Magnetoresistive effect element in CPP-type structure and magnetic disk device

An MR element in a CPP structure includes a spacer layer made of Cu, a magnetic pinned layer containing CoFe and a free layer containing CoFe that are laminated to sandwich the spacer layer. The free layer is located below the magnetic pinned layer. The free layer is oriented in a (001) crystal plane, the spacer layer is formed and oriented in a (001) crystal plane on the (001) crystal plane of the free layer. Therefore, in a low resistance area where an area resistivity (AR) of the MR element is, for example, lower than 0.3 Ω·μm2, an MR element that has a large variation of a resistance is obtained.

CROSS REFERENCE TO RELATED APPLICATION

This application is related to U.S. application Ser. No. 12/500,907, entitled “MAGNETORESISTIVE EFFECT ELEMENT IN CPP-TYPE STRUCTURE AND MAGNETIC DISK DEVICE,” filed on Jul. 10, 2009.

BACKGROUND OF INVENTION

1. Field of Invention

The present invention relates to a magnetoresistive effect element (MR element) in a CPP-type structure that detects magnetic field intensity as a signal from a magnetic recording medium, and so on, a thin film magnetic head with the MR element, and a head gimbal assembly and a magnetic disk device that have the thin film magnetic head.

2. Description of Related Art

In recent years, with an increase in the high recording density of a magnetic disk drive (HDD), there have been growing demands for improvements in the performance of a thin film magnetic head. For a thin film magnetic head, a composite type thin film magnetic head has been widely used; it has a structure where a reproducing head having a read-only magnetoresistive effect element (hereinafter, magneto-resistive (MR) element), and a writing head having a write-only induction type magnetic conversion element are laminated together.

Generally, a shield layer is formed in a reproducing head to restrict an area of a medium that interferes with a reproducing element. Currently, in a conventional mainstream head structure, a first shield layer, a second shield layer and an MR element are connected in series without an intershield insulating layer. This structure is referred to as an MR element in a current perpendicular to plane type (CPP-type) structure. In consideration of the efficiency of heat radiation and maintenance of an output, and so on, a CPP-type structure is an essential technology to realize a high recording density of 500 Gbits/in2or more.

A general CPP-type element with a spin valve is briefly explained below. A typical spin valve CPP-type element is formed by a lamination structure for its main layers as follows: a lower electrode layer/an under layer/an antiferromagnetic layer/a ferromagnetic layer (1)/a spacer layer/a ferromagnetic layer (2)/a cap layer/an upper electrode layer. The top most layer is the upper electrode layer, and the bottom most layer is the lower electrode layer. In the specification, a lamination layer may be described as having the above format.

A magnetization direction of the ferromagnetic layer (1), which is one of the ferromagnetic layers, is pinned in the perpendicular direction to a magnetization direction of the ferromagnetic layer (2) when the externally applied magnetic field is zero. The ferromagnetic layer (2) is generally referred to as a magnetic free layer. The magnetization direction of the ferromagnetic layer (1) can be pinned by making an antiferromagnetic layer adjacent thereto and providing unidirectional anisotropic energy (also referred to as “exchange bias” or “coupling magnetic field”) to the ferromagnetic layer (1) by means of exchange-coupling between the antiferromagnetic layer and the ferromagnetic layer (1). For this reason, the ferromagnetic layer (1) is also referred to as a magnetic pinned layer.

As mentioned above, a CPP-type element that is configured with a connection between a shield layer and an MR element through a metal is advantageous because it increases heat radiation efficiency and operating electric current. In this element, a smaller cross sectional area of an element has a larger resistance value and a larger resistance variation. Namely, it is an appropriate structure for a, so called, narrower track that narrows a track width. A narrower track width increases a track per inch (TPI), and it is an essential technology for increasing the recording density of an HDD.

However, in view of the high frequency characteristic of the above element, an extreme increase in the resistance of such an element is unfavorable. In other words, with the recent increase in the recording density, it is necessary to improve the high frequency characteristic of a reproducing signal. In order to improve the high frequency characteristic of a reproducing signal, it is important to match the following factors: an impedance of an MR element part; an impedance of an amplifier; and an impedance of a transmission line connecting the MR element part; and the amplifier. Since these impedance values are restricted by an impedance of a transmission line, an MR element needs to have a lower resistance value to improve the high frequency characteristic. Therefore, research and development has been conducted for a CPP-GMR element that has a spacer layer made of a low resistance material instead of having a TMR element with a tunnel barrier that has a high resistance value.

With consideration of the situation described above, the present invention is provided. An object of the present invention is to provide an MR element having a large magnetoresistive variation in a lower resistance area that has a resistance value of 0.3 Ωμm2or smaller with respect to its area resistivity (AR), a thin film magnetic head that has the MR element mentioned above, and a head gimbal assembly and a magnetic disk device that have the thin film magnetic head mentioned above.

As related art that may be related to the present invention and that discloses a method to increase an MR ratio of a CPP-GMR element, the following four references are given by an example.

