JPH1091921A - Dual spin bulb-type thin film magnetic head - Google Patents

Abstract

PROBLEM TO BE SOLVED: To produce a dual spin bulb-type thin film magnetic head having good characteristics as a thin film magnetic head by using a PtMn alloy layer or a PdMn alloy or Pt-Mn-X alloy (wherein X is Ni, Pd, Rh, etc.,) having almost the same properties as those of PtMn to form an antiferromagnetic layer. SOLUTION: The antiferromagnetic layer 4 is formed by using a PtMn alloy or a PdMn alloy or Pt-Mn-X alloy (wherein X is Ni, Pd, Rh, Ru, Ir, Cr, Fe and Co) having almost the same properties as those of PtMn. Thereby, a dual spin bulb-type thin film magnetic head can be obtd. and in this head, an effective exchange anisotropic magnetic field can be obtd. without depending whether the antiferromagnetic layer 4 is formed on or under a spin magnetic layer 3. By this method, the temp. of heat treatment to generate exchange coupling by the antiferromagnetic film 4 can be decreased. The obtd. dual spin bulb-type thin film magnetic head has such properties that diffusion on the interfaces between a nonmagnetic conductive layer 2 and a free magnetic layer 1 or the spin magnetic layer 3 can be prevented and a high change rate of resistance can be obtd.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a free (Fr) which is affected by the direction of magnetization of a pinned magnetic layer and an external magnetic field.
ee) A so-called spin-valve thin-film magnetic head in which the electric resistance changes in relation to the direction of magnetization of the magnetic layer, wherein an antiferromagnetic layer is laminated on each of the pinned magnetic layers located above and below the free magnetic layer. The present invention relates to a dual spin valve thin film magnetic head.

[0002]

2. Description of the Related Art A magnetoresistive read head employs an MR (Magnetoresistiv) using an element exhibiting a magnetoresistive effect.
e) G using head and element showing giant magnetoresistance effect
There is an MR (Giant Magnetoresistive) head. The MR head has a single-layer structure of a magnetic material exhibiting a magnetoresistance effect. On the other hand, the GMR head has a multilayer structure in which layers exhibiting a magnetoresistance effect are formed by combining a plurality of materials. There are several types of structures that produce the giant magnetoresistance effect. Among them, the spin valve method has a relatively simple structure and a high rate of change in resistance to an external magnetic field. The spin valve method includes a single spin valve method and a dual spin valve method.

FIG. 8 shows a single spin-valve thin film magnetic head, in which a free magnetic layer 1, a nonmagnetic conductive layer 2, a pinned magnetic layer 3, and an antiferromagnetic layer 4 It is composed of layers. Reference numerals 5 and 5 located on both sides are hard bias layers. 6, 7 is Ta
An underlayer and a protective layer made of a non-magnetic material such as (tantalum), and 8 is a conductive layer. The coercive force of the pinned magnetic layer 3 is set higher than the coercive force of the free magnetic layer 1. The pinned magnetic layer 3 and the antiferromagnetic layer 4 are formed in contact with each other,
The pinned magnetic layer 3 is made into a single magnetic domain in the Y direction by an exchange anisotropic magnetic field due to exchange coupling at the interface with the antiferromagnetic layer 4, and the direction of magnetization is fixed in the Y direction. The exchange anisotropic magnetic field is generated at the interface between the antiferromagnetic layer 4 and the pinned magnetic layer 3 by performing a heat treatment while applying a magnetic field.

Further, under the influence of the hard bias layer 5 magnetized in the X direction, the magnetization direction of the free magnetic layer 1 is aligned in the X direction. Since the free magnetic layer 1 is formed into a single magnetic domain in a predetermined direction by the hard bias layer 5, the occurrence of Barkhausen noise can be prevented. In this single spin valve type thin film magnetic head,
A steady current is applied from the conductive layer 8 to the free magnetic layer 1, the nonmagnetic conductive layer 2, and the pinned magnetic layer 3. The running direction of a magnetic recording medium such as a hard disk is the Z direction, and when a leakage magnetic field from the magnetic recording medium is applied in the Y direction, the direction of magnetization of the free magnetic layer 1 changes from the X direction to the Y direction. . A change in the direction of magnetization in the free magnetic layer 1 and
The electric resistance changes in relation to the fixed magnetization direction of the pinned magnetic layer 3, and a leakage magnetic field from the magnetic recording medium is detected by a voltage change based on the change in the electric resistance value.

