JP2005294453A - Magnetic detection element - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a magnetic detection element having a self-stationary type of lamination ferry stationary layer, wherein the material of a non-magnetic film formed on an opposing side to a side where a non-magnetic material layer of the lamination ferry stationary layer is formed, and the material of a ferromagnetic layer constituting the lamination ferry stationary layer are suitably selected, thereby firmly fixing the magnetization of the lamination ferry stationary layer. <P>SOLUTION: The first magnetic layer 23a of a stationary magnetic layer 23 is formed on a non-magnetic metal layer 22. The non-magnetic metal layer 22 is composed of an X-Mn alloy (wherein X is the element of a kind or two kinds or more of any one of Pt, Pd, Ir, Rh, Ru, Os, Ni and Fe). The first magnetic layer 23a contains Co and Fe as a main body, and further a rare-earth element or a noble metal element is added thereto. A strain occurs in a crystal structure of the first magnetic layer 23a by this lamination structure, thereby enabling a magnetic strain constant λ to be increased, and the magnetic detection element having a large magnetic elastic effect can be provided. <P>COPYRIGHT: (C)2006,JPO&NCIPI

Description

  The present invention relates to a magnetic detection element having a free magnetic layer, a nonmagnetic material layer, and a fixed magnetic layer, and more particularly to a magnetic detection element that fixes the magnetization of a fixed magnetic layer by uniaxial anisotropy of the fixed magnetic layer itself.

  The current mainstream of the magnetic head mounted on the magnetic recording / reproducing apparatus uses a spin-valve type magnetic detection element to which a giant magnetoresistance (GMR) effect is applied.

  A spin-valve type magnetic sensing element is formed by laminating a ferromagnetic film called a pinned magnetic layer and a ferromagnetic soft magnetic film called a free magnetic layer via a nonmagnetic film called a nonmagnetic material layer.

  The magnetization of the free magnetic layer is aligned in one direction by a longitudinal bias magnetic field from a hard bias layer made of a hard magnetic material. The magnetization of the free magnetic layer fluctuates with high sensitivity to an external magnetic field from the recording medium. On the other hand, the magnetization of the pinned magnetic layer is pinned in a direction crossing the magnetization direction of the free magnetic layer.

  The electrical resistance changes depending on the relationship between the change in the magnetization direction of the free magnetic layer and the fixed magnetization direction of the fixed magnetic layer, and the leakage magnetic field from the recording medium is detected by the voltage change or current change based on the change in the electrical resistance value. Is done.

  Conventionally, the pinned magnetic layer is formed to overlap an antiferromagnetic layer made of an antiferromagnetic material such as PtMn, and a unidirectional exchange coupling magnetic field is generated between the pinned magnetic layer and the antiferromagnetic layer. As a result, the magnetization of the pinned magnetic layer is fixed.

  However, in order to generate a sufficiently large exchange coupling magnetic field at the interface between the antiferromagnetic layer and the pinned magnetic layer, the thickness of the antiferromagnetic layer has to be about 200 mm.

  An antiferromagnetic layer having a large film thickness present in the laminated body constituting the magnetic detection element is a main cause of a sense current shunt loss. In order to cope with an increase in recording density of the recording medium, it is necessary to improve the output of the magnetic detection element. However, the above-described shunt loss of the sense current hinders improvement of the output of the magnetic detection element.

  In addition, shield layers made of a soft magnetic material are provided above and below the magnetic detection element in order to efficiently read a recording signal to be detected. In order to cope with the higher linear recording density of the recording medium, it is necessary to shorten the distance between the upper and lower shield layers. The antiferromagnetic layer having a large thickness has also hindered shortening the distance between the upper and lower shield layers.

  Therefore, a magnetic sensing element has been proposed in which the antiferromagnetic layer is omitted and the magnetization of the pinned magnetic layer is pinned by uniaxial anisotropy of the pinned magnetic layer itself.

The patent documents before filing this application are shown below.
JP-A-8-7235 JP 2000-113418 A

  The magnetic detection element described in Patent Document 1 is obtained by stacking a pinned ferromagnetic layer 70 on a buffer layer 62 made of tantalum (Ta). The pinned ferromagnetic layer 70 is formed by laminating a first cobalt (Co) film 72 and a second cobalt (Co) film 74 via a ruthenium (Ru) film 73. Magnetization of the first cobalt (Co) film 72 and the second cobalt (Co) film 74 is fixed by respective anisotropic magnetic fields. The first cobalt (Co) film 72 and the second cobalt (Co) film 74 are antiferromagnetically coupled and are magnetized in antiparallel directions.

  However, it was found that the magnetization direction of the pinned ferromagnetic layer 70 cannot be fixed appropriately in the configuration in which the Co film is laminated on the buffer layer made of tantalum as in the magnetic detection element described in Patent Document 1. . This is also pointed out in Patent Document 2.

  The magnetic detection element described in Patent Document 2 was invented for the purpose of solving the problem of Patent Document 1. In this magnetic sensing element, the induced magnetic anisotropy is improved by forming the ferromagnetic film of the laminated ferrimagnetic fixed layer of CoFe or CoFeNi.

  In order to fix the magnetization of the self-fixed pinned magnetic layer, one of the important factors is uniaxial anisotropy derived from the magnetoelastic energy of the pinned magnetic layer. In particular, it is important to optimize the magnetostriction of the pinned magnetic layer.

  If the magnetostriction of the pinned magnetic layer can be increased, it is possible to provide a magnetic detection element that is unlikely to cause magnetization reversal even when a transient current due to electrostatic discharge (ESD) flows, for example.

  However, Patent Document 2 does not discuss a mechanism for optimizing the magnetostriction of the pinned magnetic layer, and does not describe a specific configuration for optimizing the magnetostriction of the pinned magnetic layer.

  Therefore, the present invention is to solve the above-described conventional problems, and in a magnetic detection element having a self-fixing type laminated ferrimagnetic pinned layer, a mechanism for controlling the magnetostriction of the laminated ferrimagnetic pinned layer is clarified, and the magnetostriction is determined. In order to control appropriately, the material of the non-magnetic film formed on the side opposite to the side on which the non-magnetic material layer of the laminated ferri pinned layer is formed, and the material of the ferromagnetic layer constituting the laminated ferri pinned layer are appropriately selected. It is an object of the present invention to provide a magnetic detecting element capable of firmly fixing the magnetization of the laminated ferrimagnetic pinned layer.

The present invention provides a magnetic sensing element in which a pinned magnetic layer and a free magnetic layer are laminated via a nonmagnetic material layer.
The pinned magnetic layer includes a plurality of magnetic layers stacked via a nonmagnetic intermediate layer, and is formed at a position farthest from the nonmagnetic material layer among the plurality of magnetic layers. X-Mn (where X is one or more of Pt, Pd, Ir, Rh, Ru, Os, Ni, Fe) on the opposite side of the magnetic layer to the side on which the nonmagnetic material layer is provided A non-magnetic metal layer made of an alloy is formed,
The first magnetic layer is mainly composed of Co and Fe, and further added with a rare earth element or a noble metal element,
At least part of the crystals in the nonmagnetic metal layer and the crystals in the first magnetic layer are in an epitaxial or heteroepitaxial state,
The end surface of the fixed magnetic layer facing the recording medium is open.

  The present invention is a so-called self-fixed magnetic detection element in which the magnetization of the pinned magnetic layer is pinned by uniaxial anisotropy of the pinned magnetic layer itself.

  Therefore, since the shunt loss can be reduced as compared with the magnetic detection element having a thick antiferromagnetic layer having a thickness of 200 mm, the magnetic field detection output of the magnetic detection element can be improved by 20 to 30%. In addition, since the distance between the shield layers provided above and below the magnetic detection element is shortened, it is possible to cope with further increase in the recording density of the recording medium.

  Factors that determine the magnetic anisotropy field of the ferromagnetic film include crystal magnetic anisotropy, induced magnetic anisotropy, and magnetoelastic effect. Among these, the magnetocrystalline anisotropy can be increased by increasing the coercive force. On the other hand, the induced magnetic anisotropy is uniaxial by applying a unidirectional magnetic field during film formation or heat treatment, and the magnetoelastic effect is uniaxial by applying uniaxial stress.

  The present invention has been made by paying attention to the magnetoelastic effect among the induced magnetic anisotropy and the magnetoelastic effect that determine the uniaxial anisotropy for fixing the magnetization of the fixed magnetic layer.

  The magnetoelastic effect is dominated by magnetoelastic energy. The magnetoelastic energy is defined by the stress applied to the pinned magnetic layer and the magnetostriction constant of the pinned magnetic layer.

  In the present invention, since the end surface of the fixed magnetic layer facing the recording medium is open, stress symmetry is broken, and the fixed magnetic layer has an element height direction (height direction; Tensile stress acts in the direction normal to the surface. In the present invention, the magnetoelastic energy is increased by increasing the magnetostriction constant of the pinned magnetic layer, thereby increasing the uniaxial anisotropy of the pinned magnetic layer. When the uniaxial anisotropy of the pinned magnetic layer is increased, the magnetization of the pinned magnetic layer is firmly fixed in a fixed direction, the output of the magnetic detection element is increased, and the stability and symmetry of the output are also improved.

  In the present invention, first, the pinned magnetic layer has a synthetic ferri-pinned structure (hereinafter sometimes referred to as a laminated ferri-pinned layer), and among the plurality of magnetic layers constituting the laminated ferri-pinned layer, the nonmagnetic material layer is the most. X-Mn (where X is Pt, Pd, Ir, Rh, Ru, Ru, Os, Ni) on the opposite side of the first magnetic layer formed at a distance from the side where the nonmagnetic material layer is provided. A nonmagnetic metal layer made of an alloy (which is one or more elements of Fe, Fe) is formed.