(1) Japanese laid-open patent publication No. 2008-34523 discloses that, in a current confined path (CCP)—current perpendicular to plane (CPP) type giant magnetoresistive effect element (GMR) having a magnetic pinned layer, an intermediate layer, and a magnetic free layer, the GMR element is configured with the intermediate layer that is made of single crystalline or polycrystalline magnesium oxide (MgO) with a layer thickness of 1 nm or lower. The intermediate layer is preferentially oriented with a (001) crystal plane and a BCC-CoFe (001) structure is formed over the intermediate layer.

However, the magnesium oxide (MgO) of the intermediate layer is not an intended material of the present invention and is not an appropriate material for decreasing resistance.

(2) Japanese laid-open patent publication No. 2008-4956 proposes that, in an MR element with a magnetic tunnel junction structure that includes a first ferromagnetic material with a BCC structure formed on a first plane of a tunnel barrier layer and a second ferromagnetic material with a BCC structure formed on a second plane of the tunnel barrier layer, the MR element is configured with the tunnel barrier layer made of either single crystalline MgO (001) or polycrystalline MgO in which a (001) crystal plane is priority oriented, the first ferromagnetic material made of either Fe (001) or an Fe alloy system (001), and the second ferromagnetic material made of either Fe (001) or an Fe alloy system (001).

However, the magnesium oxide (MgO) of the tunnel barrier layer is not an intended material of the present invention and is not an appropriate material for decreasing resistance.

(3) Japanese laid-open patent publication No. 2008-235528 proposes that an MR element is configured with the following layers in a bottom up direction; an under layer that is made of NiFeN and is formed on a main surface of a substrate, a pinning layer that is made of an antiferromagnetic material containing Ir and Mn and is formed on the under layer, a reference layer that is made of a ferromagnetic material in which a magnetization direction is pinned by exchange-coupling with the pinning layer directly or indirectly through another ferromagnetic layer and is formed on the pinning layer, a nonmagnetic layer that is made of a nonmagnetic material and is formed on the reference layer, and a free layer that is made of a ferromagnetic material in which a magnetization direction varies depending on the externally applied magnetic field and is formed on the nonmagnetic layer.

However, this reference does not disclose or suggest a combination of an under layer made of NiFeN and a CoFe layer made on the under layer. The nonmagnetic layer is made of MgO. The magnesium oxide (MgO) of the nonmagnetic layer is not an intended material of the present invention and is not an appropriate material for decreasing resistance.

(4) Japanese laid-open patent publication No. H06-195645 discloses a magnetoresistive effect type head configured with a magnetoresistive effect film that is made of a NiFe alloy, a magnetic material with magnetoresistive effect, and a magnetic sensitive part made of a NiFe alloy in which a plane direction is oriented as a (100) orientation with respect to a layer surface of the magnetoresistive effect film.

However, this reference is related to a magnetic layer made of a NiFe alloy. This reference does not disclose or suggest a combination of CoFe in a (001) orientation and Cu in a (001) orientation.

SUMMARY OF INVENTION

In order to solve the above drawbacks, a magnetoresistive effect element (MR element) of the present invention that is a giant magnetoresistive effect element in a current perpendicular to plane (CPP) structure includes a spacer layer made of Cu, a magnetic pinned layer containing CoFe and a free layer containing CoFe that are laminated to sandwich the spacer layer, in which a sense current flows along a lamination direction of the layers. The free layer is formed before the magnetic pinned layer is formed, and is located below the magnetic pinned layer. A magnetization direction of the free layer varies depending on an externally applied magnetic field, and a magnetization direction of the magnetic pinned layer is pinned. The free layer is oriented in a (001) crystal plane, and the spacer layer is formed and oriented in a (001) crystal plane on the (001) crystal plane of the free layer.

As a preferred embodiment of the present invention, the magnetic pinned layer is formed and oriented in a (001) crystal plane on the (001) crystal plane of the spacer layer.

As a preferred embodiment of the present invention, an under layer containing a NiFeN layer that is oriented in a (001) crystal plane is formed below the free layer, the free layer is a first ferromagnetic layer and is formed on the under layer, and the spacer layer is formed on the first ferromagnetic layer.

As a preferred embodiment of the present invention, the magnetic pinned layer is formed and oriented in a (001) crystal plane on the (001) crystal plane of the spacer layer.

A thin film magnetic head of the present invention includes an air bearing surface (ABS) that is opposite to a recording medium, the magnetoresistive effect element (MR element) described above that is provided in the vicinity of the ABS to detect a signal magnetic field from the recording medium, and a pair of electrodes that apply an electric current in a lamination direction of the MR element.

A head gimbal assembly of the present invention includes a slider having the thin film magnetic head described above and being provided opposite to a recording medium, and a suspension elastically supporting the slider.

A magnetic disk device of the present invention includes a slider having the thin film magnetic head described above and being provided opposite to a recording medium; and a positioning device supporting the slider and locating a position of the slider with respect to the recording medium.

DETAILED DESCRIPTION

The best mode for implementing the present invention will be described in detail hereafter.