FIG. 1 is a sectional view showing a dual spin valve type thin film magnetic head. In the dual spin valve type, the nonmagnetic conductive layers 2 and 2, the pinned magnetic layers 3 and 3, and the antiferromagnetic layer 4
4 are stacked. The direction of magnetization of the free magnetic layer 1 is aligned in the X direction by the hard bias layer 5, and the direction of magnetization of the pinned magnetic layers 3 and 3 is aligned with the pinned magnetic layers 3 and 3.
Is exchanged by an exchange anisotropic magnetic field at the interface between the magnetic layer and the antiferromagnetic layers 4 and 4, and is fixed in a single magnetic domain in the Y direction.

When the magnetization direction of the free magnetic layer 1 changes from the X direction to the Y direction due to the leakage magnetic field in the Y direction from the recording medium, the electric resistance value changes.
In the spin-valve thin-film magnetic head, the free magnetic layer 1
When the magnetization direction of the magnetic layer changes from the X direction to the Y direction, electrons moving from one layer to the other layer between the free magnetic layer 1 and the pinned magnetic layer 3 make free electrons move to the nonmagnetic conductive layer 2. Scattering occurs at the interface with the magnetic layer 1 or at the interface between the nonmagnetic conductive layer 2 and the pinned magnetic layer 3 to change the electric resistance. The voltage change based on the change in the electric resistance value causes a change in the electric resistance from the magnetic recording medium. A leakage magnetic field is detected.

When the angle between the direction of magnetization of the free magnetic layer 1 and the direction of magnetization of the pinned magnetic layer 3 is maximized, ie, when the angle is antiparallel, the electric resistance exhibits a maximum value, When the direction of magnetization of the layer 1 and the direction of magnetization of the pinned magnetic layer 3 become the same, the electric resistance shows the minimum value. When a leakage magnetic field from the recording medium is applied, the larger the resistance change rate {(maximum voltage value-minimum voltage value) / minimum voltage value}, the better the characteristics of the thin-film magnetic head.

In the single spin-valve thin-film magnetic head shown in FIG. 8, electron scattering occurs at the interface between the nonmagnetic conductive layer 2 and the free magnetic layer 1 and between the nonmagnetic conductive layer 2 and the pinned magnetic layer 3. On the other hand, in the dual spin-valve thin film magnetic head shown in FIG. 1, electron scattering occurs at two interfaces between the non-magnetic conductive layer 2 and the free magnetic layer 1 and at the non-magnetic interface. Since there are a total of four interfaces at two interfaces between the conductive layer 2 and the pinned magnetic layer 3, the dual spin-valve thin-film magnetic head has a higher rate of resistance change than the single spin-valve thin-film magnetic head.

[0009]

As the free magnetic layer 1 and the pinned magnetic layer 3, for example, an FeNi (iron-nickel) alloy film is generally used, and as the nonmagnetic conductive layer 2, a Cu (copper) film is generally used. In the conventional single-spin-valve thin-film magnetic head shown in FIG. 8, a FeMn (iron-manganese) alloy film is generally used as an antiferromagnetic material constituting the antiferromagnetic layer 4. However, the FeMn
The membrane is susceptible to corrosion and has the drawback of rapidly rusting when exposed to air containing moisture. Further, the blocking temperature in the exchange coupling between the FeMn alloy film of the antiferromagnetic material and the FeNi alloy film as the pinned magnetic layer is as low as about 150 ° C. Therefore, when the temperature of the head becomes high, the exchange anisotropic magnetic field becomes weak, and there is a disadvantage that noise in the detection output increases.

Also, an IrMn (iridium-manganese) alloy film may be used as an antiferromagnetic material in place of the FeMn alloy.
RhMn (rhodium-manganese) alloy film and the like. However, the FeMn (iron-manganese) alloy film, IrMn
(Iridium-manganese) alloy film, RhMn (rhodium-manganese) alloy film, etc.
When formed over a ferromagnetic material such as an eNi alloy, exchange coupling can be exhibited at the interface with the pinned magnetic layer 3. However, these antiferromagnetic materials are easily affected by the underlayer, and Since the vicinity of the upper surface of the magnetic material is hard to exhibit antiferromagnetic properties, exchange coupling cannot be exhibited when the pinned magnetic layer 3 is formed on the antiferromagnetic material. Has properties.

As described above, the antiferromagnetic materials listed above can exhibit effective exchange coupling only when they are stacked on the pinned magnetic layer 3 either above or below. Therefore, FIG.
In the structure in which the antiferromagnetic layers 4 and 4 are formed on both the upper and lower portions of the pinned magnetic layers 3 and 3 as in the dual spin valve type shown in FIG. 1, the antiferromagnetic material cannot be used. Further, as a material capable of obtaining an exchange anisotropic magnetic field regardless of whether it is formed above or below the pinned magnetic layer 3, N
There is an iMn (nickel-manganese) alloy. Since this antiferromagnetic material can be formed on both the upper and lower portions of the pinned magnetic layer 3, it can be used for the dual spin-valve thin film magnetic head shown in FIG.