  The lattice constant of the nonmagnetic metal layer is larger than the lattice constant of the first magnetic layer, but at least part of the crystals in the nonmagnetic metal layer and the crystals in the first magnetic layer are epitaxial or heteroepitaxial. Therefore, the crystal structure is distorted near the interface of the first magnetic layer. As a result, the magnetostriction constant of the first magnetic layer can be increased.

In the present invention, not only the material of the nonmagnetic metal layer but also the material of the first magnetic layer are improved.
The elements necessary for the first magnetic layer have a positive magnetostriction constant, a strong RKKY interaction acting between the ferromagnetic layers constituting the laminated ferrimagnetic fixed layer, and the crystal orientation of the magnetic sensing element It is thought that it is not breaking down.

  The reason why the positive magnetostriction is necessary is that, as described above, tensile stress acts on the pinned magnetic layer in the element height direction (height direction; normal direction to the facing surface). This is because the magnetization direction of the layer is appropriately oriented in the height direction.

  The RKKY interaction needs to be increased in order to strengthen the antiferromagnetic coupling between the ferromagnetic layers constituting the laminated ferri pinned layer. If the RKKY interaction is weakened, the magnetization of the ferromagnetic layer is easily rotated by an external magnetic field or the like, which adversely affects the GMR characteristics.

  The high crystal orientation of the magnetic sensing element is an important factor for GMR characteristics. If the crystal orientation is lost (lower crystal orientation), the rate of change in resistance (ΔR / R) is reduced. It is not preferable that the crystal orientation is broken by improving the material of one magnetic layer.

  In the present invention, a magnetic material in which the lattice constant of the first magnetic layer is larger than that of a CoFe alloy or Co that has been generally used as the first magnetic layer in the past is selected in consideration of the above conditions.

  That is, in the present invention, the first magnetic layer is formed of a magnetic material mainly composed of Co and Fe and further added with a rare earth element or a noble metal element. This magnetic material has a larger lattice constant than the CoFe alloy and Co that are conventionally used as the first magnetic layer, and as a result, epitaxial or heteroepitaxial growth is promoted with the nonmagnetic metal layer. As a result, the crystal structure of the first magnetic layer is more effectively distorted, and the magnetostriction constant λs of the first magnetic layer can be further increased as compared with the conventional case.

  In the present invention, the rare earth element is preferably selected from at least one of Tb, Sm, Pr, Y, Ce, Nd, Gd, Dy, Ho, Er, and Yb.

In such a case, the first magnetic _{layer, (Co x Fe 1-x} ) formed of a magnetic material represented by _{100-y M y,} element M, Tb, Sm, Pr, Y , Ce, Nd, Gd, It is preferable that at least one kind is selected from Dy, Ho, Er, and Yb, and the composition ratio y is 0.3 at% or more and 5 at% or less.

  According to the experimental results described later, it was found that by setting the composition ratio y within the above range, the magnetostriction constant λs of the first magnetic layer can be increased as compared with the magnetic material to which the element M is not added.

  In the present invention, the noble metal element is preferably selected from at least one of Pt, Rh, Ir, and Re.

In such a case, the first magnetic _{layer, (Co x Fe 1-x} ) formed of a magnetic material represented by _{100-z N z,} the element N is, Pt, Rh, Ir, at least one from among Re The composition ratio z is preferably 5 at% or more and 20 at% or less. According to the experimental results described later, it was found that by setting the composition ratio z within the above range, the magnetostriction constant λs of the first magnetic layer can be increased as compared with a magnetic material to which no element N is added.

The atomic ratio x is preferably 1 or in the range of 0.4 to 0.6.
Furthermore, the film thickness of the first magnetic layer is preferably within a range of 12 to 19 mm.

  In the present invention, the first magnetic layer has a laminated structure of at least two layers, and the magnetic layer formed closest to the nonmagnetic metal layer is mainly composed of Co and Fe, and further includes rare earth elements or The magnetic layer may be formed of a magnetic material to which a noble metal element is added. In such a case, among the magnetic layers constituting the first magnetic layer, the magnetic layer in contact with the nonmagnetic intermediate layer is a CoFe alloy or Co. Is preferably formed. As a result, the magnetostriction constant λs of the first magnetic layer can be appropriately increased as compared with the conventional one, and the RKKY interaction works as strongly as the conventional one, so that the plurality of magnetic layers constituting the laminated ferri pinned layer are antiparallel to each other. Can be strongly magnetized.

  In the present invention, it is preferable that the nonmagnetic metal layer is formed in contact with the interface of the first magnetic layer. As a result, the crystal structure near the interface of the first magnetic layer can be more effectively distorted, and the magnetostriction constant λs of the first magnetic layer can be increased.

  In the present invention, the nonmagnetic metal layer has a face-centered cubic lattice (fcc) structure near or in the entire region of the pinned magnetic layer on the first magnetic layer side, and in a direction parallel to the interface, {111 } It is preferable that the equivalent crystal plane expressed as a plane is preferentially oriented. Thereby, the crystal orientation of the magnetic detection element can be improved, and the GMR characteristics can be improved.

  In the present invention, the nonmagnetic metal layer preferably has a thickness of 5 to 50 mm.

  The content of the X element in the X—Mn alloy (where X is one or more of Pt, Pd, Os, Ni, and Fe) is 45 atomic% to 99 atomic%. Is preferred.

  Further, the content of the X element in the X—Mn alloy (where X is one or more of Ir, Rh, and Ru) is preferably from 17 atomic% to 99 atomic%.

Furthermore, the content of Ir in the Ir—Mn alloy is preferably 20 atomic% or more and 99 atomic% or less.
Thereby, the magnetostriction of the first magnetic layer can be increased more appropriately.

  In the present invention, the first magnetic layer of the pinned magnetic layer has a face-centered cubic lattice (fcc) structure or a body-centered cubic lattice (bcc) structure in the vicinity of the interface on the nonmagnetic metal layer side or in the entire region. It is preferable that an equivalent crystal plane represented as {111} plane or {110} plane is preferentially oriented in a direction parallel to the interface. Thereby, the crystal orientation of the magnetic detection element can be improved, and the GMR characteristics can be improved.

  In the present invention, the free magnetic layer, the nonmagnetic material layer, and the pinned magnetic layer are preferably laminated in this order from the bottom. As a result, the crystal orientation of the magnetic detection element is improved as in the conventional case, and the resistance change rate (ΔR / R) can be obtained to the same extent as in the conventional case.

  In the present invention, in a magnetic sensing element having a self-fixed pinned magnetic layer, a mechanism for controlling the magnetostriction of the pinned magnetic layer is clarified, and the material of the nonmagnetic metal layer in contact with the pinned magnetic layer and the material of the first magnetic layer are clarified. By appropriately selecting the above, it is possible to provide a magnetic detection element capable of appropriately controlling the magnetostriction and firmly fixing the magnetization of the fixed magnetic layer.

  Specifically, the pinned magnetic layer is formed by laminating a plurality of magnetic layers via a nonmagnetic intermediate layer, and is formed at a position farthest from the nonmagnetic material layer among the plurality of magnetic layers. X—Mn (where X is any one of Pt, Pd, Ir, Rh, Ru, Os, Ni, Fe) on the opposite side of the first magnetic layer to the side on which the nonmagnetic material layer is provided, The nonmagnetic metal layer made of an alloy (which is two or more elements) is formed.

  In the present invention, the first magnetic layer is formed of a magnetic material mainly composed of Co and Fe, and further added with a rare earth element or a noble metal element. As a result, the lattice constant of the first magnetic layer can be increased as compared with the conventional case where the first magnetic layer is formed of CoFe or Co.

  As a result, in the laminated structure of the nonmagnetic metal layer and the first magnetic layer, the crystals are easily grown epitaxially or heteroepitaxially, and the crystal structure near the interface of the nonmagnetic metal layer is appropriately distorted. The magnetostriction constant λ of the first magnetic layer can be effectively increased. The magnetoelastic energy can be increased by increasing the magnetostriction constant of the pinned magnetic layer, and the uniaxial anisotropy of the pinned magnetic layer can be increased.

  When the uniaxial anisotropy of the pinned magnetic layer is increased, the magnetization of the pinned magnetic layer is firmly fixed in a fixed direction, the output of the magnetic detection element is increased, and the stability and symmetry of the output are also improved.

  FIG. 1 is a cross-sectional view of the magnetic detection element according to the first embodiment of the present invention as viewed from the side facing the recording medium.

  In the magnetic detection element shown in FIG. 1, a multilayer film T1 is formed on a lower gap layer 20 made of an insulating material such as alumina.

  In the embodiment shown in FIG. 1, the multilayer film T1 is formed by laminating a seed layer 21, a nonmagnetic metal layer 22, a pinned magnetic layer 23, a nonmagnetic material layer 24, a free magnetic layer 25, and a protective layer 26 in this order from the bottom. It is.

The seed layer 21 is made of NiFe alloy, NiFeCr alloy, Cr, Ta, or the like. Seed layer 21 is formed of, for example, _{(Ni 0.8 Fe 0.2) 60at%} Cr 40at% of thickness 35A～60A.

When the seed layer 21 is present, the {111} orientation of the nonmagnetic metal layer 22 is improved.
The nonmagnetic metal layer 22 will be described later.