FIG. 1is a schematic view of an air bearing surface (ABS) of a reproducing head according to one embodiment of the present invention. Specifically, it shows the ABS of a giant magnetoresistive effect element in a CPP-type structure (CPP-GMR element), which is a main part of the present invention. The ABS generally corresponds to a surface at which a reproducing head is in opposition to a recording medium (hereinafter often called the opposing medium surface or ABS), however, it is understood that the ABS of the present invention includes not only the surface but also a section where a lamination structure of the element can be clearly observed. For instance, a passivation layer of diamond-like carbon (DLC) or the like (the passivation layer adapted to cover the element), in a strict sense, positioned at the ABS may be omitted if necessary.

FIG. 2is a sectional view of a thin film magnetic head that is perpendicular to an ABS and a substrate according to one embodiment of the present invention, and it is also for explaining the structure of the thin film magnetic head.

FIG. 3is a perspective view of a slider that is a part of a head gimbal assembly according to one embodiment of the present invention.FIG. 4is a perspective view of a head arm assembly that contains a head gimbal assembly according to one embodiment of the present invention.FIG. 5is an illustration for explaining primary parts of a magnetic disk device according to one embodiment of the present invention.FIG. 6is a top plan view of a magnetic disk device according to one embodiment of the present invention.

In the explanation below, a size of the X axis is defined as “width,” a size of the Y axis is defined as “length,” and a size of the Z axis is defined as “thickness” in each drawing. In the Y axis direction, an area that is close to an ABS (hereinafter, referred as an opposing medium surface) is defined as “front,” and an area that is opposite side of the front is defined as “rear (or posterior).” The laminated up direction of an element is defined as “above” or “upper side,” and the opposite direction is defined as “below” or “lower side.”

A detailed description of a structure of a reproducing head of a giant magnetoresistive effect element in a CPP-type structure (CPP-GMR element) according to the present invention is given below with reference toFIG. 1.

As described above,FIG. 1is a sectional view corresponding to a section of a reproducing head parallel to an ABS.

As shown inFIG. 1, the CPP-GMR element according to the present embodiment includes a first shield layer3and a second shield layer5that are spaced apart and opposed to each other in upper and bottom directions on the sheet, a giant magnetoresistive effect element8(hereinafter referred simply to as “GMR element8”) interposed between the first shield layer3and the second shield layer5, an insulating layer4adapted to cover two sides of the GMR element8and a part of the upper surface of the first shield layer3along those sides, and two bias magnetic field application layers6adjacent to the two sides of the GMR element8through the insulating layer4.

In this embodiment, the first shield layer3and the second shield layer5take a so-called magnetic shield role and a role of a pair of electrodes. In other words, they have not only a function of shielding magnetism but also a function of a pair of electrodes provided to enable a sense current to flow in a direction intersecting the plane of each of the layers forming the GMR element8, for instance, in a direction perpendicular to the plane of each of the layers forming the GMR element8(lamination direction). For this reason, the first shield layer3and the second shield layer5may be referred to as a “lower electrode layer3” and an “upper electrode layer5,” respectively.

In addition to the first shield layer3and the second shield layer5, another pair of electrodes may be provided above and below the GMR element8.

A reproducing head according to the present invention includes the GMR element8in a CPP-type structure as a main part of the present invention.

As an easily understandable explanation for the concept of a structure of the GMR element8in CPP-type structure according to the present invention shown inFIG. 1, the structure has a spacer layer40, and a free layer50and a magnetic pinned layer30, which are laminated to sandwich the spacer layer40.

In a preferred embodiment shown inFIG. 1, the free layer50is formed before the magnetic pinned layer30is formed and is a layer provided in a lower part of the structure. A magnetization direction of the free layer50varies depending on an externally applied magnetic field. A magnetization direction of the magnetic pinned layer30is pinned. The angles of the magnetization directions of the magnetic pinned layer30and free layer50relatively changes due to an externally applied magnetic field. As a sense current flows through a lamination direction of the GMR element8, it causes the element to perform its own function. In other words, it is the GMR element8in the current perpendicular to plane (CPP) type structure.

In the preferred embodiment shown inFIG. 1, as discussed above, the magnetic pinned layer30is formed in an upper part of the structure relative to the free layer50. Therefore, an antiferromagnetic layer22is formed in an upper part relative to the magnetic pinned layer30. This structure in the embodiment is referred to as a top-type structure.

A cap layer26is formed on the antiferromagnetic layer22.

An under layer21is formed below the free layer50. The under layer21can be considered to have an additional function as a part of an electrode that connects to the first shield layer3. In this sense, the under layer21is also referred to as pseudo-electrode under layer21.

A detailed explanation of each structure is given below.

[Explanation of Free Layer50]

The free layer50is a layer of which a magnetization direction varies depending on an externally applied magnetic field, i.e., a signal magnetic field from a recording medium. The free layer50is made of a CoFe alloy system in which a CoFe alloy or CoFe is a main component, the free layer50being a ferromagnetic layer with a small coercivity (soft magnetic layer). The free layer50has a thickness of, for example, approximately 2 to 10 nm.