However, this NiMn alloy film and FeNi
In order to exhibit effective exchange coupling with the base alloy film (pin magnetic layer 3), heat treatment (annealing) at a relatively high temperature is required. That is, in order to generate an exchange anisotropic magnetic field, it is necessary to apply a magnetic field and perform a heat treatment after joining and forming the antiferromagnetic layer 4 and the pinned magnetic layer 3. When the layer 4 is a NiMn alloy film and the pinned magnetic layer 3 is an FeNi-based alloy, the heat treatment temperature for exhibiting effective exchange anisotropic coupling requires a considerably high temperature of about 250 ° C. or more. However, when heat treatment at a high temperature of 250 ° C. or more is performed, the interface between the free magnetic layer 1 and the pinned magnetic layer 3 formed of the FeNi alloy film and the nonmagnetic conductive layer 2 formed of Cu causes Diffusion occurs, affecting the magnetoresistive effect due to electron diffusion at the interface between the free magnetic layer 1 and the nonmagnetic conductive layer 2 and at the interface between the pinned magnetic layer 3 and the nonmagnetic conductive layer 2, and the effect of external magnetic fields is reduced. There is a problem that the rate of change in resistance is reduced.

The present invention has been made to solve the above-mentioned conventional problems, and comprises an antiferromagnetic layer made of PtMn (platinum-manganese).
An object of the present invention is to provide a dual spin-valve thin-film magnetic head capable of obtaining an effective exchange anisotropic magnetic field, regardless of whether the antiferromagnetic layer is formed above or below a pinned magnetic layer by being formed of an alloy or the like. The purpose is.

Further, the present invention prevents the diffusion at the interface between the free magnetic layer and the pinned magnetic layer and the non-magnetic conductive layer by lowering the heat treatment temperature for exhibiting the exchange coupling by the antiferromagnetic film. It is an object of the present invention to provide a dual spin-valve thin film magnetic head capable of achieving a high resistance change rate.

[0015]

According to the present invention, there is provided a dual spin-valve thin-film magnetic head comprising: a nonmagnetic conductive layer laminated on and under a free magnetic layer; A pinned magnetic layer located below the conductive layer,
An antiferromagnetic layer positioned above one of the pinned magnetic layers and below the other pinned magnetic layer to fix the magnetization direction of each pinned magnetic layer in a fixed direction by an exchange anisotropic magnetic field; A bias layer for aligning the magnetization direction of the layer with a direction crossing the magnetization direction of the pinned magnetic layer, wherein the antiferromagnetic layer is formed of a PtMn (platinum-manganese) alloy. is there.

In the above, the free magnetic layer and the pinned magnetic layer are formed of, for example, an FeNi (iron-nickel) alloy.

The film composition of the PtMn alloy is PtMn.
Is preferably in the range of 44 to 51 atomic% and Mn is in the range of 49 to 56 atomic%.

Further, the antiferromagnetic layer is replaced with a PtMn alloy, and Pt—Mn—X (X = Ni, Pd, Rh, Ru,
Ir, Cr, Fe, Co) alloys or PdMn alloys are also possible.

Further, the free magnetic layer and the pinned magnetic layer may be formed of Co (cobalt), Fe-Co (iron-cobalt) alloy, or Fe-Co-Ni (iron-cobalt-nickel) alloy. is there.

In the present invention, a PtMn alloy film or a PdMn alloy film having properties equivalent to the PtMn alloy film is used as the antiferromagnetic material constituting the antiferromagnetic layer. These antiferromagnetic materials can exert an effective exchange anisotropic magnetic field at the interface with the pinned magnetic layer, regardless of whether they are overlaid on or below the ferromagnetic material constituting the pinned magnetic layer. Therefore, a dual spin-valve thin-film magnetic head in which a pinned magnetic layer is provided at vertically symmetric positions of a free magnetic layer and an antiferromagnetic layer is provided on one pinned magnetic layer and under the other pinned magnetic layer, When using an antiferromagnetic material, a sufficient magnetoresistance effect can be obtained.