  The pinned magnetic layer 23 has an artificial ferri structure in which a first magnetic layer 23a and a second magnetic layer 23c are laminated via a nonmagnetic intermediate layer 23b. The magnetization of the pinned magnetic layer 23 is pinned in a direction parallel to the height direction (Y direction in the drawing) by the uniaxial anisotropy of the pinned magnetic layer 23 itself.

  The nonmagnetic material layer 24 is a layer that prevents magnetic coupling between the pinned magnetic layer 23 and the free magnetic layer 25, and may be formed of a nonmagnetic material having conductivity such as Cu, Cr, Au, or Ag. preferable. In particular, it is preferably formed of Cu. The film thickness of the nonmagnetic material layer is 17 to 30 mm.

  The free magnetic layer 25 is formed of a magnetic material such as a NiFe alloy or a CoFe alloy. In the embodiment shown in FIG. 1, a diffusion prevention layer (not shown) made of Co, CoFe, or the like is formed between the free magnetic layer 25 and the nonmagnetic material layer 24 particularly when the free magnetic layer 25 is formed of a NiFe alloy. It is preferable that The film thickness of the free magnetic layer 25 is 20 to 60 mm. The free magnetic layer 25 may have an artificial ferri structure in which a plurality of magnetic layers are stacked with a nonmagnetic intermediate layer interposed therebetween.

  The protective layer 26 is made of Ta or the like and suppresses the progress of oxidation of the multilayer film T1. The thickness of the protective layer 26 is 10 to 50 mm.

  In the embodiment shown in FIG. 1, a bias underlayer 27, a hard bias layer 28, and an electrode layer 29 are formed on both sides of the multilayer film T1 from the seed layer 21 to the protective layer 26. The magnetization of the free magnetic layer 25 is aligned in the track width direction (X direction in the drawing) by the longitudinal bias magnetic field from the hard bias layer 28.

  The bias underlayers 27, 27 are made of Cr, W, Ti, and the hard bias layers 28, 28 are made of, for example, a Co—Pt (cobalt-platinum) alloy or a Co—Cr—Pt (cobalt-chromium-platinum) alloy. The electrode layers 29 and 29 are made of Cr, Ta, Rh, Au, W (tungsten), or the like.

  The thickness of the bias underlayers 27 and 27 is 20 to 100 mm, the thickness of the hard bias layers 28 and 28 is 100 to 400 mm, and the thickness of the electrode layers 29 and 29 is 400 to 1500 mm.

  An upper gap layer 30 made of an insulating material such as alumina is laminated on the electrode layers 29 and 29 and the protective layer 26. Although not shown, a lower shield layer is provided below the lower gap layer 20, and an upper shield layer is provided on the upper gap layer. The lower shield layer and the upper shield layer are formed of a soft magnetic material such as NiFe. The film thickness of the upper gap layer and the lower gap layer is 50 to 300 mm.

  The magnetization of the free magnetic layer 25 is aligned in the track width direction (X direction in the drawing) by the longitudinal bias magnetic field from the hard bias layers 28 and 28. The magnetization of the free magnetic layer 25 fluctuates with high sensitivity to the signal magnetic field (external magnetic field) from the recording medium. On the other hand, the magnetization of the pinned magnetic layer 23 is pinned in a direction parallel to the height direction (Y direction in the drawing).

  The electrical resistance changes depending on the relationship between the change in the magnetization direction of the free magnetic layer 25 and the fixed magnetization direction of the fixed magnetic layer 23 (particularly the fixed magnetization direction of the second magnetic layer 23c), and a voltage based on the change in the electrical resistance value. The leakage magnetic field from the recording medium is detected by the change or the current change.

Features of this embodiment will be described.
The pinned magnetic layer 23 of the magnetic detection element shown in FIG. 1 has an artificial ferri structure in which a first magnetic layer 23a and a second magnetic layer 23c are stacked with a nonmagnetic intermediate layer 23b interposed therebetween. The magnetization of the first magnetic layer 23a and the magnetization of the second magnetic layer 23c are directed in antiparallel directions by the RKKY interaction via the nonmagnetic intermediate layer 23b.

  In the present invention, the magnetostriction constant λs of the first magnetic layer 23a is made larger than before by optimizing the material of the first magnetic layer 23a and the nonmagnetic metal layer 22 and the like. First, the nonmagnetic metal layer 22 will be described.

  The first magnetic layer 23 a is formed at a position farther from the nonmagnetic material layer 24 than the second magnetic layer 23 c and is in contact with the nonmagnetic metal layer 22.

The nonmagnetic metal layer 22 is formed of an alloy of X—Mn (where X is one or more elements of Pt, Pd, Ir, Rh, Ru, Os, Ni, and Fe). .
The film thickness of the nonmagnetic metal layer 22 is preferably 5 mm or more and 50 mm or less.

  The film thickness of the nonmagnetic metal layer 22 made of X—Mn (where X is one or more of Pt, Pd, Ir, Rh, Ru, Os, Ni, and Fe) is in this range. If it is inside, the crystal structure of the nonmagnetic metal layer 22 continues to maintain the face-centered cubic lattice (fcc) structure that is the state at the time of film formation. When the film thickness of the nonmagnetic metal layer 22 is larger than 50 mm, the crystal structure of the nonmagnetic metal layer 22 is CuAuI type regular face centered square lattice (fct) when heat of 250 ° C. or more is applied. This is not preferable because the structure is transformed into a structure. However, even if the film thickness of the nonmagnetic metal layer 22 is greater than 50 mm, the crystal structure of the nonmagnetic metal layer is the face-centered cubic lattice (fcc ) Continue to maintain the structure.

  The transformation to the CuAuI type ordered phase is not preferable from the viewpoint of magnetostriction enhancement, because atomic rearrangement occurs in the process and the matching relationship at the interface with the first magnetic layer 23a is lost. If the transformation to the ordered phase is performed, the magnetostriction is hardly lowered, and the effect of increasing the coercive force of the first magnetic layer 23a due to antiferromagnetism is also added, so that only a part of it may be ordered.

  A nonmagnetic metal layer 22 made of X—Mn (where X is one or more of Pt, Pd, Ir, Rh, Ru, Os, Ni, Fe) is a face-centered cubic lattice ( fcc) When having a crystal structure, an exchange coupling magnetic field is not generated or very weak at the interface between the nonmagnetic metal layer 22 and the first magnetic layer 23a, and the magnetization of the first magnetic layer 23a is caused by the exchange coupling magnetic field. The direction cannot be fixed.

The nonmagnetic metal layer 22 is antiferromagnetic at room temperature or lower, but most of the nonmagnetic metal layer 22 has a blocking temperature (T _B ) lower than room temperature. Some may have an antiferromagnetic phase having a blocking temperature higher than room temperature.

  In the embodiment shown in FIG. 1, the magnetoelastic effect is mainly used among the induced magnetic anisotropy and the magnetoelastic effect that determine the uniaxial anisotropy for fixing the magnetization of the fixed magnetic layer 23.

  The magnetoelastic effect is dominated by magnetoelastic energy. The magnetoelastic energy is defined by the stress σ applied to the pinned magnetic layer 23 and the magnetostriction constant λ of the pinned magnetic layer 23.

  FIG. 2 is a plan view of the magnetic detection element shown in FIG. 1 as viewed from the upper side (the direction opposite to the Z direction in the drawing). The multilayer film T1 of the magnetic detection element is formed between a pair of bias base layers 27 and 27, hard bias layers 28 and 28, and electrode layers 29 and 29. The bias base layers 27 and 27 and the hard bias layers 28 and 28 are not shown in FIG. 2 because they are provided under the electrode layers 29 and 29. The multilayer film T1, the bias base layers 27 and 27, the hard bias layers 28 and 28, and the electrode layers 29 and 29 are filled with an insulating material layer 31 indicated by hatching.

  Further, the end face F of the multilayer film T1, the bias underlayers 27 and 27, the hard bias layers 28 and 28, and the electrode layers 29 and 29 on the side facing the recording medium is exposed or diamond-like carbon (DLC). It is only covered with a thin protective layer having a thickness of 20 to 50 mm, and is an open end.

  Therefore, as a result of the stress from the lower gap layer 20 and the upper gap layer 30 that was originally two-dimensional isotropic being released at the end face F, the symmetry is broken, and the multilayer film T1 has a height direction (not shown). A tensile stress is applied in a direction parallel to the (Y direction). Further, when the laminated film of the bias underlayers 27 and 27, the hard bias layers 28 and 28, and the electrode layers 29 and 29 has compressive internal stress, the electrode layer and the like may extend in the in-plane direction. Therefore, a compressive stress is applied to the multilayer film T1 in a direction parallel to the track width direction (X direction in the drawing) and in an antiparallel direction.

  That is, tensile stress in the height direction and compressive stress in the track width direction are applied to the pinned magnetic layer 23 whose end face F on the side facing the recording medium is open. Since the first magnetic layer 23a is made of a magnetic material having a positive magnetostriction constant, the easy axis of magnetization of the first magnetic layer 23a is located on the back side (height direction) of the magnetic detection element due to the magnetoelastic effect. The direction of magnetization of the first magnetic layer 23a is fixed in the direction parallel to the height direction or in the antiparallel direction. The magnetization of the second magnetic layer 23c is fixed in a state in which the magnetization direction of the second magnetic layer 23c is antiparallel to the magnetization direction of the first magnetic layer 23a by the RKKY interaction via the nonmagnetic intermediate layer 23b.

  In the present invention, the magnetoelastic energy is increased by increasing the magnetostriction constant of the pinned magnetic layer 23, thereby increasing the uniaxial anisotropy of the pinned magnetic layer 23. When the uniaxial anisotropy of the pinned magnetic layer 23 increases, the magnetization of the pinned magnetic layer 23 is firmly fixed in a certain direction, the output of the magnetic detection element increases, and the stability and symmetry of the output also improve. Further, for example, it is possible to provide a magnetic detection element that hardly causes magnetization reversal even when a transient current due to electrostatic discharge (ESD) flows.

