Abstract:
The present invention addresses the problem of providing an element which uses the current-perpendicular-to-plane giant magnetoresistance (CPPGMR) effect of a thin film having the three-layer structure of ferromagnetic metal/non-magnetic metal/ferromagnetic metal. The problem is solved by a magnetoresistive element provided with a lower ferromagnetic layer and an upper ferromagnetic layer which contain a Heusler alloy, and a spacer layer sandwiched between the lower ferromagnetic layer and the upper ferromagnetic layer, the magnetoresistive element being characterized in that the spacer layer contains an alloy having a bcc structure. Furthermore, it is preferable for the alloy to have a disordered bcc structure.

Description:
TECHNICAL FIELD 
       [0001]    The present invention relates to an element using a current-perpendicular-to-plane giant magnetoresistance (CPPGMR) effect of a thin film having a three-layer structure of ferromagnetic metal/non-magnetic metal/ferromagnetic metal, particularly to a magnetoresistive element using a non-magnetic spacer layer having a body-centered cubic (bcc) structure as the non-magnetic metal layer. 
       BACKGROUND ART 
       [0002]    The element using a current-perpendicular-to-plane giant magnetoresistance (CPPGMR) effect is formed of a thin film having a three-layer structure of ferromagnetic metal/non-magnetic metal/ferromagnetic metal, and is expected to be used for a reading head for a magnetic disc. An element using a Heusler alloy having a large spin polarizability as a ferromagnetic metal has been studied. For example, Patent Literatures 1 and 2 have proposed use of Cu which is a metal having a face-centered cubic (fcc) structure for a spacer layer (layer of a non-magnetic metal). In addition, Non-Patent Literatures 1 and 2 have proposed use of a Heusler alloy CFGG for a magnetic layer and use of Ag which is a metal having a face-centered cubic structure for a spacer layer. 
         [0003]    Furthermore, Non-Patent Literature 3 discloses that a magnetoresistive output is changed largely by the orientation of a Heusler alloy as a ferromagnetic layer when a spacer layer having a fcc structure of Ag or Cu is used. This is because a lattice distortion formed by the Heusler alloy having a bcc group structure and Ag or Cu having a fcc structure largely depends on a crystal orientation of the Heusler alloy. As a result, it is disclosed that high magnetoresistance can be obtained when (001) plane of the Heusler alloy constitutes an interface with the spacer layer in the case of using Ag and when (011) plane of the Heusler alloy constitutes an interface with the spacer layer in the case of using Cu. In this context, (001) and (011) each are a Miller index to describe a crystal plane or a direction in a lattice of a crystal. 
         [0004]    However, because of magnetic conductivity dependence due to the lattice distortion formed by the Heusler alloy having a bcc group structure and Ag or Cu having a fcc structure and a crystal orientation thereof, such a magnetoresistive output as to be predicted from theoretical calculation has not been obtained. 
         [0005]    On the other hand, it has been theoretically predicted that use of a L2 1  ordered alloy Cu 2 RhSn or a B2 type ordered alloy NiAl having the same bcc group crystal structure as the Heusler alloy for a spacer layer improves consistency at an interface of a band structure to bring about a larger magnetoresistance effect. Therefore, studies have been made based on this theoretical prediction. Patent Literatures 3 and 4 according to proposal by the present inventors disclose CPPGMR using a Heusler alloy for a magnetic layer and using a L2 1  type or B2 type ordered alloy for a spacer layer. However, the inventions according to Patent Literatures 3 and 4 have not obtained such an effect as to be predicted from theoretical calculation. It is considered that this is because the magnetoresistance effect is weakened by an effect of strong spin-orbit scattering or spin scattering due to a relatively heavy element Rh. Sn or a magnetic element Ni contained in these alloys. 
       CITATION LIST 
     Patent Literatures 
       [0006]    PATENT LITERATURE 1: JP 2007-59927 A 
         [0007]    PATENT LITERATURE 2: JP 2008-52840 A 
         [0008]    PATENT LITERATURE 3: JP 2010-212631 A 
         [0009]    PATENT LITERATURE 4: JP 5245179 B2 
       Non-Patent Literatures 
       [0010]    NON-PATENT LITERATURE 1: Appl. Phys. Lett. 98, 152501 (2011). 
         [0011]    NON-PATENT LITERATURE 2: J. Appl. Phys. 113, 043901 (2013). 