When a PtMn alloy film or a PdMn alloy film is used as the antiferromagnetic layer, a sufficient exchange anisotropic magnetic field can be obtained even at a heat treatment temperature of 230 ° C. or less after film formation. Therefore, in the heat treatment, diffusion at the interface between the nonmagnetic conductive layer, the pinned magnetic layer, and the free magnetic layer can be prevented, and a high resistance change rate with respect to an external magnetic field can be obtained.

Further, the PtMn alloy film has better corrosion resistance than the FeMn alloy film and the NiMn alloy film, and the corrosion does not progress at all even in various solvents and cleaning agents in the manufacturing process of the dual spin valve type thin film magnetic head. It is chemically stable even in the operation of a dual spin-valve thin film magnetic head in a harsh environment.

Further, the exchange anisotropic magnetic field obtained by the contact between the PtMn alloy film and the pinned magnetic layer is extremely stable thermally and has a high blocking temperature of about 380 ° C. Even when the temperature is high, a stable exchange anisotropic magnetic field can be generated, and the reading accuracy is stabilized.

[0024]

FIG. 1 is a sectional view showing the structure of a dual spin-valve thin film magnetic head according to the present invention. The thin-film magnetic head is provided at the trailing end of a flying slider provided in a hard disk drive. The moving direction of a magnetic recording medium such as a hard disk is in the Z direction. Is the Y direction.

The bottom of FIG. 1 is Ta.
The underlayer 6 is made of a nonmagnetic material such as (tantalum). On this underlayer 6, PtMn (platinum-manganese)
An antiferromagnetic layer 4 made of an alloy and a pinned magnetic layer 3 made of an FeNi (iron-nickel) alloy are laminated. A nonmagnetic conductive layer 2 of Cu (copper) or the like is formed on the pinned magnetic layer 3, and a free magnetic layer 1 of a FeNi-based alloy is formed on the nonmagnetic conductive layer 2. Further, a nonmagnetic conductive layer 2, a pinned magnetic layer 3, and an antiferromagnetic layer 4 are successively laminated on the free magnetic layer 1, and a protective layer 7 of Ta or the like is formed.

By subjecting the antiferromagnetic layer 4 and the pinned magnetic layer 3 to heat treatment in a magnetic field of a predetermined magnitude in a laminated state, an exchange anisotropic magnetic field is obtained at the interface between the two layers. ,
The direction of magnetization of the pinned magnetic layer is converted into a single magnetic domain in the Y direction and fixed. When the antiferromagnetic layer 4 is formed of a PtMn alloy and the pinned magnetic layer 3 is formed of a FeNi-based alloy, when the antiferromagnetic layer 4 is formed below the pinned magnetic layer 3, Exchange coupling is possible both when formed on The pinned magnetic layer 3 is made of Co (cobalt), Fe-Co (iron-cobalt) alloy, Fe-Co
-Even if it is formed of Ni (iron-cobalt-nickel) alloy,
An exchange anisotropic magnetic field can be obtained at the interface with the antiferromagnetic layer 4.

After a multilayer film from the underlayer 6 to the protective layer 7 is formed by sputtering and etched into a predetermined sectional shape, a hard bias layer 5 for applying a bias magnetic field to the free magnetic layer 1 is formed. The hard bias layer 5 is magnetized in the X direction, and the magnetization of the free magnetic layer 1 is aligned in the X direction. Further, conductive layers 8 and 8 made of W (tungsten), Cu (copper) or the like are formed on hard bias layers 5 and 5, respectively.

In the dual spin-valve thin-film magnetic head thus formed, a steady current is applied from the conductive layer 8 to the free magnetic layer 1, the non-magnetic conductive layer 2, and the pinned magnetic layer 3. When a magnetic field is applied in the direction, the direction of magnetization of the free magnetic layer 1 changes from the X direction to the Y direction. At this time, electrons which are going to move from one of the free magnetic layer 1 and the pinned magnetic layer 3 to the other are transferred to the interface between the nonmagnetic conductive layer 2 and the free magnetic layer 1 or between the nonmagnetic conductive layer 2 and the pinned magnetic layer. Causing scattering at the interface with layer 3,
Electric resistance changes. Therefore, the steady current changes, and a detection output can be obtained. The PtMn alloy used for the antiferromagnetic layer 4 in the present invention is a FeMn (iron-manganese) alloy or Ni
It has better corrosion resistance than Mn (nickel-manganese) alloy. Therefore, deterioration of the head characteristics due to corrosion can be prevented.

[0029]

DESCRIPTION OF THE PREFERRED EMBODIMENTS A description will now be given of embodiments of a multilayer film using a PtMn alloy film as an antiferromagnetic layer and a dual spin-valve thin film magnetic head using this multilayer film. Dual spin valve element (FIG. 1) and single spin valve element (FIG. 8) having an element width (track width) of 2.2 μm in the X direction and an element length (MR height) of 1.5 μm in the Y direction.
Was formed.