  In the present invention, as a first feature point, the material of the nonmagnetic metal layer 22 in contact with the first magnetic layer 23a constituting the pinned magnetic layer 23 is optimized as described above, so that the crystal structure of the first magnetic layer 23a is obtained. Distortion is caused to increase the magnetostriction constant λ of the first magnetic layer 23a.

  The atoms constituting the first magnetic layer 23a and the atoms constituting the nonmagnetic metal layer 22 are likely to overlap each other, and at least some of the crystals in the nonmagnetic metal layer 22 and the crystals in the pinned magnetic layer 23 are It is in an epitaxial or heteroepitaxial state.

  In order to increase the magnetostriction of the first magnetic layer 23a in order to cause distortion in the crystal structure while overlapping the atoms constituting the nonmagnetic metal layer 22 and the atoms of the first magnetic layer 23a, It is preferable to adjust the content of the X element in the X—Mn alloy as the material.

  For example, when the content of the X element in the X—Mn alloy (where X is one or more of Pt, Pd, Os, Ni, Fe) is 51 atomic% or more, the nonmagnetic metal The magnetostriction of the first magnetic layer 23a overlapping the layer 22 increases rapidly. In addition, the content of the X element in the X—Mn alloy (where X is one or more of Pt, Pd, Os, Ni, and Fe) is 45 atomic% to 99 atomic%. And the magnetostriction of the first magnetic layer takes a large value. Furthermore, the content of the X element in the X—Mn alloy (where X is one or more of Pt, Pd, Os, Ni, and Fe) is 55 atomic% or more and 99 atomic% or less. The magnetostriction of the first magnetic layer is stabilized while taking a large value.

  In the present invention, the X element content in the X—Mn alloy (where X is one or more of Ir, Rh, and Ru) is 17 atomic% or more and 99 atomic% or less. Is preferred.

Furthermore, the content of Ir in the Ir—Mn alloy is preferably 20 atomic% or more and 99 atomic% or less.
Thereby, the magnetostriction of the first magnetic layer 23a can be increased more appropriately.

  As a second feature of the present invention, the first magnetic layer 23a is formed of a magnetic material mainly composed of Co and Fe and further added with a rare earth element or a noble metal element.

  The material used for the first magnetic layer 23a is positive magnetostriction, and the RKKY interaction generated with the second magnetic layer 23c is increased, so that the first magnetic layer 23a and the second magnetic layer 23c are appropriately selected. It is necessary that the magnetization can be fixed in anti-parallel to that, and that the crystal orientation of the multilayer film T1 can be maintained well.

  CoFe alloys and Co that have been generally used as the first magnetic layer 23a hitherto satisfy the above requirements, but satisfy the above requirements, and the magnetostriction constant λs of the first magnetic layer 23a is set to CoFe. As a material that can be made larger than when an alloy or Co is used, the present invention provides a magnetic material mainly composed of Co and Fe, and further added with a rare earth element or a noble metal element.

In the present invention, the rare earth element is preferably selected from at least one of Tb, Sm, Pr, Y, Ce, Nd, Gd, Dy, Ho, Er, and Yb. In such a case, the first magnetic layer 23a _{is, (Co x Fe 1-x} ) formed of a magnetic material represented by _{100-y M y,} element M, Tb, Sm, Pr, Y , Ce, Nd, Gd , Dy, Ho, Er, Yb are selected, and the composition ratio y is preferably 0.3 at% or more and 5 at% or less.

  According to the experimental results described later, the magnetostriction enhancing effect of the first magnetic layer 23a was appropriately obtained by setting the composition ratio y of the element M in the range of 0.3 at% to 5 at%. In the present invention, by setting the composition ratio of the element M to 4 at% or less, it was possible to reliably obtain a magnetostriction constant having a higher value than the magnetostriction constant of the magnetic material when the element M was not added.

In the present invention, the noble metal element is preferably selected from at least one of Pt, Rh, Ir, and Re. In this case, the first magnetic layer 23a is formed of a magnetic material represented by (Co _x Fe _1-x ) _100-z N _z , and the element N is at least one of Pt, Rh, Ir, and Re. The type is selected, and the composition ratio z is preferably 5 at% or more and 20 at% or less.

  According to the experimental results described later, the magnetostriction enhancing effect of the first magnetic layer 23a was appropriately obtained by setting the composition ratio z of the element N in the range of 5 at% to 20 at%. In the present invention, by setting the composition ratio of the element N to 16 at% or less, a magnetostriction constant having a value higher than the magnetostriction constant of the magnetic material when the element N is not added can be surely obtained.

  Further, in CoFe—Pt or Co—Pt in which Pt of the element N is selected, the coercive force enhancement effect of the first magnetic layer 23a appears significantly when the composition ratio of Pt is 10 at% or more.

  When Ir was selected as the element N, a very high magnetostriction constant was obtained as compared with CoFe and Co to which the element N was not added, and the coercive force Hc was stably obtained at a high value.

  In the present invention, the atomic ratio x is preferably 1 or in the range of 0.4 to 0.6. Accordingly, the coercive force Hc of the first magnetic layer 23a can be increased. Further, the RKKY interaction generated with the second magnetic layer 23c can be increased, and the first magnetic layer 23a and the second magnetic layer 23c can be appropriately pinned in an antiparallel state. Also, the crystal orientation of the first magnetic layer 23a can be improved. In the present invention, the first magnetic layer 23a has a face-centered cubic lattice (fcc) structure or a body-centered cubic lattice (bcc) structure in the vicinity of the interface on the nonmagnetic metal layer side or in the entire region, and is parallel to the interface. It is preferable that an equivalent crystal plane represented as {111} plane or {110} plane is preferentially oriented in the direction.

  In the present invention, the thickness of the first magnetic layer 23a is preferably in the range of 12 to 19 mm. If the film thickness of the first magnetic layer 23a is too large, the strain generated in the first magnetic layer 23a is reduced, and the magnetostriction constant λ and uniaxial anisotropy are also reduced.

The combined magnetic moment (Net Mst) per unit area of the first magnetic layer 23a and the second magnetic layer 23c constituting the pinned magnetic layer 23 is 0.07 (memu / cm ² ) = {0.32π ( T · nm)} to 0.13 (memu / cm ² ) = {0.52 (T · nm)}. As a result, it is possible to obtain a resistance change rate (ΔR / R) comparable to that in the case where the first magnetic layer 23a is conventionally formed of Co or a CoFe alloy.

When forming the first magnetic layer 23a of a magnetic material represented by the above _{(Co x Fe 1-x)} 100-y M y, or _{(Co x Fe 1-x)} 100-z N z, wherein the first magnetic the magnetostriction constant λs layer 23a, can be larger than that of CoFe alloy or Co _{are, (Co x Fe 1-x} ) 100-y M y, or _{(Co x Fe 1-x)} 100-z N z This is probably because the magnetic material represented by the formula has a larger lattice constant than the CoFe alloy and Co.

  In the magnetic sensing element of the present embodiment, as schematically shown in FIG. 3, the atoms constituting the nonmagnetic metal layer 22 and the atoms of the first magnetic layer 23a overlap, but the crystal structure is distorted near the interface. Will occur.

  In FIG. 3, the symbol N1 indicates the nearest interatomic distance in the {111} plane of the first magnetic layer 23a, and the symbol N2 indicates the nearest interatomic distance in the {111} plane of the nonmagnetic metal layer 22. ing. N1 and N2 are measured where there is little influence of strain away from the interface between the nonmagnetic metal layer 22 and the first magnetic layer 23a. As shown in FIG. 3, the closest interatomic distance N1 in the {111} plane of the first magnetic layer 23a is smaller than the closest interatomic distance N2 in the {111} plane of the nonmagnetic metal layer 22.

  As described above, when distortion occurs in the crystal structure of the first magnetic layer 23a, the magnetostriction constant λ of the first magnetic layer 23a can be increased, so that a large magnetoelastic effect can be exhibited.

As described above, the first magnetic layer _{23a (Co x Fe 1-x} ) 100-y M y, or when _{(Co x Fe 1-x)} 100-z N to a magnetic material represented by _z, the grating Since the constant can be made larger than that of CoFe alloy or Co, the nearest interatomic distance N1 in the {111} plane of the first magnetic layer 23a is larger than when the first magnetic layer 23a is made of CoFe alloy or Co. spread.

  As a result, at the interface between the first magnetic layer 23a and the nonmagnetic metal layer 22, the atoms constituting the first magnetic layer 23a and the atoms constituting the nonmagnetic metal layer 22 are likely to overlap each other effectively. A large strain can be generated in the crystal structure near the interface of the first magnetic layer 23a, and the magnetostriction constant λs of the first magnetic layer 23a can be increased.

On the other hand, when the first magnetic layer 23a is formed of a CoFe alloy or Co, the overlap between atoms at the interface between the first magnetic layer 23a and the nonmagnetic metal layer 22 is reduced. The crystal structure in the vicinity of the interface of the first magnetic layer 23a cannot be strained, and the magnetostriction constant λs of the first magnetic layer 23a is the same as that described above for the first magnetic layer 23a (Co _x Fe _1-x ) _{100-y M} y, or _(tends to be smaller as compared with the case of forming a magnetic material represented by _{Co x Fe 1-x) 100} -z N z.