         [0012]    NON-PATENT LITERATURE 3: Jiamin Chen, Songtian Li, T. Furubayashi, Y. K. Takahashi and K. Hono, J. Appl. Phys. 115, 233905 (2014) 
       SUMMARY OF INVENTION 
     Technical Problem 
       [0013]    The present invention has solved the above problems. An object thereof is to provide a magnetoresistive element exhibiting a higher magnetoresistive output than a conventional structure in an element using a current-perpendicular-to-plane giant magnetoresistance (CPPGMR) effect of a thin film having a three-layer structure of ferromagnetic metal/non-magnetic metal/ferromagnetic metal. 
       Solution to Problem 
       [0014]    In order to solve the above problems, the present invention is a magnetoresistive element having the following configuration. 
         [0015]    For example, as illustrated in  FIG. 1 , the magnetoresistive element of the present invention includes a lower ferromagnetic layer  13  and an upper ferromagnetic layer each formed of a Heusler alloy, and a spacer layer  14  sandwiched between the lower ferromagnetic layer  13  and the upper ferromagnetic layer  15 , and is characterized in that the spacer layer  14  is formed of an alloy or an intermetallic compound having a bcc structure. 
         [0016]    In the magnetoresistive element of the present invention, the alloy or the intermetallic compound is preferably selected from the group consisting of CuZn, Cu 3 Al, CuBe, Ag 3 Al, AgMg, and AgZn. 
         [0017]    In the magnetoresistive element of the present invention, the alloy or the intermetallic compound is preferably at least one selected from the group consisting of an alloy having a bcc structure formed of Cu and Zn, an alloy having a bcc structure formed of Cu and Al, an alloy having a bcc structure formed of Cu and Be, an alloy having a bcc structure formed of Ag and Al, an alloy having a bcc structure formed of Ag and Mg, and an alloy having a bcc structure formed of Ag and Zn. 
         [0018]    In the magnetoresistive element of the present invention, the alloy or the intermetallic compound preferably has a disordered bcc structure. 
         [0019]    In the magnetoresistive element of the present invention, a substrate  11  is preferably at least one selected from the group consisting of a surface oxidized Si substrate, a silicon substrate, a glass substrate, a metal substrate, and an MgO substrate. 
         [0020]    For example, as illustrated in  FIG. 1 , the magnetoresistive element of the present invention is preferably stacked on a base layer (also referred to as an orientation layer)  12  formed on the substrate  11  to epitaxially grow a Heusler alloy in a predetermined crystal direction. The base layer  12  preferably contains at least one metal or alloy selected from the group consisting of Ag, Al, Cu, Au, and Cr. A crystal direction in which the Heusler alloy is grown epitaxially is preferably (001) direction. 
         [0021]    In the magnetoresistive element of the present invention, each of the lower ferromagnetic layer  13  and the upper ferromagnetic layer  15  preferably contains a Heusler alloy represented by the composition formula Co 2 AB. The aforementioned A is Cr, Mn, Fe, or a mixture of two or more species thereof in which the total amount thereof is 1. The aforementioned B is Al, Si, Ga, Ge, In, Sn, or a mixture of two or more species thereof in which the total amount thereof is 1. 
         [0022]    In the magnetoresistive element of the present invention, each of the lower ferromagnetic layer  13  and the upper ferromagnetic layer  15  is preferably formed of a Heusler ferromagnetic alloy having a B2 ordered structure or a L2 1  ordered structure, and the Heusler ferromagnetic alloy preferably contains a 
         [0023]    Heusler ferromagnetic alloy selected from the group consisting of Co 2 Fe(Ga x Ge x−1 ) (0.25&lt;x&lt;0.6), CoFeAlSi, CoMnSi, CoMnGe, CoFeAl, and CoFeSi. 
         [0024]    In the magnetoresistive element of the present invention, a base layer  12   b  as an electrode for measuring magnetoresistance is preferably further disposed while being sandwiched between the base layer  12  and the lower ferromagnetic layer  13 . 
         [0025]    The magnetoresistive element of the present invention preferably further includes a cap layer  16  for protecting a surface, stacked on the upper ferromagnetic layer  15 , and the cap layer  16  is preferably formed of at least one metal or alloy selected from the group consisting of Ag, Al, Cu, Au, Ru, and Pt. 