The free layer50that is made of CoFe according to the present invention is formed with a (001) crystal plane orientation toward a lamination direction (hereinafter, “crystal plane” may be referred to as “plane”).

A (001) crystal plane orientation of CoFe functioning as the free layer50is not conventional in the technology area of the present invention. The reasons why are given below.

A basic crystal structure of CoFe is a BCC structure. A close-packed plane of BCC-CoFe is a (110) crystal plane. Therefore, a BCC-CoFe layer formed with regular layer forming conditions has a (110) plane orientation. If, for example, a Cu layer as a spacer layer is formed on this layer, the Cu layer has a (111) plane orientation. In this situation, it could be said that a degree of mismatch is relatively small. In lamination layers of close packed planes, even though there is only a small mismatch in its lattice, a lattice defect is unavoidable. Since this lattice defect causes a spin scattering, an increase of an MR ratio is prevented.

In contrast, the free layer50according to the present invention has a (001) plane orientation as discussed above. When a Cu layer is formed on this free layer50with a (001) plane orientation, a spacer layer40made of Cu has a (001) plane orientation. Cu is usually an FCC structure; however, Cu formed by the method described above is a BCC structure.

In the present invention, since a (001) plane of the Cu layer as the spacer layer40is formed on a (001) plane of the BCC-CoFe alloy as the free layer50, a structure is configured in which spin scattering is small by assimilating atomic scale differences. The forming structure of the CoFe (001)-Cu (001) does not exist in the prior art.

As discussed above, a spacer layer40according to the present invention is configured with Cu having a (001) plane orientation, and a layer thickness of approximately 1 to 5 nm.

The most critical aspect is that the free layer50and the spacer layer40are formed in the (001) plane orientation.

[Explanation of Magnetic Pinned Layer30]

In the preferred embodiment according to the present invention, the magnetic pinned layer30is made of a CoFe alloy system in which a CoFe alloy or CoFe is a main component is formed on the Cu layer that is the spacer layer40. The magnetic pinned layer30has a thickness of, for example, approximately 2 to 10 nm.

As shown inFIG. 1, the magnetic pinned layer30is magnetically pinned by an influence of the antiferromagnetic layer22that is formed on the magnetic pinned layer30and that performs a pinning function.

In the present invention, it is particularly preferred that the CoFe layer configuring the magnetic pinned layer30is oriented in a (001) plane on the Cu layer configuring the spacer layer40, and that the CoFe layer is epitaxially-formed on the Cu layer.

As discussed above, since the antiferromagnetic layer22is exchange-coupled with the magnetic pinned layer30, the antiferromagnetic layer22functions to pin a magnetization direction of the magnetic pinned layer30.

The antiferromagnetic layer22is made of an antiferromagnetic material at least containing one element M′ and Mn. Herein, the element M′ is selected from a group, for example, consisting of Pt, Ru, Rh, Pd, Ni, Cu, Ir, Cr, and Fe. The Mn content is preferably 35 to 95% by atomic weight. The antiferromagnetic materials are categorized in two types:

(1) non-heat treatment type antiferromagnetic materials that exhibit antiferromagnetism without heat treatment and induce an exchange-coupled magnetic field between themselves and a ferromagnetic material; and

(2) heat treatment type antiferromagnetic materials that exhibit antiferromagnetism with heat treatment. In the above type (1), heat treatment is usually conducted to align an exchange-coupling direction. Either type, (1) or (2), can be used in the present invention. Examples of non-heat treatment type antiferromagnetic materials include RuRhMn, FeMn, and IrMn. Examples of heat treatment type antiferromagnetic material include PtMn, NiMn, and PtRhMn.

The antiferromagnetic layer22has a thickness of approximately 4 to 30 nm.

[Explanation of Under Layer21]

The under layer21is formed below the free layer50. As mentioned above, the under layer21can be considered to have an additional function as a part of an electrode that connects to the first shield layer3(lower electrode layer3). In this sense, the under layer21is also called a pseudo-electrode under layer21.

A lamination structure of the preferred under layer21shown inFIG. 1is explained.

As shown inFIG. 1, the under layer21is configured with the following lamination layers in a bottom up direction: (1) a Ta layer with reference numeral21a, (2) a NiFeN layer with21b, (3) a Cu layer with21c, and (4) a Fe4N layer with21d.

The Ta layer21ais made from a thin film in amorphous status. The Ta layer21afunctions as a resetter for preventing an orientation influence caused by the first shield layer3(lower electrode layer3).

The Ta layer21ahas a thickness of approximately 1 to 20 nm. It is not necessary to use Ta when another material functions to reset an orientation influence. For example, Zr, Hf, CoFeB, CoZrTa, and so on, can be used instead of Ta.