  In the present invention, in the vicinity of the interface between the first magnetic layer 23 a and the nonmagnetic metal layer 22, the atoms constituting the first magnetic layer 23 a and the majority of the atoms constituting the nonmagnetic metal layer 22 overlap each other. It only has to be. For example, as schematically shown in FIG. 3, there may be a region where atoms constituting the first magnetic layer 23 a and atoms constituting the nonmagnetic metal layer 22 do not overlap.

  In the present invention, the mismatch value between the nonmagnetic metal layer 22 and the first magnetic layer 23a is preferably 0.1 or more and 0.2 or less. Here, the “mismatch value” refers to the closest interatomic distance in the {111} plane of the nonmagnetic metal layer 22 and the closest interatomic distance in the {111} plane of the first magnetic layer 23a of the pinned magnetic layer 23. Is divided by the distance between the nearest atoms in the {111} plane of the first magnetic layer 23a.

  Although it has been described above that the crystal structure of the first magnetic layer 23a preferably has an fcc structure, the first magnetic layer 23a has a body-centered cubic (bcc) structure and is parallel to the interface. In addition, an equivalent crystal plane represented as a {110} plane may be preferentially oriented.

  As described above, the nonmagnetic metal layer 22 has an fcc structure, and an equivalent crystal plane represented as a {111} plane is preferentially oriented in a direction parallel to the interface.

  The atomic arrangement of the equivalent crystal plane represented as the {110} plane of the crystal having the bcc structure is similar to the atomic arrangement of the equivalent crystal plane represented as the {111} plane of the crystal having the fcc structure, and bcc At least part of the crystal having the structure and the crystal having the fcc structure can be brought into a matching state in which the atoms overlap each other, that is, a so-called heteroepitaxial state.

The material of the second magnetic layer 23c includes Co _l Fe _m having a bcc structure (m ≧ 20 at%, l + m = 100 at%), Co having a fcc structure or Co _n Fe _o (o ≦ 20 at%, n + o = Either 100 at%) may be used.

When Co ₁ Fe _m (m ≧ 20 at%, l + m = 100 at%) having a bcc structure is used as the material of the second magnetic layer 23c, the positive magnetostriction can be increased. Co _n Fe _o (o ≧ 20, n + o = 100) having a bcc structure has a large coercive force and can strengthen the magnetization pinning of the pinned magnetic layer 23. Further, the RKKY interaction between the first magnetic layer 23a and the second magnetic layer 23c via the nonmagnetic intermediate layer 23b is strengthened.

On the other hand, the second magnetic layer 23c is in contact with the nonmagnetic material layer 24 and has a great influence on the magnetoresistive effect. Therefore, Co or Co _l Fe _m (m ≦ 20, l + m = 100) having an fcc structure is used. When formed, there is little deterioration of the magnetoresistive effect.

FIG. 4 is a partial cross-sectional view showing another aspect of the pinned magnetic layer 23.
As shown in FIG. 4, the first magnetic layer 23a constituting the pinned magnetic layer 23 is formed in a two-layer structure, the nonmagnetic metal layer side magnetic layer 23a1 is provided on the nonmagnetic metal layer 22 side, and the nonmagnetic intermediate layer 23a1 is provided. A nonmagnetic intermediate layer-side magnetic layer 23a2 is formed on the layer 23b side.

In this embodiment, the non-magnetic metal layer-side magnetic layer 23a1, the magnetic represented by the above _{(Co x Fe 1-x)} 100-y M y, or _{(Co x Fe 1-x)} 100-z N z It is preferable that it is made of a material. As a result, the magnetostriction constant λs of the first magnetic layer 23a can be increased.

On the other hand, the nonmagnetic intermediate layer-side magnetic layer 23a2 is preferably formed of a CoFe alloy or Co. The nonmagnetic intermediate layer-side magnetic layer 23a2 is formed of Co or Co _w Fe _100-w (wherein the composition ratio w is 40 to 60 at%), whereby the first magnetic layer 23a via the nonmagnetic intermediate layer 23b and The RKKY interaction between the second magnetic layers 23c can be strengthened. As a result, GMR characteristics can be improved.

The first magnetic layer 23a may have a laminated structure of three or more layers. Even in such a case, the magnetic layer in contact with the nonmagnetic metal layer 22 is (Co _x Fe _1-x ) _{100- y My} Or a magnetic layer formed of a magnetic material represented by (Co _x Fe _1-x ) _100-z N _z and further in contact with the nonmagnetic intermediate layer 23b is made of Co or Co _w Fe _100-w (where the composition ratio w Is preferably formed at 40 to 60 at%).

  FIG. 5 is a cross-sectional view of the magnetic detection element according to the second embodiment of the present invention as viewed from the side facing the recording medium.

  The magnetic detection element shown in FIG. 5 is similar to the magnetic detection element shown in FIG. 1, and is different from the magnetic detection element shown in FIG. 1 in that a multilayer film T2 is formed instead of the multilayer film T1. It is different from the detection element. The multilayer film T2 includes, in order from the bottom, the seed layer 21, the free magnetic layer 25, the nonmagnetic material layer 24, the second magnetic layer 23c, the nonmagnetic intermediate layer 23b, the fixed magnetic layer 23 including the first magnetic layer 23a, and a nonmagnetic metal. The layer 22 and the protective layer 26 are laminated. That is, the multilayer film T2 is obtained by reversing the stacking order of the layers of the multilayer film T1.

  Also in the magnetic detection element of the present embodiment, the first magnetic layer 23 a of the pinned magnetic layer 23 is in contact with the nonmagnetic metal layer 22.

  Also in this embodiment, the crystal structure of the nonmagnetic metal layer 22 continues to maintain the face-centered cubic lattice (fcc) structure that is the state at the time of film formation.

The first magnetic layer 23a is formed of a magnetic material represented by the above _{(Co x Fe 1-x)} 100-y M y, or _{(Co x Fe 1-x)} 100-z N z.

  In the embodiment shown in FIG. 5, the same phenomenon as described in FIG. 3 occurs. That is, the atoms constituting the nonmagnetic metal layer 22 and the atoms constituting the first magnetic layer 23a of the pinned magnetic layer 23 are overlapped with each other but are distorted at the interface of the first magnetic layer 23a. At least part of the crystals in the layer 22 and the crystals in the first magnetic layer 23a are in an epitaxial or heteroepitaxial state. As a result, the magnetostriction constant λs of the first magnetic layer 23a can be effectively increased.

  Further, as in the embodiment shown in FIG. 5, in the configuration in which the free magnetic layer 25, the nonmagnetic material layer 24, and the pinned magnetic layer 23 are sequentially laminated from the bottom, the crystal orientation of the multilayer film T2 can be easily maintained. . High orientation is an important factor in securing a high rate of change in resistance (ΔR / R) in the magnetic sensing element.

  In the configuration of FIG. 1, a large number of layers are stacked below the free magnetic layer 25. For example, all of these layers are equivalent crystal planes represented as {111} planes or crystals similar to {111} planes. The plane (for example, the {110} plane) is only required to be preferentially oriented, but if any of these layers has a low orientation that disturbs the crystal orientation, the crystal orientation of the free magnetic layer 25 As a result, the rate of change in resistance (ΔR / R) decreases.

  On the other hand, in the configuration of FIG. 5, the free magnetic layer 25 and the second magnetic layer 23c that contribute to the magnetoresistive effect are formed below the multilayer film T2. 1 is smaller than that of FIG. 1, and as a result, the resistance change rate (ΔR / R) is easily improved as compared with the embodiment of FIG.

  In particular, in the present invention, rare earth elements or noble metal elements are added to the first magnetic layer 23a, but the crystal orientation tends to be deteriorated as compared with the case where these elements are not added. Therefore, as shown in FIG. 5, it is preferable that the second magnetic layer 23c and the free magnetic layer 25 are provided below the first magnetic layer 23a.

  FIG. 6 is a cross-sectional view of the magnetic detection element according to the third embodiment of the present invention as viewed from the side facing the recording medium.

  6 has a multilayer film T3 similar to FIG. 1, and unlike FIG. 1, the coercive force Hc of the pinned magnetic layer 23 is increased between the pinned magnetic layer 23 and the nonmagnetic metal layer 22. FIG. A nonmagnetic layer 32 is formed. The nonmagnetic layer 32 is preferably formed in contact with the pinned magnetic layer 23. The nonmagnetic layer 32 is a layer provided to increase the coercive force Hc of the pinned magnetic layer 23. By forming the nonmagnetic layer 32 and the pinned magnetic layer 23 in contact with each other, the coercive force Hc of the pinned magnetic layer 23 can be increased more effectively.

The nonmagnetic layer 32 is specifically Cu _{or, (Ni u Fe 1-u} ) 100-v Cr v ( however, u is 0-1 in atomic ratio, v is 18～50At%, or 90~100at %). The composition range of u and v of the (Ni _u Fe _1-u ) _100-v Cr _{v is} a range having non-magnetic properties.

Even more preferably, u is in the range of 0.7 to 1, and v is in the range of 22 to 45 at%. Within this range, the coercive force Hc of the pinned magnetic layer 23 can be increased more effectively.
The thickness of the nonmagnetic layer 32 is preferably 3 mm or more and 10 mm or less.