         [0026]    The magnetoresistive element of the present invention preferably further includes a pinning layer disposed on the upper ferromagnetic layer  15  or under the lower ferromagnetic layer  13 , and the pinning layer is preferably a layer of an antiferromagnetic substance such as an IrMn alloy or a PtMn alloy. 
         [0027]    In the magnetoresistive element having such a configuration, by suppressing magnetization reversal of the upper ferromagnetic layer by exchange anisotropy, the upper ferromagnetic layer and the lower ferromagnetic layer magnetized antiparallel can be stabilized. 
         [0028]    For example, as illustrated in  FIG. 1 , the current-perpendicular-to-plane giant magnetoresistance (CPPGMR) element of the present invention is characterized by the following. That is, the current-perpendicular-to-plane giant magnetoresistance (CPPGMR) element includes the spacer layer  14  between the Heusler alloy thin films ( 13  and  15 ). Each of the Heusler alloy thin films is formed of a Heusler ferromagnetic alloy having a B2 ordered structure or a L2 1  ordered structure. The Heusler ferromagnetic alloy is selected from the group consisting of Co 2 Fe(Ga x Ge x−1 ) (0.25&lt;x&lt;0.6), CoFeAlSi, CoMnSi, CoMnGe, CoFeAl, and CoFeSi. The spacer layer  14  is formed of an alloy or an intermetallic compound having a bcc structure. The alloy or the intermetallic compound is selected from the group consisting of CuZn, Cu 3 Al, CuBe, Ag 3 Al, AgMg, and AgZn. 
         [0029]    Here, when Co 2 Fe(Ga x Ge x−1 ) has a Ga ratio x of 0.25 or less or a Ga ratio x of 0.6 or more, magnetoresistance is lowered disadvantageously due to reduction of a spin polarizability. The Ga ratio x in (Ga x Ge x−1 ) is preferably between 0.25 and 0.6, and more preferably between 0.45 and 0.55. 
         [0030]    The present invention and preferable embodiments thereof will be listed as follows: 
         [0031]    [1] A magnetoresistive element including a lower ferromagnetic layer and an upper ferromagnetic layer each containing a Heusler alloy, and a spacer layer sandwiched between the lower ferromagnetic layer and the upper ferromagnetic layer, characterized in that the spacer layer contains an alloy having a bcc structure. 
         [0032]    [2] The magnetoresistive element described in [1], characterized in that the alloy is at least one selected from the group consisting of CuZn, Cu 3 Al, CuBe, Ag 3 Al, AgMg, and AgZn. 
         [0033]    [3] The magnetoresistive element described in [1], characterized in that the alloy is at least one selected from the group consisting of an alloy having a bcc structure formed of Cu and Zn, an alloy having a bcc structure formed of Cu and Al, an alloy having a bcc structure formed of Cu and Be, an alloy having a bcc structure formed of Ag and Al, an alloy having a bcc structure formed of Ag and Mg, and an alloy having a bcc structure formed of Ag and Zn. 
         [0034]    [4] The magnetoresistive element described in any one of [1] to [3], in which the alloy has a disordered bcc structure. 
         [0035]    [5] The magnetoresistive element described in any one of [1] to [4], further including a substrate, characterized in that the substrate is at least one selected from the group consisting of a surface oxidized Si substrate, a silicon substrate, a glass substrate, a metal substrate, and an MgO substrate. 
         [0036]    [6] The magnetoresistive element described in [5], further including an orientation layer formed on the substrate to epitaxially grow the Heusler alloy in a predetermined crystal direction, characterized in that the orientation layer contains at least one metal selected from the group consisting of Ag, Al, Cu, Au, and Cr or an alloy thereof, and a crystal direction in which the Heusler alloy is grown epitaxially is (001) direction. 
         [0037]    [7] The magnetoresistive element described in any one of [1] to [6], characterized in that each of the lower ferromagnetic layer and the upper ferromagnetic layer contains a Heusler alloy represented by the composition formula Co 2 AB, the aforementioned A is Cr, Mn, Fe, or a combination of two or more species thereof (the total amount of A is 1), and the B is Al, Si, Ga, Ge, In, Sn, or a combination of two or more species thereof (the total amount of B is 1). 