The NiFeN layer21bis formed on the Ta layer21aand has a thickness of approximately 0.5 to 20 nm. The NiFeN layer21bis configured with a (001) plane orientation. The NiFeN layer21bwith the (001) plane orientation is formed by a sputtering method in an argon atmosphere to which a nitrogen gas is added with NiFe as a target. The content ratio of nitrogen in the layer is approximately 0.5 to 25% by atomic weight. More preferably, it is 2 to 15% by atomic weight.

When the content of nitrogen exceeds the range mentioned above, the (001) plane orientation of the NiFeN layer21bis difficult to achieve. The NiFeN layer21bwith the (001) plane orientation is a preliminary arrangement to affect an influence on the (001) plane orientation of the free layer50.

The Cu layer21cand the Fe4N layer21dare respectively formed on or above the NiFeN layer21bin this order and are configured with a (001) plane orientation.

The Cu layer21cis formed primarily for increasing crystallinity of a free layer and a spacer layer.

The Fe4N layer21dis formed to coordinate a distance of the crystalline lattice by expanding it. The Fe4N layer21dhas a thickness of approximately 2 to 20 nm.

[Explanation of Cap Layer26]

As shown inFIG. 1, a cap layer26that is made of, for example, a Ta layer or a Ru layer is formed on the antiferromagnetic layer22. The cap layer26has a thickness of approximately 0.5 to 20 nm.

[Explanation of Functions for Main Parts of Present Invention]

In a conventional CPP-GMR element that has a structure of CoFe (magnetic layer)/Cu (spacer layer)/CoFe (magnetic layer), in which the Cu spacer layer is sandwiched between two CoFe ferromagnetic layers, a technology in which (110) planes that are closely-packed are laminated is used for a BCC-CoFe alloy that functions as a magnetic layer for an MR element. Due to the structure, a large MR ratio cannot be obtained by the CPP-GMR element having the CoFe (magnetic layer)/Cu (spacer layer)/CoFe (magnetic layer) structure.

In contrast, in the present invention, since a (001) plane of a BCC-CoFe alloy and a (001) plane of a nonmagnetic metal configured for a spacer layer are united, a structure is realized in which spin scattering is small by assimilating atomic scale differences. It is quite different from the conventional art.

Further, as will be explained below, a layer configuration is realized in which a (001) plane of a magnetic layer and a (001) plane of a nonmagnetic layer (spacer layer) are both grown to form the lamination structure, and where the (001) plane is not a closely-packed, thereby increasing an MR ratio.

A closely-packed plane of BCC-CoFe is a (110) plane. When a Cu layer is formed on a BCC-CoFe layer under ordinary conditions, the Cu layer is oriented in a (111) plane. A mismatch ratio in its lattice is small in the above structure. However, if there is a mismatching of the lattices, regardless of the size of the mismatch, lattice defects will unavoidably exist in the lamination layer on which the closely-packed planes face each other. The defect causes spin scattering.

In contrast, a BCC-CoFe alloy is first oriented in a (001) plane. Then, a Cu layer is formed on the BCC-CoFe alloy. The Cu layer has a BCC structure rather than a typical FCC structure. The Cu layer is oriented in a (001) plane. (It seems that since lattice distortion in the Cu layer occurs due to a pulling force from a lattice in the layer underneath, the Cu layer has the BCC structure.) With the structure, considering ratios either of Cu atoms and Co atoms or of Cu atoms and Fe atoms that exist in the vicinity of the interface, a contact ratio with a magnetic element becomes larger compared with a (110) orientation structure. Therefore, a mutual interaction between Cu in the interface and Co or Fe becomes strong so that a polarizability of Co, Fe, and Cu is increased. With the phenomenon mentioned above, since a spin polarizability is increased in a (001) orientation system compared to a (110) orientation system, an increase of an MR ratio can be achieved. At the same time, the problem of small differences minute in atomic size is resolved by forming a plane other than a close-packed plane, so that spin scattering becomes small. This also contributes to an increase in an MR ratio.

[Explanation of Overall Structure of Thin Film Magnetic Head]

FIG. 2shows a sectional view (i.e., a cross section taken through the Y-Z plane) of a thin film magnetic head in parallel with the so-called air bearing surface (ABS).

A thin film magnetic head100as shown inFIG. 2is mounted on a magnetic recording device such as a hard disk drive in order to magnetically process a recording medium10such as a hard disk that moves in a medium traveling direction M.

The thin film magnetic head100as exemplified in the drawing is a so-called complex type head that is executable for both recording processing and reproducing processing as magnetic processing. As shown inFIG. 2, it has a structure of a magnetic head part101formed on a slider substrate1structured of ceramic material such as ALTIC (Al2O3.TiC).

A magnetic head part101has a lamination constitution of a reproducing head part100A for reproducing magnetic information recorded using the MR effect and, for example, a shield type recording head part100B for executing the recording processing of the perpendicular recording system.

A description is given below in more detail.

A first shield layer3and a second shield layer5are flat layers formed in a manner of being substantially parallel to the side surface1aof the slider substrate1. These layers3and5form a part of the ABS that is the ABS70.