The dual spin-valve element has a film configuration in which alumina (Al ₂ O ₃ ) is formed as a nonmagnetic material on a silicon (Si) substrate, and the film is protected from the underlayer 6 as in FIG. The film was formed in the order of the layer 7, and its constituent film material was Ta (3 nm) / PtMn (20 nm) / N
iFe (4 nm) / Cu (2.5 nm) / NiFe (7
nm) / Cu (2.5 nm) / NiFe (4 nm) / P
tMn (20 nm) / Ta (5 nm). The thickness in parentheses is the film thickness. The single spin-valve element has a film configuration in which an alumina film is formed on a silicon substrate, and a layer upside down in FIG. 8 is formed thereon. The order of the pinned magnetic layer / non-magnetic conductive layer / free magnetic layer / protective layer is as follows. Concrete materials include Ta (3 nm) / PtMn (30 nm) / NiF
e (4 nm) / Cu (2.5 nm) / NiFe (8n
m) / Ta (5 nm).

Further, in both the dual spin valve film and the single spin valve film, P
The film composition of the tMn film is as follows: Pt is 48 atomic% (at%);
n was 52 atomic% (at%) (Pt ₄₈ M
_n52 ). The above film formation was performed by DC magnetron sputtering using an alloy target. In the dual spin-valve element, by performing a heat treatment at 230 ° C., the exchange coupling magnetic field (He) applied from the PtMn alloy film as the antiferromagnetic layer 4 to the FeNi alloy film of the pinned magnetic layer 3 is increased.
x) is 470 (Oe), the coercive force (Hc) of the pinned magnetic layer 3
Was 240 (Oe).

As shown in FIGS. 1 and 8, on both sides of the dual spin valve element, a 30 nm-thick C
An oPt alloy film was formed as a hard bias layer 5, and the CoPt alloy film was formed as a hard bias layer 5 on both sides of a single spin valve element with a thickness of 20 nm. The hard bias layer 5 has a remanent magnetism (M
r) is 0.9 T (tesla) and the coercive force is 1300 (O
e). When the multilayer film is formed on a 5 mm × 25 mm silicon substrate, the dual spin valve element has a resistance change rate of 6.2% and a sheet resistance of 1%.
0.8Ω / m 2, in the single spin valve element,
Resistance change rate is 3.9%, sheet resistance is 16.3Ω / m ²
Met.

As described above, the resistance change rate of the dual spin valve element is higher than that of the single spin valve element. This is because both the pinned magnetic layers 3 and 3 formed on the upper and lower sides of the free magnetic layer 1
This means that the magnetization is fixed in the direction, which means that the antiferromagnetic layer 4 of the PtMn alloy formed below the pinned magnetic layer 3 and the antiferromagnetic layer of the PtMn alloy formed above the pinned magnetic layer 3. This means that both the ferromagnetic layers 4 exhibit exchange coupling at the interfaces with the pinned magnetic layers 3 and 3. Next, a steady current (Is) of 5 mA is applied to a dual spin valve element and a single spin valve element having an element width (track width Tw) of 2.2 μm and an element length (MR height h) of 1.5 μm, An external magnetic field was applied from the Y direction, and the external magnetic field was changed, and a change in voltage (proportional to a change in resistance) was measured from the steady current Is.

FIG. 2 shows the magnitude of the external magnetic field on the horizontal axis.
The vertical axis shows the voltage change (ΔV) based on the steady-state current given to the dual spin valve element,
(A) is a major loop in which changes in the external magnetic field in the range of ± 2 K (Oe) are plotted on the horizontal axis, and (B) is a ± 2K (Oe) of the external magnetic field.
This is a minor loop in which changes in the range of 200 (Oe) are plotted on the horizontal axis.

From the major loop of FIG. 2A, the voltage change of the dual spin valve element was 4.4 mV, and the resistance change rate was 3.5%. The major loop draws a smooth curve and does not change in two steps. This indicates that the two pinned magnetic layers 3 and 3 are formed into a single magnetic domain by an exchange anisotropic magnetic field having substantially the same magnitude and have substantially the same coercive force. Further, it can be seen that there is no hysteresis in the minor loop, and the coercive force of the free magnetic layer is almost zero even when the external magnetic field is returned to 0 (Oe). In other words, it indicates that the free magnetic layer 1 is formed into a single magnetic domain in the X direction by the hard bias layer 5, and Barkhausen noise can be reduced.