         [0038]    [8] The magnetoresistive element described in [7], characterized in that each of the lower ferromagnetic layer and the upper ferromagnetic layer contains a Heusler ferromagnetic alloy having a B2 ordered structure or a L2 1  ordered structure, and the Heusler ferromagnetic alloy is selected from the group consisting of Co 2 Fe(Ga x Ge x−1 ) (0.25&lt;x&lt;0.6), Co 2 FeAl 0.5 Si 0.5 , Co 2 MnSi, Co 2 MnGe, Co 2 FeAl, and Co 2 FeSi. 
         [0039]    [9] The magnetoresistive element described in any one of [6] to [8], further including a base layer as an electrode for measuring magnetoresistance, characterized in that the base layer is disposed between the orientation layer and the lower ferromagnetic layer. 
         [0040]    [10] The magnetoresistive element described in any one of [1] to [9], further including a cap layer for protecting a surface, stacked on the upper ferromagnetic layer, characterized in that the cap layer contains at least one metal selected from the group consisting of Ag, Al, Cu, Au, Ru, and Pt or an alloy thereof. 
         [0041]    [11] The magnetoresistive element described in any one of [1] to [10], further including a pinning layer disposed on the upper ferromagnetic layer or under the lower ferromagnetic layer, characterized in that the pinning layer is a layer of an antiferromagnetic substance such as an IrMn alloy or a PtMn alloy. 
         [0042]    [12] A current-perpendicular-to-plane giant magnetoresistance (CPPGMR) element including at least one spacer layer between at least two Heusler alloy thin films, characterized in that each of the Heusler alloy thin films contains a Heusler ferromagnetic alloy having a B2 ordered structure or a L2 1  ordered structure, the Heusler ferromagnetic alloy is selected from the group consisting of Co 2 Fe(Ga x Ge x−1 ) (0.25&lt;x&lt;0.6), Co 2 FeAl 0.5 Si 0.5 , Co 2 MnSi, Co 2 MnGe, Co 2 FeAl, and Co 2 FeSi, the spacer layer contains an alloy having a bcc structure, and the alloy is selected from the group consisting of CuZn, Cu 3 Al, CuBe, Ag 3 Al, AgMg, and AgZn. 
         [0043]    [13] The current-perpendicular-to-plane giant magnetoresistance (CPPGMR) element described in [12], in which the alloy has a disordered bcc structure. 
         [0044]    [14] A magnetic head characterized by including the magnetoresistive element described in any one of [1 to  11  or the current-perpendicular-to-plane giant magnetoresistance element described in [12] or [13]. 
         [0045]    [15] A magnetic reproducing device characterized by including the magnetic head described in [14]. 
         [0046]    The present invention and preferable embodiments thereof can be listed also as follows: 
         [0047]    [1] A magnetoresistive element including a lower ferromagnetic layer and an upper ferromagnetic layer each formed of a Heusler alloy, and a spacer layer sandwiched between the lower ferromagnetic layer and the upper ferromagnetic layer, characterized in that the spacer layer is formed of an intermetallic compound having a bcc structure. 
         [0048]    [2] The magnetoresistive element described in [1], characterized in that the intermetallic compound is selected from the group consisting of CuZn, Cu 3 Al, CuBe, Ag 3 Al, AgMg, and AgZn. 
         [0049]    [3] The magnetoresistive element described in [1], characterized in that the intermetallic compound is an intermetallic compound of at least one alloy selected from the group consisting of an alloy having a bcc structure formed of Cu and Zn, an alloy having a bcc structure formed of Cu and Al, an alloy having a bcc structure formed of Cu and Be, an alloy having a bcc structure formed of Ag and Al, an alloy having a bcc structure formed of Ag and Mg, and an alloy having a bcc structure formed of Ag and Zn. 
         [0050]    [4] The magnetoresistive element described in any one of [1] to [3], characterized in that the substrate is at least one selected from the group consisting of a surface oxidized Si substrate, a silicon substrate, a glass substrate, a metal substrate, and an MgO substrate. 
         [0051]    [5] The magnetoresistive element described in any one of [1] to [4], stacked on a base layer formed on the substrate to epitaxially grow a Heusler alloy in a predetermined crystal direction, characterized in that the base layer contains at least one metal or alloy selected from the group consisting of Ag, Al, Cu, Au, and Cr, and a crystal direction in which the Heusler alloy is grown epitaxially is (001) direction. 