An MR effect part8is sandwiched between the first shield layer3and the second shield layer5and forms part of the ABS70. A height perpendicular to the ABS70(i.e., in the Y direction) is an MR height (MR-h).

The first shield layer3and the second shield layer5are formed by a pattern plating method including a frame plating method, for example.

The MR effect part8is a lamination layer substantially parallel to the side surface1aof the slider substrate1, and forms a part of the ABS70.

The MR effect part8is a lamination layer in a film surface perpendicular type (or current perpendicular to plane: CPP) structure in which a sense current flows in the direction perpendicular to the laminating surface.

Moreover, as shown inFIG. 2, an interelement shield layer9made of the same material as that of the second shield layer5is formed between the second shield layer5and the recording head part100B.

The interelement layer9functions in a manner of shielding the MR element8that functions as a sensor from a magnetic field generated by the recording head part100B, thereby blocking exogenous noises at the time of reproducing. A bucking coil part may also be formed between the interelement layer9and the recording head part100B. The bucking coil part is to generate magnetic flux that overrides a magnetic flux loop that is generated by the recording head part100B and passes through the upper and lower electrode layers of the MR element8and, therefore, acts in a manner of suppressing unnecessary writing to a magnetic disk or wide area adjacent tracks erasing (WATE) phenomena that are erasing operations.

Insulating layers4and44made of alumina, etc. are formed as follows:

i) in a gap between the first shield layer3and the second shield layer5on the side opposite to the ABS70of the MR element8;

ii) in rear (posterior) regions of the first and second shield layers3and5and the interelement shield layer9, the rear regions being opposite to the ABS70;

iii) in a gap between the first shield layer3and the slider substrate1; and

iv) in a gap between the interelement shield layer9and the recording head part100B.

The recording head part100B is preferably structured for perpendicular magnetic recording and, as shown inFIG. 2, has a main magnetic pole layer15, a gap layer18, a coil insulating layer26, a coil layer23, and an auxiliary magnetic pole layer25. The perpendicular recording system can be exchanged with a so-called longitudinal recording system.

The main magnetic pole layer15is structured to be a leading magnetic path for leading and focusing magnetic flux initiated by the coil layer23to the recording layer of a magnetic recording medium10to be written. It is preferred that the end part of the main magnetic pole layer15on the side of the ABS70should be smaller in thickness compared with other portions in the track width direction (i.e., the direction along the X-axis inFIG. 2) and in the laminating direction (i.e., the direction along the Z-axis inFIG. 2). As a result, it is possible to generate a magnetic field for minute and strong writing corresponding to high recording density.

On the end part of the auxiliary magnetic pole layer25magnetically coupled with the main magnetic pole layer15on the side of the ABS70is formed a trailing shield part that has a wider layer cross section than the other portions of the auxiliary magnetic layer25. As shown inFIG. 2, the auxiliary magnetic pole layer25is disposed in a manner of being opposed to the end part of the main magnetic pole layer15on the side of the ABS70via the gap layer18made of insulating material such as alumina and the coil insulating layer26.

The provision of the auxiliary magnetic pole layer25enables formation of a steep magnetic field gradient between the auxiliary magnetic pole layer25and the main magnetic pole layer15in the vicinity of the ABS70. As a result, jitter is reduced in a signal output, thereby making the error rate smaller at the time of reproducing.

The auxiliary magnetic pole layer25is formed, for example, to about 0.5-5 μm in thickness by a frame plating method, a sputtering method or the like. The material may be an alloy made of two or three elements selected from the group consisting of Ni, Fe and Co, for example, or an alloy made of these elements, as main components, along with predetermined chemical elements.

The gap layer18is formed to separate the coil layer23from the main magnetic pole layer15. The gap layer18may be formed by a sputtering method, a CVD method or the like, for example, have a thickness of about 0.01-0.5 μm and be structured of Al2O3, diamond-like carbon (DLC) or the like.

[Explanation of Function of Thin Film Magnetic Head]

The function of a thin film magnetic head according to the present embodiment is given below. The thin film magnetic head has a function that a recording head writes information on a recording medium, and a reproducing head reads recorded information on the recording medium.

In the reproducing head, a direction of a bias magnetic field of the bias magnetic field application layer6is a direction that is orthogonal to the perpendicular direction relative to the ABS (X direction inFIG. 1). In the MR element8, a magnetization direction of the free layer50is equal to a direction of the bias magnetic field when there is not a signal magnetic field. A magnetization direction of the magnetic pinned layer30is pinned to a direction (Y direction) that is perpendicular to the ABS.

In the MR element8, a magnetization direction of the free layer50is changed based on a signal magnetic field from a recording medium. Then, a relative degree between the magnetization direction of the free layer50and a magnetization direction of the magnetic pinned layer30is changed, and as a result, the resistance of the MR element8is changed. The resistance of the MR element8is obtained through an electric potential difference between two electrodes (or the first and second shield layers3and5) when a sense current flows in the MR element by the first and second shield layers3and5. As described above, the reproducing head is able to read recorded information on the recording medium.