FIG. 3 shows a voltage change rate (resistance change rate) (ΔR) when the steady-state current (Is) is changed in a range of ± 10 mA.
(V / V) is a result of measuring the fluctuation of both the single spin valve element and the dual spin valve element.
The steady-state current is, in a single spin valve element,
The direction in which the magnetic field due to the steady current weakens the exchange anisotropic magnetic field of the pinned magnetic layer is positive. In FIG. 3, the resistance change rate of the dual spin-valve element is larger than the resistance change rate of the single spin-valve element regardless of the change in the steady-state current. Further, the rate of change ΔV / V when the steady-state current is 10 mA is larger than ΔV / V at 1 mA.
In the dual spin valve element, the reduction is 8.8%.
In the case of the single spin valve element, the reduction is 16.2%. FIG. 3 shows that the resistance change rate in the dual spin valve element of the present invention is stable with respect to the change in the steady-state current.

FIG. 4 is a graph showing a relationship between a change in the steady-state current and asymmetry. FIG.
Is obtained from a minor loop and examines the symmetry of a voltage change (resistance change) at ± 40 (Oe) corresponding to the magnitude of a leakage magnetic field from a magnetic recording medium such as a hard disk. The horizontal axis shows the change in steady-state current,
The vertical axis shows the asymmetry of both the dual spin valve element and the single spin valve element by (ΔV (−40 O
e) −ΔV (+40 Oe)) / (ΔV (−40 Oe) +
ΔV (+40 Oe)).

In FIG. 4, the asymmetry of the dual spin valve element is about -10%, and it can be seen that there is almost no dependence on the steady current. On the other hand, in the case of the single spin valve element, it changes from about −32% to + 1%, and it can be seen that the single spin valve element strongly depends on the steady current. This is because the dual spin-valve element has an upper and lower symmetric film configuration, and the steady current magnetic field generated by the steady current flowing above and below the free magnetic layer cancels out in the free magnetic layer, and the steady current magnetic field is generated in the free magnetic layer. It does not work.

As described above, the dual spin valve element using the PtMn alloy as the antiferromagnetic layer 4 can obtain a large resistance change rate with respect to an external magnetic field, and has no hysteresis in the resistance change rate. , And is less susceptible to changes in steady-state current. Therefore, a dual spin-valve thin-film magnetic head using a PtMn alloy as an antiferromagnetic layer can obtain excellent characteristics.

Next, experimental results on exchange coupling between the PtMn alloy forming the antiferromagnetic layer 4 and the ferromagnetic material forming the pinned magnetic layer 3 will be described. First, alumina is deposited on the surface of a silicon (Si) substrate by DC magnetron sputtering and RF conventional sputtering,
Further from the bottom, Ta (3 nm) / FeNi (5 nm)
/ PtMn (20 nm) / Ta (5 nm) was formed and further covered with alumina. The thickness in parentheses is the film thickness.

The PtMn film is formed by forming Pt on a Mn target.
This was performed using a composite target and an alloy target on which chips were arranged, so that the composition of PtMn at the time of film formation could be changed. In the multilayer film having the above structure, the composition of the PtMn film is changed.
m PtMn film was formed, and the film composition of PtMn was analyzed by XMA (X-ray microanalyzer). In the multilayer film, heat treatment for obtaining exchange coupling between the PtMn alloy of the antiferromagnetic material and the FeNi alloy of the ferromagnetic material is performed at a vacuum degree of 5 × 10 ⁻⁶ Torr or less, and at 200 ° C.
The test was performed at a temperature of 270 ° C. in a magnetic field of 0 (Oe).
Measurement of exchange anisotropic magnetic field (Hex) is performed by VS with vacuum heating mechanism.
M.

FIG. 5 shows the film composition of the PtMn film, where Pt is 0%.
Ａｔ60 at%, the state immediately after film formation (as depo.) When changed so as to fall within the range of 2 to 60 at%.
Exchange anisotropic magnetic field (Hex) after heat treatment at 70 ° C.
Shows the measured values. As shown in FIG. 5, Pt is 0 to 2 both when the heat treatment is performed and when the heat treatment is not performed.
Hex occurs in the range of 5 at%, but this exchange coupling is
It occurs only when the PtMn film is stacked on the NiFe film, and no exchange coupling occurs when the PtMn film is formed below the FeNi film.