In the embodiment shown in FIG. 6, the nonmagnetic metal layer 22 / nonmagnetic layer 32 / pinned magnetic layer 23 are stacked in this order, so that not only the magnetostriction constant of the pinned magnetic layer 23 but also the coercive force Hc is obtained. Can be bigger. Since the nonmagnetic metal layer 22 is not provided directly under the pinned magnetic layer 23, the distortion of the crystal structure at the interface of the first magnetic layer 23a described with reference to FIG. Thus, it is predicted that the magnetostriction constant λs of the pinned magnetic layer 23 cannot be increased. However, in the configuration of FIG. 6, the above-described (Co _x Fe ₁₋ because using _{x) 100-y M} y, or _{(Co x} Fe _1-x) magnetic material represented by _{100-z N} z, in the case of using Co or CoFe alloy in said first magnetic layer 23a In comparison, the magnetostriction constant of the first magnetic layer 23a can be increased, and the coercive force Hc of the first magnetic layer 23a can also be increased. Even when an excessive stress (mechanical stress) is applied, for example, when the magnetic detection element collides with a protrusion on the medium while it is floating, the magnetization reversal of the pinned magnetic layer 23 can be appropriately suppressed. .

  1, 5 and 6, in order to increase the anisotropy based on the magnetoelastic effect of the pinned magnetic layer 23, the bias underlayers 27, 27, It is preferable to increase the compressive stress applied from the hard bias layers 28 and 28 and the electrode layers 29 and 29 in the direction parallel to the track width direction (the X direction in the drawing) and the antiparallel direction.

  For example, when the electrode layers 29 and 29 are made of Cr (chromium), α-Ta, or Rh, and the plane spacing in the film plane parallel direction of the crystal lattice plane of the electrode layers 29 and 29 is Cr, 0.2044 nm or more. (Bcc structure {110} face spacing), α-Ta, 0.2337 nm or more (bcc structure {110} face spacing), Rh, 0.2200 nm or more (fcc structure {111} face spacing) If so, the compressive stress applied to the multilayer films T1, T2 and T3 can be increased. At this time, the electrode layers 29, 29 extend in the direction of the arrow shown in FIG. 2, that is, toward the outer side of the electrode layers 29, 29, and in the track width direction (shown as X in the figure) with respect to the multilayer films T1, T2, T3. Compressive stress is applied in a direction parallel to (direction) and in an antiparallel direction.

  The interplanar spacing of the crystal lattice planes of the electrode layers 29 and 29 can be measured by X-ray diffraction or electron beam diffraction. In addition, Cr, α-Ta, or Rh in the bulk state is 0.2040 nm (a {110} plane spacing of the bcc structure) when the plane spacing of the crystal lattice plane in the film plane direction is Cr, and α-Ta. 0.2332 nm (buck structure {110} face spacing), and Rh is 0.2196 nm (fcc structure {111} face spacing). When the face spacing exceeds this value, the electrode layers 29 and 29 It acts to give a compressive stress to the multilayer films T1, T2, and T3.

  When the electrode layers 29 and 29 are made of Cr and when they are made of a soft metal material such as Au, the following differences occur in the compressive stress.

  For example, in order from the bottom, a bias underlayer: Cr (50Å) / hard bias layer: CoPt (200Å) / intermediate layer: Ta (50Å) / electrode layer: Au (800Å) / protective layer: Ta (50Å) are laminated. The compressive stress generated by the film is 280 MPa.

  On the other hand, in order from the bottom, bias underlayer: Cr (50Å) / hard bias layer: CoPt (200Å) / intermediate layer: Ta (50Å) / electrode layer: Cr (1400Å) / protective layer: Ta (50Å) The compressive stress generated by the laminated film is 670 MPa.

  The intermediate layer Ta (50Å) and the protective layer Ta (50Å) are not shown in FIGS. 1, T5, and 6, but function as a layer for adjusting the crystal orientation of the electrode layer and an antioxidant layer, respectively.

When the electrode layers 29 and 29 are formed by sputtering, ion beam sputtering is used, and the pressure of Ar, Xe, Kr, etc. in the sputtering apparatus is as small as 5 × 10 ⁻³ to 1 × 10 ⁻¹ (Pa). To do. When the pressure of Ar, Xe, Kr, etc. in the sputtering apparatus is small, the probability that Cr, Ta, Rh atoms forming the electrode layer collide with Ar atoms decreases, so that atoms such as Cr retain high energy. Accumulate. When Cr atoms, such as flying from the target, collide with large energy and are embedded in a film such as Cr that has already been formed, the electrode layers 29 and 29 extend outward.

  The magnetization direction of both ends of the pinned magnetic layer 23 in the track width direction is easily inclined by the longitudinal bias magnetic field generated by the hard bias layers 28 and 28. However, a large compressive stress is applied to both ends of the pinned magnetic layer 23 in the track width direction. Therefore, both ends of the pinned magnetic layer 23 in the track width direction have a large anisotropy due to the magnetoelastic effect, and the magnetization direction is strongly fixed in one direction.

  The present invention fixes the magnetization direction of the pinned magnetic layer 23 by uniaxial anisotropy based on the relationship between the compressive stress and magnetostriction from both sides of the pinned magnetic layer 23, and the compressive stress applied to the pinned magnetic layer is fixed. Strong at both ends of the magnetic layer 23 in the optical track width direction and weak at the center. Therefore, when the width dimension of the pinned magnetic layer 23 in the optical track width direction is large, the magnetization direction pinning force near the center of the pinned magnetic layer 23 is reduced. Therefore, the optical track width dimension W1 of the pinned magnetic layer 23 is preferably 0.15 μm or less.

  The magnetostriction of the free magnetic layer 25 is preferably negative magnetostriction. As described above, since the multilayer films T1, T2, and T3 of the magnetic detection element are subjected to compressive stress from both sides, the free magnetic layer 25 having negative magnetostriction has a track width direction (X direction in the drawing) due to the magnetoelastic effect. The direction parallel or antiparallel to the axis tends to be the easy axis of magnetization.

  The magnetization at both ends of the free magnetic layer 25 in the track width direction tends to be unstable due to the demagnetizing field. However, both ends of the free magnetic layer 25 in the track width direction are close to the hard bias layers 28 and 28, and a large compressive stress is applied. Accordingly, both ends of the free magnetic layer 25 in the track width direction are more anisotropic due to the magnetoelastic effect, and the magnetization direction is stabilized.

  Therefore, the free magnetic layer 25 can be brought into a stable single domain state even if the film thickness of the hard bias layers 28 is reduced and the longitudinal bias magnetic field is reduced. If the thickness of the hard bias layers 28 and 28 is reduced to reduce the longitudinal bias magnetic field, the fixed magnetization state in the height direction of the fixed magnetic layer 23 can be stabilized.

  Since the compressive stress near the center of the free magnetic layer 25 is smaller than the compressive stress at both ends, it is possible to suppress a decrease in magnetic field detection sensitivity.

The magnetostriction constant λ of the free magnetic layer 25 is preferably in the range of −8 × 10 ⁻⁶ ≦ λ ≦ −0.5 × 10 ⁻⁶ . The film thickness t of the hard bias layers 28, 28 is preferably 100Å ≦ t ≦ 200Å. If the magnetostriction λ of the free magnetic layer 25 is too small, or if the film thickness t of the hard bias layers 28 and 28 is too thick, the reproduction sensitivity of the magnetic detection element decreases. On the other hand, if the magnetostriction λ of the free magnetic layer 25 is too large, or if the film thickness t of the hard bias layers 28 and 28 is too thin, the reproduction waveform of the magnetic detection element is likely to be disturbed.

  The magnetic sensing element of the present embodiment shown in FIGS. 1, 5, and 6 is manufactured by forming a thin film by sputtering or vapor deposition and patterning by resist photolithography. Sputtering and resist photolithography use methods that are usually used when forming a magnetic sensing element.

  In the present embodiment, a laminate of hard bias layers 28 and 28 and electrode layers 29 and 29 is formed on both sides of the multilayer films T1, T2 and T3, and the laminate is compressed into the multilayer films T1, T2 and T3. Stress is applied. However, the hard bias layers 28 may not be provided on both sides of the multilayer films T1, T2, and T3. For example, a laminate of a soft magnetic material layer and an antiferromagnetic layer may be provided on both sides of the multilayer films T1, T2, and T3, and both sides of the multilayer films T1, T2, and T3 are insulating layers. May be.

  The present invention may be used for a tunnel type magnetoresistive effect element or a CPP-GMR type magnetic sensing element in which a sense current flows in the direction perpendicular to the film thickness of the multilayer films T1, T2, T3. In this case, the electrode layers are respectively formed above and below the multilayer films T1, T2, and T3.

  Although the present invention has been described with reference to preferred embodiments thereof, various modifications can be made without departing from the scope of the present invention.

  The above-described embodiment is merely an example, and does not limit the scope of the claims of the present invention.

A sample having the following film configuration was formed.
(Membrane structure)
Seed layer; (Ni _0.8 Fe _0.2 ) ₆₀ Cr ₄₀ (52) / nonmagnetic metal layer; Pt _{50 at%} Mn _{50 at%} (30) / first magnetic layer (50) / Ru (9.1) / Cu (65) / Ta (30)
The brackets indicate the film thickness and the unit is 単 位.

  Using each sample in which the first magnetic layer was formed of Tb—Co, Pr—Co, and Sm—Co, the relationship between the composition ratio of Tb, Pr, and Sm and the magnetostriction constant λs of the first magnetic layer was examined. The magnetostriction constant λs was measured by an optical lever method. The experimental result is shown in FIG.

  In all of Tb—Co, Pr—Co, and Sm—Co, the magnetostriction constant λs of the first magnetic layer was maximized when the composition ratio of Tb, Pr, and Sm was about 1 (at%). As the composition ratio of Tb, Pr, and Sm is increased from 1 (at%), the magnetostriction constant λs of the first magnetic layer gradually decreases, and the composition ratio of Tb, Pr, and Sm is 5 at. %, The magnetostriction constant of the first magnetic layer is less than 50 (ppm), and the magnetostriction constant λs when Co is used as the magnetic material when Tb, Pr and Sm are not added, that is, Co is used as the first magnetic layer. It was found that only a small magnetostriction constant can be obtained. It was also found that the composition ratio of Tb, Pr, and Sm is preferably 4 at% or less in order to obtain a magnetostriction constant that is surely larger than the magnetostriction constant λs when Co is used as the first magnetic layer.