         [0052]    [6] The magnetoresistive element described in any one of [1] to [5], characterized in that each of the lower ferromagnetic layer and the upper ferromagnetic layer contains a Heusler alloy represented by the composition formula Co 2 AB, the aforementioned A is Cr, Mn, Fe, or a mixture of two or more species thereof in which the total amount thereof is 1, and the B is Al, Si, Ga, Ge, In, Sn, or a mixture of two or more species thereof in which the total amount thereof is 1. 
         [0053]    [7] The magnetoresistive element described in [6], characterized in that each of the lower ferromagnetic layer and the upper ferromagnetic layer is formed of a Heusler ferromagnetic alloy having a B2 ordered structure or a L2 1  ordered structure, and the Heusler ferromagnetic alloy contains a Heusler ferromagnetic alloy selected from the group consisting of Co 2 Fe(Ga x Ge x−1 ) (0.25&lt;x&lt;0.6), CoFeAlSi, CoMnSi, CoMnGe, CoFeAl, and CoFeSi. 
         [0054]    [8] The magnetoresistive element described in any one of [1] to [7], further including a base layer as an electrode for measuring magnetoresistance while the base layer is sandwiched between the base layer and the lower ferromagnetic layer. 
         [0055]    [9] The magnetoresistive element described in any one of [1] to [8], further including a cap layer for protecting a surface, stacked on the upper ferromagnetic layer, characterized in that the cap layer contains at least one metal or alloy selected from the group consisting of Ag, Al, Cu, Au, Ru, and Pt. 
         [0056]    [10] The magnetoresistive element described in any one of [1] to [9], further including a pinning layer disposed on the upper ferromagnetic layer or under the lower ferromagnetic layer, characterized in that the pinning layer is a layer of an antiferromagnetic substance such as an IrMn alloy or a PtMn alloy. 
         [0057]    [11] A current-perpendicular-to-plane giant magnetoresistance (CPPGMR) element including a spacer layer between Heusler alloy thin films, characterized in that each of the Heusler alloy thin films is formed of a Heusler ferromagnetic alloy having a B2 ordered structure or a L2 1  ordered structure, the Heusler ferromagnetic alloy is selected from the group consisting of Co 2 Fe(Ga x Ge x−1 ) (0.25&lt;x&lt;0.6), CoFeAlSi, CoMnSi, CoMnGe, CoFeAl, and CoFeSi, the spacer layer is formed of an intermetallic compound having a bcc structure, and the intermetallic compound is selected from the group consisting of CuZn, Cu 3 Al, CuBe, Ag 3 Al, AgMg, and AgZn. 
         [0058]    [12] A magnetic head characterized by using the magnetoresistive element described in any one of [1] to [10] or the current-perpendicular-to-plane giant magnetoresistance element described in [11]. 
         [0059]    [13] A magnetic reproducing device characterized by using the magnetic head described in [12]. 
       ADVANTAGEOUS EFFECTS OF INVENTION 
       [0060]    In the present invention, a relatively heavy element Rh.Sn or a magnetic element Ni is not essential unlike the prior art, but an alloy having a bcc structure, for example, a Cu-based alloy such as CuZn or Cu 3 Al is used for a spacer layer as a material having a low electric resistivity, suitable for the spacer layer. A larger change amount of magnetoresistance can be thereby obtained than a case of using an Ag spacer layer. The Cu alloy having a bcc group structure, used in an example of the present invention, is lattice-matched well with a Heusler alloy regardless of an orientation. Therefore, a high magnetoresistance ratio is obtained regardless of an orientation a Heusler alloy layer. 
         [0061]    Therefore, in an example of the present invention, a CPPGMR element using a Cu alloy having a bcc group structure can be manufactured, and a high magnetoresistive output can be provided. In addition, the CPPGMR element is suitably used for a magnetic head and a magnetic reproducing device using the magnetoresistive element of the present invention. 
     
    
     
       BRIEF DESCRIPTION OF THE DRAWINGS 
         [0062]      FIG. 1  is a schematic structural view of a magnetoresistive element according to an embodiment of the present invention. 
           [0063]      FIG. 2  is an X-ray diffraction pattern diagram of a film obtained by stacking Cr(10)/Ag(100)/CFGG(10)/CuZn(5)/CFGG(10)/Ag(5)/Ru(8) on an MgO(001) single crystal substrate from the bottom. 
           [0064]      FIG. 3  illustrates a cross-sectional transmission electron micrograph and electron diffraction images of layers after the same sample as in  FIG. 2  is annealed at 300° C. 
