix (CO7o, s Fe (5Six s B x o )
It is a table showing the average particle size of other second phase particles in the sample.

Table 2 If it is, the dispersion state of the second phase particles is stable even in the molten alloy base material. That is, at the stage where the second phase particles are suspended in the molten alloy base material, a dispersion system exists in which the alloy base material is the dispersion medium and the second phase particles are the dispersoid. Since this dispersion system is thermodynamically unstable, the free energy change ΔF is largely involved in the dispersion or aggregation of the second phase particles. Generally, the free energy change ΔF includes a change in interfacial free energy, a change in energy, and a change due to a chemical reaction. By the way, when the alloy base material in the molten state and the second phase particles are in an equilibrium state, the free energy change due to the chemical reaction is considered to be zero, so the dispersion state of the second phase particles depends on the change in the interfacial free energy. It will be controlled.

The dispersion of the second phase particles in the molten alloy matrix eliminates the in-phase (second-phase particles)-solid phase (second-phase particles) interface, resulting in the dispersion of the in-phase (second-phase particles) and liquid phase (molten alloy matrix). ) is a change in which an interface is formed. Therefore, the change in interfacial free energy ΔFs at this time is defined as in the following equation (8). Note that γss in the formula is the interfacial tension at the solid phase-solid phase interface.

ΔFs=2γSL−γss ”'Cs) From this formula, 8F
If the value of s is negative, the second phase particles will be dispersed or naturally clouded with S in the molten alloy base material, and if the value is positive, they will aggregate.

In order to make the change in interfacial free energy ΔFs negative when changing from the solid phase-solid phase interface to the same phase-liquid phase interface, it is necessary to make the particle size of the second phase particles as small as possible. Approximately 7 of the second phase particles are dispersed as described above.
If the particle diameter of 0% or more, preferably 90% or more, is less than about 0.1 μm, the second phase particles do not aggregate with each other, are stable in a dispersed state, and are uniformly dispersed.

FIG. 7 is a plan view of the magnetic head according to the present invention. The first core 22 is arranged on the upstream side in the transport direction (arrow A) of the magnetic tape 21, and the second core 23 is arranged on the downstream side.
A head gap is formed by a spacer 24 made of glass. The magnetic flux cross-sectional area of the tip 25 on the head gap side of the first core 22 is formed to be narrower than the magnetic flux cross-sectional area of the tip 26 of the second core 23 on the head gap side. The first core 22 includes
A bobbin 28 wound with an excitation coil 27 is attached to constitute a magnetic head.

The first core 22 is made of an iron-silicon-aluminum crystalline alloy (Sendust) having a silicon content of 9.6% by weight, an aluminum content of 5.4% by weight, and the balance being iron.

On the other hand, the second core 23 is made of the second phase particle-dispersed ultra-quenched amorphous alloy (Coyo, S F
e4. s S ils B1 o) 9e(WC) z
It is made by punching thin core materials into a predetermined shape and laminating them. First core 22 and second core 23
A comparison of the magnetic properties is shown in Table 3 below.

Table 3 As is clear from this table, the first core 22 uses a soft magnetic material with a higher Bzo than the second core 23, and as described above, the magnetic flux flow cross-sectional area of the tip 25 is the same as that of the second core 23. It is made narrower than that of the tip 26 of the core 23 so as to be easily magnetically saturated. On the other hand, the second core 23 uses a soft magnetic material with a higher μe than the first core 22.

Therefore, when recording with this magnetic head, the tip 25 of the first core 22 becomes magnetically saturated at first, and the magnetically saturated region gradually expands toward the upstream side in the tape transport direction. Therefore, the field magnetic flux near the tip 25 is
It is gentle as shown by the broken line in the figure.

On the other hand, the second core 23 has a much higher magnetic permeability μ than the first core 22, and the magnetic flux distribution cross section of the tip 25 is wide, so the field magnetic flux near the tip 26 is as follows:
As shown by the broken line in FIG. 7, the change is very steep. With such a magnetic flux distribution between the first core 22 and the second core 23, there is less recording demagnetization effect when the magnetic tape 21 passes therethrough, and a highly efficient magnetic head can be obtained.

FIG. 8 is a characteristic diagram showing the relationship between the bias current and the third harmonic distortion factor of the magnetic head X having the above-mentioned configuration and the magnetic head Y using Sendust in the first core and the second core. . As is clear from this figure, the magnetic head X according to the present invention has a smaller signal distortion than the conventional magnetic head Y, for example, when the third harmonic distortion is taken as a standard of 3%.

The magnetic head X according to the present invention requires a lower bias current.

FIG. 9 is a characteristic diagram showing the relationship between bias current and output level of the magnetic heads X and Y. As is clear from this figure, in order to obtain a signal with a desired output level, the magnetic head X according to the present invention requires a lower bias current than the conventional magnetic head Y. In this case, the magnetic head X according to the present invention can obtain a higher output.

Note that the second core 23 is (CO7o, o F e4.s S i s, x B2
o, a) 9! B
10 to 8800, that is, to the same level as Sendust that makes up the first core 22,
Furthermore, μ is maintained higher than that of the first core 22, making it possible to record with high efficiency and high density.

The present invention has the above-described configuration, and can provide a highly reliable and highly efficient magnetic head.