  It was also found that when the composition ratio of Tb, Pr and Sm is 0.3 at% or more, a magnetostriction constant larger than the magnetostriction constant λs when Co is used as the first magnetic layer can be obtained.

Next, a sample having the following film configuration was formed.
Seed layer; (Ni _0.8 Fe _0.2 ) ₆₀ Cr ₄₀ (52) / nonmagnetic metal layer; Pt _{50 at%} Mn _{50 at%} (30) / first magnetic layer / Ru (9.1) / second magnetic Layer: Co (20) / Cu (18) / free magnetic layer; [CoFe (10) / NiFe (28 or 32)] / Ta (30)
The brackets indicate the film thickness and the unit is 単 位.

  As shown in Table 1, spin flop magnetic field (Hsf) and resistance were measured using samples in which the first magnetic layer (pin1) was formed of Tb-Co, Pr-Co, Sm-Co, and Co and the film thickness was varied. The relationship with the rate of change (ΔR / R) was examined.

  The composition ratio of the first magnetic layer and the thickness of the free magnetic layer in each sample are as described in Table 1 and FIG.

  Here, the spin flop magnetic field Hsf means the magnitude of the magnetic field when the antiparallel magnetization state of the first magnetic layer and the second magnetic layer collapses. The larger the spin flop magnetic field, the more appropriately the first magnetic layer and the second magnetic layer maintain an antiparallel magnetization state.

  As shown in FIG. 8, the spin flop magnetic field (Hsf) of each sample in which the first magnetic layer is formed of Tb—Co, Pr—Co, and Sm—Co is the same as the case where the first magnetic layer is formed of Co. Takes a value that does not change much.

  However, the rate of change in resistance (ΔR / R) is larger when the first magnetic layer is made of Co than when the first magnetic layer is made of Tb—Co, Pr—Co, or Sm—Co. I understood.

However, if the spin flop magnetic field (Hsf) is increased in each sample in which the first magnetic layer is formed of Tb—Co, Pr—Co, and Sm—Co, ΔR / R tends to increase, and the spin flop increases. If the magnetic field is 2000 (Oe) (= about 15.8 × 10 ⁴ (A / m)) or more, ΔR / R can be increased to 12% or more, and ΔR / R of the sample using Co for the first magnetic layer can be increased. You can get closer.

  From the experimental results shown in FIG. 7, when adding rare earth elements to the first magnetic layer, it was derived that the addition amount is preferably 0.3 (at%) or more and 5 (at%) or less.

Next, a sample having the following film configuration was formed.
Seed layer; (Ni _0.8 Fe _0.2 ) ₆₀ Cr ₄₀ (52) / nonmagnetic metal layer; Pt _{50 at%} Mn _{50 at%} (when the first magnetic layer is Ir—Co, Rh—Co, 10 μm, Pt— Co) 30) / first magnetic layer (50 と き for Ir-Co, Rh-Co, 20 Å, 22.4 Å, 24 か ら) from the smallest Pt composition ratio for Pt-Co) / Ru (9.1)
The brackets indicate the film thickness and the unit is 単 位.

  Using each sample in which the first magnetic layer was formed of Ir—Co, Rh—Co, and Pt—Co, the relationship between the composition ratio of Ir, Rh, and Pt and the coercive force Hc of the first magnetic layer was examined. The experimental result is shown in FIG.

  As shown in FIG. 9, when Rh—Co is used for the first magnetic layer, the coercive force Hc is not so different from that when Co is used for the first magnetic layer. On the other hand, when Ir—Co was used for the first magnetic layer, the coercive force Hc of the first magnetic layer could be increased compared to the case where Co was used for the first magnetic layer.

  Further, when Pt—Co is used for the first magnetic layer, the coercive force Hc of the first magnetic layer can be increased compared to the case where Co is used for the first magnetic layer, and in particular, the composition ratio of Pt. When the content was 10 at% or more, the effect of enhancing the coercive force Hc was remarkably obtained.

  FIG. 10 is a graph obtained by measuring the relationship between the composition ratio of Ir and Rh and the magnetostriction constant of the first magnetic layer using the same sample as that used in the experiment of FIG. The magnetostriction constant was measured by the optical lever method.

  As shown in FIG. 10, when the composition ratio of Ir and Rh is increased, the magnetostriction constant of the first magnetic layer increases up to about 6 to 8 (at%), and the composition ratio of Ir and Rh is about It has been found that the magnetostriction constant of the first magnetic layer gradually decreases as it becomes larger than 8 (at%).

Next, a sample having the following film configuration was formed.
Seed layer; (Ni _0.8 Fe _0.2 ) ₆₀ Cr ₄₀ (52) / nonmagnetic metal layer; Pt _{50 at%} Mn _{50 at%} (30) / first magnetic layer; Pt—Co (when Pt is 0 at%) , 20 Å, when Pt is 10.7at% 22.4Å, when Pt is 16.7at% 24Å) / Ru (8.7 ) / the second magnetic layer; Co (40) / Cu ( 21) / Co 90 Fe ₁₀ (14) / Ru (9) / Co ₉₀ Fe ₁₀ (14) / PtMn (140) / Ta (30)
The brackets indicate the film thickness and the unit is 単 位.

  Magnetostriction of a pinned magnetic layer having a synthetic ferri-pinned structure of the first magnetic layer / Ru / second magnetic layer when the above-described sample is used and the composition ratio of Pt of Pt—Co constituting the first magnetic layer is changed. A constant λs was determined. The magnetostriction constant was measured by a bending method. The bending method is a method of measuring a magnetostriction constant from a change in uniaxial anisotropy due to an inverse magnetostriction effect by bending a sample having the above-described film configuration to give a uniaxial strain. The experimental results are shown in FIG.

  As shown in FIG. 11, as the Pt composition ratio of Pt—Co constituting the first magnetic layer is increased to about 10 at%, the magnetostriction constant λs of the pinned magnetic layer gradually increases accordingly. As the Pt composition ratio of Pt—Co constituting the first magnetic layer was increased from about 10 at%, the magnetostriction constant λs of the pinned magnetic layer gradually decreased.

  From the experimental results shown in FIGS. 9 to 11, it was derived that when the noble metal element is added to the first magnetic layer, the addition amount is preferably 5 (at%) or more and 20 (at%) or less. When the addition amount is 5 (at%) or more, the coercive force Hc can be increased together with the magnetostriction constant. On the other hand, when the addition amount is larger than 20 (at%), the magnetostriction constant λs is larger than that in the case where Ir, Rh, Pt is not added, that is, when Co is used as the first magnetic layer. Therefore, the upper limit of the addition amount was set to 20 (at%). More preferably, if the upper limit of the addition amount is 16 at% or less, the magnetostriction constant λs can be reliably increased as compared with the case where the magnetic material without adding Ir, Rh, Pt is used as the first magnetic layer. I understood it.

  From the experimental results shown in FIG. 9 to FIG. 11, the magnetostriction constant of the first magnetic layer is set to a value much larger than that of the magnetic material (Co or CoFe) not added with the noble metal element. Ir—Co is preferably used, and the magnetostriction constant is not greatly affected by the amount of the noble metal element added, and the magnetostriction constant is made large and stable as compared with a magnetic material (Co or CoFe) to which no noble metal element is added. It was found that it is preferable to use Pt—Co for the first magnetic layer.

  It has also been found that if Ir—Co or Pt—Co is used for the first magnetic layer, the coercivity of the first magnetic layer can be improved appropriately.

Next, a sample having the following film configuration was formed.
Seed layer; (Ni _0.8 Fe _0.2 ) ₆₀ Cr ₄₀ (52) / nonmagnetic metal layer; Pt _{50 at%} Mn _{50 at%} (10) / first magnetic layer / Ru (9.1) / second magnetic Layer: Co (20) / Cu (18) / free magnetic layer; [CoFe (10) / NiFe (32)] / Ta (30)
The brackets indicate the film thickness and the unit is 単 位.

  In the experiment, the composite magnetic moment (net-Ms · t) per unit area of the first magnetic layer and the second magnetic layer was changed by changing the film thickness of the first magnetic layer (pin1) shown in Table 2. The relationship between net-Ms · t and the rate of resistance change (ΔR / R) was examined. The material and composition ratio of the first magnetic layer in each sample are as shown in Table 2 and FIG.

  As shown in FIG. 12, it was found that as net-Ms · t increases, ΔR / R increases accordingly.

  As shown in FIG. 12, when Rh—Co is used for the first magnetic layer, ΔR / R is obtained even when the same net-Ms · t is obtained as compared with the case where Co is used for the first magnetic layer. However, when Ir-Co is used for the first magnetic layer, when the same net-Ms · t is obtained as compared with the case where Co is used for the first magnetic layer, It was found that the same or high ΔR / R can be obtained.

For this reason, it was found that it is preferable to use Ir—Co for the first magnetic layer from the viewpoint of improving ΔR / R. Even when Rh—Co is used for the first magnetic layer, if the net-Ms · t is 0.07 (memu / cm ² ) (= 0.28π (T · nm)) or more, the first magnetic layer It can be seen that ΔR / R comparable to ΔR / R when net-Ms · t is 0.05 (memu / cm ² ) (= 0.20π (T · nm)) using Co for It was.