After the heat treatment, Pt is reduced from 42 at% to 55 a.
In the range of t%, exchange coupling occurs. In this case, exchange coupling occurs both when the PtMn film is formed on the FeNi film and when it is formed below the FeNi film. And Pt is 44
When the exchange anisotropic magnetic field (Hex) is 1
Hex exceeds 240 (Oe) when Pt exceeds 46 (Oe) and Pt is in the range of 46 to 49 at%. Therefore, in the dual spin valve type thin film magnetic head shown in FIG.
An exchange anisotropic magnetic field is generated by heat treatment, and the composition of the PtMn alloy constituting the antiferromagnetic layer is such that the Pt is 44 to 51 at.
% Is preferably in the range of 49 to 56 at%, more preferably 46 to 49 at%, and more preferably Mn is in the range of 46 to 49 at%.
Is 51 to 54 at%.

FIG. 6 shows the relationship between the exchange coupling between the PtMn film, which is an antiferromagnetic material, and the FeNi film, which becomes a pinned magnetic layer, and the heat treatment temperature. The film configuration is such that an alumina layer is formed on a silicon substrate, and a Ta (3n) layer is formed thereon.
m) / PtMn (30 nm) / FeNi / Ta (5n
m) / alumina. The film was formed by DC magnetron sputtering using an alloy target. Also,
The composition of the PtMn film is such that Pt is 48 at% and Mn is 52 at%.
%. The thickness of the FeNi film is 2 nm, 3 nm, 4 nm,
nm, 10 nm, and 20 nm.

5 × 10 5
^An exchange anisotropic magnetic field (Hex) was generated in a magnetic field of 2000 (Oe) at a degree of vacuum of ^-6 Torr or less. The heat treatment in the vacuum is performed at 0 ° C., 190 ° C., 210 ° C., and 23 ° C.
0 ° C. and 250 ° C. The exchange anisotropic magnetic field of the multilayer film heat-treated at each temperature was measured by VSM. In FIG. 6, the horizontal axis represents the change in the thickness of the FeNi film, and the vertical axis represents the exchange anisotropic magnetic field (Hex).

According to FIG. 6, FeNi to be a pin magnetic layer is formed.
If the film thickness is 5 nm or less, heat treatment at 210 ° C.
When an exchange anisotropic magnetic field (Hex) of 00 (Oe) or more can be obtained and the thickness of the FeNi film is 10 nm or less,
At a relatively low heat treatment temperature of about 230 ° C., the exchange anisotropic magnetic field can be made 200 (Oe) or more. That is, P
When tMn is used as the antiferromagnetic layer 4, an exchange anisotropic magnetic field can be generated by heat treatment at a relatively low temperature, and a Cu film and a pinned magnetic layer as non-magnetic conductive layers which become problematic due to high temperature heat treatment. Or Ni as a free magnetic layer
Diffusion with the Fe film can be prevented, and good characteristics as a thin-film magnetic head can always be obtained.

FIG. 7 shows the effect of the operating environment temperature when the FeNi alloy is used and when Co is used as the pinching material constituting the pinned magnetic layer 3. The film is composed of alumina / Ta on a silicon substrate.
(3 nm) / PtMn (30 nm) / FeNi (3n
m) / Ta (5 nm) / alumina, and alumina / Ta (3 nm) / PtMn on a silicon substrate.
(30 nm) / Co (4 nm) / Ta (5 nm) / alumina were formed into two types.

The film was formed by DC magnetron sputtering using an alloy target, and the composition of the PtMn film was PtMn.
Was 48 at% and Mn was 52 at%. With respect to the above two types of multilayer films, at a degree of vacuum of 5 × 10 ⁻⁶ Torr or less,
Heat treatment was performed at 230 ° C. in a magnetic field of 2000 (Oe) to generate an exchange anisotropic magnetic field (Hex). After the heat treatment, it was cooled to room temperature. After cooling, the environmental temperature of each of the multilayer films was increased, and the exchange anisotropic magnetic field at that time was measured.

FIG. 7 shows the ambient temperature on the horizontal axis and the exchange anisotropic magnetic field (Hex) on the vertical axis. When a FeNi film is used as the ferromagnetic material for the pinned magnetic layer, Hex does not decrease so much even when the temperature is increased from room temperature to about 200 ° C.
It begins to fall from 0 ° C. and disappears at about 380 ° C. (blocking temperature). When Co is used for the pinned magnetic layer, Hex shows little change from room temperature to about 120 ° C.
The temperature gradually starts to decrease from 0 ° C. or higher, and reaches the blocking temperature at about 380 ° C. as in the case of the FeNi film. Thus, the temperature at which Hex disappears (blocking temperature) is F
Both the eNi film and the Co film show a very high value of 380 ° C., and particularly in the range of room temperature to about 120 ° C., which may increase as a practical temperature around the magnetoresistive effect film.
Since Hex by the FeNi film and the Co film shows a substantially flat value, it is possible to always obtain a stable exchange anisotropic magnetic field.