[Explanation of Head Gimbal Assembly and Hard Disk Device]

Next, a head gimbal assembly on which the above mentioned thin film head is mounted and one embodiment of a hard disk device are described below.

First, a description of a slider210equipped with the head gimbal assembly is illustrated inFIG. 3. In the hard disk device, the slider210is disposed in a manner of being opposed to a hard disk that is a rotatably driven disk-like recording medium. The slider210is provided with a base substrate211mainly configured of a substrate and an overcoat.

The base substrate211is substantially hexahedronal. Of the six surfaces of the base substrate211, one surface is disposed in a manner of being opposed to a hard disk. The ABS70is formed on the surface.

When a hard disk is rotated in the Z direction inFIG. 3, an airflow passing between the hard disk and the slider210creates lifting power downwardly in the Y direction inFIG. 3. The slider210floats from the surface of the hard disk by this lifting power. The X direction inFIG. 3is the track traversing direction of the hard disk.

In the vicinity of the end part of the slider210on the air exit side (i.e., the end part on the lower left inFIG. 3), the thin film magnetic head according to the present embodiment is formed.

Next, a description of the head gimbal assembly220according to the present embodiment is described by referring toFIG. 4. The head gimbal assembly220is provided with the slider210and a suspension221for elastically supporting the slider210. The suspension221has a plate spring load beam222formed of stainless steel, a flexure223that is provided on one end part of the load beam222and joined with the slider210in a manner of giving the slider210a proper degree of freedom, and a base plate224provided on the other end part of the load beam222.

The base plate224is mounted on an arm230of an actuator for moving the slider210in the track traversing direction X of the hard disk262. The actuator has the arm230and a voice coil motor for driving the arm230. A gimbal part is provided for keeping a posture of the slider210constant on the portion of the flexure223on which the slider210is mounted.

The head gimbal assembly220is mounted on the arm230of the actuator. One arm230with a head gimbal assembly220mounted thereon is called a head arm assembly. A carriage having multiple arms, each of which has a head gimbal assembly mounted thereon, is referred as a head stack assembly.

FIG. 4shows one embodiment of a head arm assembly. In this head arm assembly, a head gimbal assembly220is mounted on one end part of the arm230. A coil231, part of a voice coil motor, is mounted on the other end part of the arm230. A bearing part233is provided in the middle part of the arm230so that a shaft234is rotatably supported.

A description of one example of the head stack assembly and the hard disk device according to the present embodiment is described by referring toFIG. 5andFIG. 6.

FIG. 5is an illustration for explaining primary parts of a hard disk device.FIG. 6is a plan view of the hard disk device.

The head stack assembly250has a carriage251having multiple arms252. On the multiple arms252are mounted multiple head gimbal assemblies220in the perpendicular direction at certain intervals. A coil253, part of a voice coil motor, is mounted on the opposite side of the arms252in the carriage251. The head stack assembly250is incorporated into a hard disk device.

A hard disk device has multiple hard disks262mounted on a spindle motor261. Two sliders210are disposed for each hard disk262in a manner of being opposed to each other by sandwiching the hard disk262. The voice coil motor has permanent magnets263disposed in a manner of being opposed to each other by sandwiching the coil253of the head stack assembly250.

The head stack assembly250and an actuator except for sliders210support as well as locate the slider210relative to the hard disk22corresponding to a positioning device of the present invention.

In the hard disk device according to the present embodiment, an actuator allows moving sliders210in the track traversing direction of the hard disk262in order to position sliders210relative to the hard disk262. Thin film magnetic heads included in sliders210record information on the hard disk262by the recording head and reproduce (or read) information recorded in the hard disk262by the reproducing head.

The head gimbal assembly and hard disk device according to the present embodiment are as effective as the thin film magnetic head according to the above-mentioned embodiment.

In the embodiment, it is explained that a thin film magnetic head has a structure of a reproducing head part formed on the base substrate side and a perpendicular recording head part layered thereon. However, the layering order may be reversed. Moreover, the configuration may be such that only a reproducing part is provided in the case of a reproduction-only thin film head.

EXEMPLARY EMBODIMENT

The present invention related to a CPP-GMR element discussed above is explained through a detailed exemplary embodiment.

A CPP-GMR element configured with a lamination structure as shown in Table 1 below was formed by a sputtering method. This is Sample 1 of an embodiment according to the present invention.

As shown in Table 1, a basic structure of a lamination structure is that an under layer21(pseudo-electrode under layer21) was formed on a lower shield layer3that has a layer thickness of 1000 nm and that was made of NiFe. The under layer21was configured with the following lamination layers in a bottom up direction: a Ta layer with a layer thickness of 2 nm; a NiFeN layer with a layer thickness of 5 nm; a Cu layer with a layer thickness of 10 nm; and a Fe4N layer with a layer thickness of 5 nm.