Next, a sample having the following film configuration was formed.
(Membrane structure)
Seed layer; (Ni _0.8 Fe _0.2 ) ₆₀ Cr ₄₀ (52) / nonmagnetic metal layer; Pt _{50 at%} Mn _{50 at%} (30) / first magnetic layer; CoFe (15-20) / Ru (8 .7) / Cu (85) / Ta (30)
The brackets indicate the film thickness and the unit is 単 位.

  FIG. 13 shows the relationship between the composition ratio of the CoFe alloy constituting the first magnetic layer and the coercivity of the first magnetic layer at that time, and FIG. 14 shows the composition ratio of the CoFe alloy constituting the first magnetic layer. It is the graph which measured the relationship with the magnetostriction constant of the 1st magnetic layer at that time. In addition, in each figure, the comparative example (it describes with no PtMn base | substrate in a drawing) which does not provide the nonmagnetic metal layer which consists of PtMn was also put on the graph.

  As shown in FIG. 13, in the example in which the nonmagnetic metal layer made of PtMn was provided, the coercive force Hc of the first magnetic layer tended to be lower than in the comparative example in which the nonmagnetic metal layer made of PtMn was not provided. It was.

  In the present invention, the main purpose is to increase the magnetostriction constant of FIG. 14 as follows. However, since the coercive force of the first magnetic layer is also an important factor for fixing the magnetization, the composition ratio that increases the coercive force is selected. It is preferable.

  In FIG. 13, it was found that a relatively high coercive force can be obtained if the Co composition ratio is selected within the range of 40 at% to 60 at%.

  As shown in FIG. 14, in the example in which the nonmagnetic metal layer made of PtMn was provided, it was found that the magnetostriction constant λs of the first magnetic layer could be made larger than the comparative example in which the nonmagnetic metal layer made of PtMn was not provided. .

  As shown in FIG. 14, it was found that the magnetostriction constant of the first magnetic layer can be stably set to a high value if the Co composition ratio is selected within the range of 40 at% to 60 at%. It was also found that when the Co composition ratio was 100 at%, the magnetostriction constant of the first magnetic layer could be set to a very high value.

From the experimental results shown in FIG. 13 and FIG. 14, the first magnetic layer is (Co _x Fe _1-x ) _{100- y My} (where element M is a rare earth element), or (Co _x Fe _1-x ) _100-z. In the case of forming with a magnetic material represented by N _z (however, the element N metal element), setting the atomic ratio x between Co and Fe to 0.4 to 0.6 or 1 increases the magnetostriction constant, and From the viewpoint of obtaining a stable coercive force, it was derived that was preferable.

Sectional drawing which looked at the structure of the magnetic detection element of 1st Embodiment of this invention from the opposing surface side with a recording medium, FIG. 1 is a plan view of the magnetic detection element shown in FIG. A schematic diagram showing a state in which a nonmagnetic metal layer and a pinned magnetic layer are aligned and strain is generated, The fragmentary sectional view of the vicinity of the pinned magnetic layer different from FIG. 1 of the magnetic sensing element of the present invention, Sectional drawing which looked at the structure of the magnetic detection element of 2nd Embodiment of this invention from the opposing surface side with a recording medium, Sectional drawing which looked at the structure of the magnetic detection element of 3rd Embodiment of this invention from the opposing surface side with a recording medium, A graph showing the relationship between the composition ratio of Tb, Pr, Sm and the magnetostriction constant of the first magnetic layer, wherein the first magnetic layer is made of Tb—Co, Pr—Co or Sm—Co; A graph showing a relationship between a spin flop magnetic field (Hsf) and a resistance change rate (ΔR / R) when the first magnetic layer is formed of Tb—Co, Pr—Co, Sm—Co or Co; A graph showing the relationship between the composition ratio of Ir, Rh, and Pt and the coercivity of the first magnetic layer, wherein the first magnetic layer is made of Ir—Co, Rh—Co, or Pt—Co; A graph showing the relationship between the composition ratio of Ir and Rh and the magnetostriction constant of the first magnetic layer, wherein the first magnetic layer is made of Ir—Co and Rh—Co; A graph showing the relationship between the composition ratio of Pt and the magnetostriction constant of the pinned magnetic layer having a laminated ferri-pinned structure, in which the first magnetic layer is made of Pt—Co; A graph showing a relationship between net-Ms · t of a laminated ferri-pinned structure and a rate of change in resistance (ΔR / R) when the first magnetic layer is made of Ir—Co, Rh—Co, or Co; A graph showing the relationship between the Co composition ratio and the coercive force Hc of the first magnetic layer when the first magnetic layer is made of CoFe and there is a PtMn underlayer (Example) and when there is no PtMn underlayer (Comparative Example) , A graph showing the relationship between the composition ratio of Co and the magnetostriction constant λs of the first magnetic layer when the first magnetic layer is made of CoFe and there is a PtMn underlayer (Example) and when there is no PtMn underlayer (Comparative Example) ,

Explanation of symbols

20 lower gap layer 21 seed layer 22 nonmagnetic metal layer 23 pinned magnetic layer 23a first magnetic layer 23b nonmagnetic intermediate layer 23c second magnetic layer 24 nonmagnetic material layer 25 free magnetic layer 26 protective layer 27 bias underlayer 28 hard bias Layer 29 Electrode layer 30 Upper gap layer 32 Nonmagnetic layer

Claims (17)

In a magnetic sensing element in which a pinned magnetic layer and a free magnetic layer are laminated via a nonmagnetic material layer,
The pinned magnetic layer includes a plurality of magnetic layers stacked via a nonmagnetic intermediate layer, and is formed at a position farthest from the nonmagnetic material layer among the plurality of magnetic layers. X-Mn (where X is one or more of Pt, Pd, Ir, Rh, Ru, Os, Ni, Fe) on the opposite side of the magnetic layer to the side on which the nonmagnetic material layer is provided A non-magnetic metal layer made of an alloy is formed,
The first magnetic layer is mainly composed of Co and Fe, and further added with a rare earth element or a noble metal element,
At least part of the crystals in the nonmagnetic metal layer and the crystals in the first magnetic layer are in an epitaxial or heteroepitaxial state,
An end face of the fixed magnetic layer facing the recording medium is open.   The magnetic detection element according to claim 1, wherein the rare earth element is selected from at least one of Tb, Sm, Pr, Y, Ce, Nd, Gd, Dy, Ho, Er, and Yb. Said first magnetic _{layer, (Co x Fe 1-x} ) formed of a magnetic material represented by _{100-y M y,} element M, Tb, Sm, Pr, Y , Ce, Nd, Gd, Dy, Ho 3. The magnetic detection element according to claim 2, wherein at least one kind is selected from among Er, Er, and Yb, and the composition ratio y is 0.3 at% or more and 5 at% or less.   The magnetic sensing element according to claim 1, wherein at least one of the noble metal elements is selected from Pt, Rh, Ir, and Re. Said first magnetic _{layer, (Co x Fe 1-x} ) formed of a magnetic material represented by _{100-z N z,} the element N is, Pt, Rh, Ir, at least one from among Re is selected The magnetic detection element according to claim 4, wherein the composition ratio z is 5 at% or more and 20 at% or less.   The magnetic detection element according to claim 3 or 5, wherein the atomic ratio x is 1 or within a range of 0.4 to 0.6.   The magnetic detection element according to claim 1, wherein the first magnetic layer has a thickness in a range of 12 to 19 mm.   The first magnetic layer has a laminated structure of at least two layers, and the magnetic layer formed closest to the nonmagnetic metal layer is mainly composed of Co and Fe, and further added with a rare earth element or a noble metal element. The magnetic detection element according to claim 1, wherein the magnetic detection element is formed of a magnetic material.   The magnetic detection element according to claim 8, wherein a magnetic layer in contact with the nonmagnetic intermediate layer among the magnetic layers constituting the first magnetic layer is formed of a CoFe alloy or Co.   The magnetic detection element according to claim 1, wherein the nonmagnetic metal layer is formed in contact with an interface of the first magnetic layer.   The nonmagnetic metal layer has a face-centered cubic lattice (fcc) structure in the vicinity of or in the entire region of the pinned magnetic layer on the first magnetic layer side, and is represented as a {111} plane in a direction parallel to the interface. The magnetic sensing element according to claim 1, wherein equivalent crystal planes are preferentially oriented.   The magnetic sensing element according to claim 1, wherein the nonmagnetic metal layer has a thickness of 5 to 50 mm.   The X element content in the X-Mn alloy (where X is one or more of Pt, Pd, Os, Ni, and Fe) is 45 atomic percent or more and 99 atomic percent or less. The magnetic detection element according to any one of 1 to 12.   13. The X element content in the X—Mn alloy (where X is one or more of Ir, Rh, and Ru) is 17 atomic% or more and 99 atomic% or less. Any one of the magnetic detection elements.   The magnetic sensing element according to any one of claims 1 to 12, wherein the content of Ir in the Ir-Mn alloy is 20 atomic percent or more and 99 atomic percent or less.   The first magnetic layer of the pinned magnetic layer has a face-centered cubic lattice (fcc) structure or a body-centered cubic lattice (bcc) structure in the vicinity of the interface on the nonmagnetic metal layer side or in the entire region, and a direction parallel to the interface. The magnetic sensing element according to claim 1, wherein an equivalent crystal plane represented as a {111} plane or a {110} plane is preferentially oriented.   The magnetic detection element according to claim 1, wherein a free magnetic layer, a nonmagnetic material layer, and a fixed magnetic layer are laminated in that order from the bottom.

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