           [0065]      FIG. 4  is a schematic cross-sectional view of an element obtained by adding an electrode for measuring electric resistance with respect to a magnetic field to a CPPGMR element according to an embodiment of the present invention. 
           [0066]      FIG. 5  is a diagram for explaining change of electric resistance×element area with respect to an applied magnetic field in an element using CuZn for a spacer layer. 
           [0067]      FIG. 6  is a diagram for explaining change amount of magnetoresistance×element area (ΔRA) with respect to an annealing temperature. 
           [0068]      FIG. 7  is a diagram for explaining an X-ray diffraction pattern of a film obtained by stacking Cr(10)/Ag(10)/CFGG(5)/Cu 3 Al(20) on an MgO(001) single crystal substrate from the bottom. 
       
    
    
     DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS 
       [0069]    Hereinafter, the present invention will be described with reference to the drawings. 
         [0070]      FIG. 1  is a schematic structural view of a magnetoresistive element according to an embodiment of the present invention. In  FIG. 1 , the magnetoresistive element has a substrate  11 , a base layer  12 , a lower ferromagnetic layer  13 , a spacer layer  14 , an upper ferromagnetic layer  15 , and a cap layer  16  stacked in this order. 
         [0071]    For example, a single crystal MgO substrate is used for the substrate  11 . However, the substrate  11  is not particularly limited to the single crystal MgO substrate. Si, a metal, an alloy, or the like on which a Heusler alloy layer is polycrystalline may be used for the substrate. The substrate  11  is preferably a surface oxidized Si substrate due to inexpensiveness, but may be a silicon substrate used for manufacturing a semiconductor, a glass substrate, or a metal substrate. Even when these materials are used for the substrate  11 , a high magnetoresistance ratio is obtained as a magnetoresistive element. 
         [0072]    The base layer  12  is an electrode for measuring magnetoresistance. For example, a metal containing at least one selected from the group consisting of Ag, Al, Cu, Au, and Cr, or an alloy thereof is used for the base layer  12 . Note that the base layer  12  may have a two-layer structure obtained by adding a base layer  12   a  under a base layer  12   b  or a multi-layer structure having three or more layers. 
         [0073]    Note that an orientation layer may be disposed under the base layer  12 . The orientation layer orients a Heusler alloy layer in a (100) direction. For example, a layer containing at least one selected from the group consisting of an MgO alloy, a TiN alloy, and a NiTa alloy is used for the orientation layer. 
         [0074]    Each of the lower ferromagnetic layer  13  and the upper ferromagnetic layer  15  contains a Heusler alloy represented by the composition formula Co 2 AB. The A is Cr, Mn, Fe, or a mixture of two or more species thereof in which the total amount thereof is 1. The aforementioned B is Al, Si, Ga, Ge, In, Sn, or a mixture of two or more species thereof in which the total amount thereof is 1. The Heusler alloy is particularly preferably Co 2 FeGa 0.5 Ge 0.5  (CFGG), but may be Co 2 FeAl 1−x Si x , Co 2 MnSi, or Co 2 Fe 1−x Mn x Si obtaining a large change amount of magnetoresistance×element area (ΔRA) in CPPGMR using a (100) single crystal thin film. For each of the upper ferromagnetic layer and the lower ferromagnetic layer, one Heusler alloy may be used, or two or more Heusler alloys, other metals, or other alloys may be combined. 
         [0075]    The spacer layer  14  is formed of a metal or an alloy. The cap layer  16  is formed of a metal or an alloy for protecting a surface. An alloy or an intermetallic compound selected from the group consisting of CuZn, Cu 3 Al, CuBe, Ag 3 Al, AgMg, and AgZn is used for the spacer layer  14 . Furthermore, for example, a layer formed of a metal containing at least one selected from the group consisting of Ag, Al, Cu, Au, and Cr, or an alloy thereof may be added. For the spacer layer  14 , at least one alloy or intermetallic compound selected from the group consisting of an alloy having a bcc structure formed of Cu and Zn, an alloy having a bcc structure formed of Cu and Al, an alloy having a bcc structure formed of Cu and Be, an alloy having a bcc structure formed of Ag and Al, an alloy having a bcc structure formed of Ag and Mg, and an alloy having a bcc structure formed of Ag and Zn may be used. It is considered that the alloy or the intermetallic compound constituting the spacer layer  14  only needs to have a bcc structure even when having a composition different from CuZn, Cu 3 Al, CuBe, Ag 3 Al, AgMg, or AgZn which is a typical alloy or intermetallic compound to a considerable extent. Therefore, a composition ratio of an element in the alloy or the intermetallic compound can be selected appropriately within a range constituting a bcc structure. For example, the spacer layer  14  has a thickness of 0.1 nm to 20 nm. Therefore, the alloy or the intermetallic compound forms a metal atomic layer formed of about one to 200 atoms. The thickness of the spacer layer  14  is from several atoms to several hundreds of atoms. Therefore, a crystal structure of the alloy or the intermetallic compound may be different from a bulk due to an influence by an adjacent layer such as the lower ferromagnetic layer. 