[0050]

According to the present invention described in detail above, the antiferromagnetic layer is made of a PtMn alloy or PdM
n alloy or Pt-Mn-X (X = Ni, Pd, R
h, Ru, Ir, Cr, Fe, Co) alloy, it is possible to obtain an exchange anisotropic magnetic field regardless of whether the antiferromagnetic layer is formed above or below the pinned magnetic layer. An effective exchange anisotropic magnetic field can be obtained even with a heat treatment at a relatively low temperature. Further, the PtMn alloy has high thermal stability and excellent corrosion resistance. Therefore, it is possible to manufacture a dual spin-valve thin film magnetic head having characteristics as a good thin film magnetic head.

The antiferromagnetic layer is made of a PtMn alloy or a PtMn alloy.
dMn alloy or Pt-Mn-X (X = Ni, P
d, Rh, Ru, Ir, Cr, Fe, Co) alloy, the dual spin-valve thin-film magnetic head has a higher resistance change rate than the single spin-valve thin-film magnetic head, and the asymmetry is dramatically improved. improves.

The antiferromagnetic layer is made of PtMn alloy or PtMn.
dMn alloy or Pt-Mn-X (X = Ni, P
(d, Rh, Ru, Ir, Cr, Fe, Co) alloy, the material of the antiferromagnetic layer above and below the pinned magnetic layer can be used in common, so that a sputtering target at the time of film formation can be used. Can be reduced, and manufacturing becomes easier.

[Brief description of the drawings]

FIG. 1 is an enlarged sectional view showing the structure of a dual spin-valve thin film magnetic head.

FIGS. 2A and 2B are diagrams showing a relationship between an external magnetic field and a resistance change rate in a dual spin valve film, wherein FIG. 2A is a major loop, FIG.

FIG. 3 is a diagram showing a relationship between a steady current and a resistance change rate in a single spin valve film and a dual spin valve film;

FIG. 4 is a diagram showing a relationship between steady current and asymmetry in a single spin valve element and a dual spin valve element;

FIG. 5 is a diagram showing a relationship between a film composition of a PtMn film and an exchange anisotropic magnetic field;

FIG. 6 is a diagram showing a relationship between a heat treatment temperature, a thickness of a pinned magnetic layer (FeNi film), and an exchange anisotropic magnetic field;

FIG. 7 is a diagram showing a relationship between an ambient temperature and an exchange anisotropic magnetic field when an FeNi film and a Co film are used for a pinned magnetic layer;

FIG. 8 is an enlarged sectional view showing the structure of a single spin-valve thin-film magnetic head;

[Explanation of symbols]

 DESCRIPTION OF SYMBOLS 1 Free magnetic layer 2 Nonmagnetic conductive layer 3 Pin magnetic layer 4 Antiferromagnetic layer 5 Hard bias layer 6 Underlayer 7 Protective layer 8 Conductive layer

Claims (4)

[Claims] 1. A non-magnetic conductive layer laminated above and below a free magnetic layer, a pinned magnetic layer positioned above one non-magnetic conductive layer and below another non-magnetic conductive layer, and one of the pins An antiferromagnetic layer positioned above the magnetic layer and below the other pinned magnetic layer to fix the magnetization direction of each pinned magnetic layer in a fixed direction by an exchange anisotropic magnetic field, and a magnetization direction of the free magnetic layer And a bias layer for aligning the antiferromagnetic layer in a direction crossing the magnetization direction of the pinned magnetic layer.
A dual spin-valve thin film magnetic head formed of an n (platinum-manganese) alloy. 2. The free magnetic layer and the pinned magnetic layer according to claim 1, wherein the free magnetic layer and the pinned magnetic layer are formed of a FeNi (iron-nickel) alloy, a Co (cobalt), a Fe—Co alloy, or a Fe—Co—Ni alloy. Dual spin valve thin film magnetic head. 3. The film composition of the PtMn alloy has a Pt of 4
3. The dual spin-valve thin film magnetic head according to claim 1, wherein the Mn is in a range of 4 to 51 at% and Mn is in a range of 49 to 56 at%. 4. An antiferromagnetic layer, wherein a PtMn alloy is used instead of a PtMn alloy.
Pt—Mn—X (X = Ni, Pd, Rh, Ru, Ir,
2. The dual spin-valve thin-film magnetic head according to claim 1, wherein the dual spin-valve thin-film magnetic head is formed of a Cr, Fe, Co) alloy or a PdMn alloy.