[Brief explanation of the drawing]

1 and 2 are principle explanatory diagrams showing a first manufacturing example of the core material according to the present invention, FIG. 3 is an enlarged sectional view of the manufactured core material, and FIG. 4 is a core material according to the present invention. FIG. 5 is a principle explanatory diagram showing a second manufacturing example of the core material according to the present invention. FIG. 6 is a principle explanatory diagram showing a third manufacturing example of the core material according to the present invention.
), (d) are particle size distribution diagrams of second phase particles in the alloy matrix, FIG. 7 is a plan view of the magnetic head according to the present invention, and FIG. 8 is the bias of the magnetic head according to the present invention and the conventional magnetic head. A characteristic diagram showing the relationship between current and third harmonic distortion rate. FIG. 9 is a characteristic diagram showing the relationship between bias current and output level of the magnetic head according to the present invention and the conventional magnetic head. ■... Base metal base material, 4... Second phase particles,
13... Core material, 14... Ultra-quenched alloy matrix, 21... Magnetic tape, 22...
...First core, 23 ...Second core, 2
4...Spacer (head gap), 25.2
6...Tip, A...Transfer direction Fig. 1 Fig. 2 Fig. 3 Fig. 4 Fig. 4 Fig. 5 Fig. 6 Xunzi Xu (XIO) Im) Fig. 7 Fig. 8 Figure 9 Bias current (mA) Procedural amendment (method) November 7, 1980 Commissioner of the Japan Patent Office Kazuo Wakasugi 1, Indication of the case 1982 Patent Application No. 132908 2, Invention Name: Magnetic head 3, person making the amendment Relationship to the case: Applicant 4, attorney (1) "Figure 6 Ca on page 39, line 9 of the specification"
(b)l (C). (First, extract month d to "Figure 6". 61

Claims (25)

[Claims] (1) The first one located on the upstream side in the transport direction of the magnetic recording medium.
and a second core disposed on the downstream side in the transport direction of the magnetic recording medium are provided so as to face each other across a head gap, and the second core has a magnetic permeability higher than that of the first core. A magnetic head characterized by being implanted with a soft magnetic material. (2) The magnetic head according to claim (1), wherein the first core has a higher magnetic flux density than the second core. (3) The magnetic head according to claim (1), wherein the first core and the second core are made of a soft magnetic material having substantially the same magnetic flux density. (4) Claim (1) characterized in that a cross-sectional area of magnetic flux on the head gap side in the first core is narrower than a cross-sectional area of magnetic flux on the head gap side in the second core. The magnetic head described in Section 1. (5) The first core is made of an iron-silicon-aluminum alloy containing iron as a main component and small amounts of silicon and aluminum, and the second core is made of an amorphous alloy. A magnetic head according to claim (1) or (4). (6) The second core is made of a composite material in which at least one second phase particle is uniformly dispersed three-dimensionally in an ultra-quenched alloy matrix consisting of an amorphous, crystalline, or mixed phase thereof. Claim No. 1 (1) characterized in that
) or (4). (7) The magnetism according to claim (6), wherein the first core is made of an iron-silicon-aluminum alloy containing iron as a main component and small amounts of silicon and aluminum. head. (8) The magnetic head according to claim (6), wherein the super-quenched alloy matrix is made of cobalt. (9) The magnetic head according to claim (6), wherein the super-quenched alloy matrix is a nickel-based amorphous alloy containing nickel as a main component. (10) The magnetic head according to claim (6), wherein the super-quenched alloy matrix is an iron-based amorphous alloy containing iron as a main component. (11) The magnetic head according to claim (6), wherein the second phase particles are carbide. (12) The magnetic head according to claim (11), wherein the second phase particles are diluted tungsten. (13) The magnetic head according to claim (6), wherein the second phase particles are carbon. (14) The magnetic head according to claim (6), wherein the second phase particles are oxides. (15) The magnetic head according to claim (14), wherein the second phase particles are chromium oxide. (16) The magnetic head according to claim (6), wherein the second phase particles are nitride. (17) The magnetic head according to claim (6), wherein the second phase particles are silicate. (18) The magnetic head according to claim (6), wherein the second phase particles are metal. (19) A claim characterized in that, of the second phase particles uniformly dispersed in the ultra-quenched alloy matrix, about 70% or more of the second phase particles have a particle size of less than about 0.1 μm. The magnetic head according to item (6). (20) The magnetic head according to claim (6), wherein the composite material is made of thin plate members, and the core is constituted by a laminate in which a predetermined number of these thin plate members are laminated. (21) The composite material is tested by heating the alloy base material constituting the super-quenched alloy matrix, and then, before the alloy base material solidifies, the second phase particles are injected together with an injection medium consisting of an inert gas. spraying and dispersing the second phase particles onto the alloy base material together with the alloy base material injection medium;
The patent is characterized in that it is a composite material obtained by cooling the ingot to create an ingot in which the second phase particles are uniformly dispersed, and then remelting this ingot to such an extent that the second phase particles do not dissolve and solidifying it by ultra-rapid cooling. A magnetic head according to claim (6). (22) The composite material heats and melts the alloy base material constituting the ultra-quenched alloy matrix to such an extent that the second phase particles do not dissolve, and before the alloy base material solidifies, an injection of an inert gas is applied. The magnetic head according to claim (6), wherein the magnetic head is a composite material obtained by spraying and dispersing second phase particles together with a medium onto the base metal base material, and then solidifying it by ultra-rapid cooling. . (23) The magnetic head according to claim (21) or (22), wherein the second phase particles are a metal that has poor wettability with respect to the super-quenched alloy matrix. (24) The second phase particles are chromium oxide. (25) A claim characterized in that, of the second phase particles uniformly dispersed in the ultra-quenched alloy matrix, about 70% or more of the second phase particles have a particle size of less than about 0.1 μm. The magnetic head according to item (21) or item (2z).