The Ta layer was in an amorphous state and had a function to reset an orientation. The NiFeN layer was formed by a sputtering method in an argon gas atmosphere to which a nitrogen gas was added with NiFe as a target. A content rate of nitrogen in the NiFeN layer was 3% by atomic weight, and it was confirmed that the NiFeN layer was oriented in a (001) plane. It was also confirmed that the Cu layer and Fe4N layer that were formed on the NiFeN layer in this order were oriented in a (001) plane.

A free layer50made of a CoFe layer with a layer thickness of 4 nm was formed on the under layer21. A crystal structural analysis with respect to a crystalline orientation was performed through an X-ray diffraction (XRD) measurement and a transmission electron microscope (TEM) observation. It was confirmed that this CoFe layer (free layer50) was oriented in a (001) plane.

Next, a spacer layer40made of a Cu layer with a layer thickness of 3 nm was formed on the CoFe layer (free layer50). A crystal structural analysis with respect to a crystalline orientation was performed through an XDR measurement and a TEM observation. It was confirmed that this Cu layer (spacer layer40) was oriented in a (001) plane.

Then, a magnetic pinned layer30made of a CoFe layer with a layer thickness of 4 nm was formed on the Cu layer (spacer layer40). A crystal structural analysis with respect to a crystalline orientation was performed through an XDR measurement and a TEM observation. It was confirmed that this CoFe layer (magnetic pinned layer30) was oriented in a (001) plane.

An antiferromagnetic layer22made of a MnIr layer with a layer thickness of 7.5 nm was formed on the CoFe layer (magnetic pinned layer30). With influence from this antiferromagnetic layer22, magnetization of the CoFe layer (magnetic pinned layer30) was pinned.

A cap layer configured with two layers, Ru with a thickness of 10 nm and Ta with a thickness of 2.0 nm, was formed on the antiferromagnetic layer22.

A lamination layer discussed above that forms a main structure of an element was fabricated in a quadrangular prism shape with dimensions of 200 nm×200 nm. Then, an insulating layer (Al2O3) with a layer thickness of 20.0 nm covered sides of the fabricated quadrangular prism shape, and an upper electrode layer (Cu 20 nm) was formed at the top portion. As a result, Sample 1 of the present embodiment according to the present invention was made.

In Sample 1 of the present embodiment according to the present invention, Comparison Sample 1 was formed for inserting a Ta layer with a layer thickness of 1 nm between the Fe4N layer as the under layer21and the free layer50.

Other than that, Comparison Sample 1 was formed with a laminated structure described in Table 2 below through the similar processes of Sample 1.

In Comparison Sample 1, since an amorphous Ta layer with a layer thickness of 1 nm was formed on a Fe4N layer as an under layer21, a (001) orientation condition of the under layer, laminated NiFeN, Cu, and Fe4N layers, was canceled based on the amorphous Ta layer.

In fact, a CoFe layer was oriented in a (110) plane. The CoFe layer was a free layer50and was formed on the amorphous Ta layer. A Cu layer as a spacer layer40that was formed on the CoFe layer (free layer50) was oriented in a (111) plane.

A CoFe layer as a magnetic pinned layer30that was formed on the Cu spacer layer40was oriented in a (110) plane.

With respect to Sample 1 and Comparison Sample 1 formed by the above conditions in Table 1 and Table 2, respectively, (1) an area resistivity AR (Ω·μm2) of an MR element and (2) an MR ratio were obtained through the following procedures.

(1) Area Resistivity AR (Ω·μm2) of Element

It was measured by a DC four-probe method. The number of samples was 100 (n=100), and the AR was calculated through an average of ARs of 100 samples.

(2) MR Ratio

An MR ratio was measured by an ordinary DC four-probe method. The MR ratio was calculated through dividing “a variation of a resistance ΔR” by “a resistance R,” represented as ΔR/R. The number of samples was 100 (n=100), and the MR ratio was calculated through an average of MRs of 100 samples.

It is noted that with respect to the MR ratio, when the MR ratio of Comparison Sample 1 is set as a value of “1,” the MR ratio of Sample 1 of the present embodiment is shown in its relative value.

The results are shown in Table 3 below.

According to the experimental results above, an effect of the present invention is apparent.

The MR element of the present invention that is a giant magnetoresistive effect element in a current perpendicular to plane (CPP) structure includes a spacer layer made of Cu, a magnetic pinned layer containing CoFe and a free layer containing CoFe that are laminated to sandwich the spacer layer, in which a sense current flows along a lamination direction of the layers. The free layer is formed before the magnetic pinned layer is formed, and is located below the magnetic pinned layer, a magnetization direction of the free layer varies depending on an externally applied magnetic field, a magnetization direction of the magnetic pinned layer is pinned. The free layer is oriented in a (001) crystal plane, the spacer layer is formed and oriented in a (001) crystal plane on the (001) crystal plane of the free layer. Therefore, in a low resistance area that has an AR of an MR element is, for example, lower than 0.3 Ω·μm2, an MR element that has a large variation of a resistance is obtained.

Possibilities for the industrial use of the present invention include its use in a magnetic disk device with an MR element that detects magnetic field intensity as a signal from a magnetic recording medium, and so on.