         [0076]    For example, a metal containing at least one selected from the group consisting of Ag, Al, Cu, Au, and Cr, or an alloy thereof is used for the cap layer  16 . One material may be used or two or more materials may be stacked to be used for each of the base layer  12 , the spacer layer  14 , and the cap layer  16 . 
       EXAMPLE 1 
       [0077]      FIG. 1  is a schematic cross-sectional view of a CPPGMR element according to an embodiment of the present invention.  FIG. 4  is a schematic cross-sectional view of an element obtained by adding an electrode for measuring electric resistance with respect to a magnetic field to a CPPGMR element according to an embodiment of the present invention. In  FIG. 4 , a single crystal MgO substrate is used for the substrate  11 , a product obtained by stacking Cr and Ag from the bottom is used for the base layer  12 , a Heusler alloy Co 2 FeGa 0.5 Ge 0.5  (CFGG) is used for each of the lower ferromagnetic layer  13  and the upper ferromagnetic layer  15 , CuZn is used for the spacer layer  14 , and a product obtained by stacking Ag and Ru from the bottom is used for the cap layer 16. 
         [0078]    In the element illustrated in  FIG. 1 , a film was formed on an MgO substrate by a sputtering method so as to have a film configuration from the bottom of Cr(10)/Ag(100)/CFGG(10)/CuZn(5)/CFGG(10)/Ag(5)/Ru(8) in which each of the numbers in the parentheses indicates the film thickness (nm). 
         [0079]      FIG. 2  is an X-ray diffraction pattern diagram of a CPPGMR element film having the above-mentioned stacked configuration. When the pattern diagram is represented by 2θ in the X-ray diffraction, three sharp peaks around 39°, 41°, and 43° due to reflection on the MgO substrate are observed. A peak at 31° is found due to reflection in a CFGG(002) direction, and an obtuse peak around 64° is found due to reflection in a CFGG(004) direction. A peak at 44° is found due to reflection in an Ag(002) direction, and an obtuse peak around 60° is found due to reflection in a CuZn(002) direction. Therefore, by examining a crystal structure, it has been found that each of a Cr layer, an Ag layer, a CuZn layer, and a CFGG layer is oriented in a (001) direction from the result illustrated in  FIG. 2 . 
         [0080]      FIG. 3  illustrates a cross-sectional transmission electron micrograph and electron diffraction images of layers after the same sample as in  FIG. 2  is annealed at 300° C. In order to improve a crystal structure of a CFGG thin film, the same sample as in  FIG. 2  has been annealed at 300 to 400° C. In the CPPGMR element film having the above stacked configuration, all the layers from the single crystal MgO substrate  11  to an upper Ag cap layer  16   a  have been grown epitaxially while being oriented in (001) direction. In the result of the electron diffraction, diffraction due to a B2 ordered structure of CuZn is not found. Therefore, it is considered that the spacer layer  14  has a disordered bcc structure of CuZn. An equilibrium diagram indicates that CuZn is an alloy having a B2 ordered structure. However, a thin film for CPPGMR was manufactured, and it was found that CuZn did not have a B2 ordered structure but was a disordered alloy having a bcc structure. 
         [0081]    Next, the element structure in  FIG. 4  will be described in detail. In  FIG. 4 , note that the same sign will be given to a component having the same function as in  FIG. 1 , and description thereof will be omitted. In  FIG. 4 , a silicon oxide layer  17  is disposed around the lower ferromagnetic layer  13 , the spacer layer  14 , the upper ferromagnetic layer  15 , and the cap layer  16  illustrated in  FIG. 1 , and is stacked on the Ag base layer  12   b . A copper electrode layer  18  is stacked on the silicon oxide layer  17  and the cap layer  16 . A constant current source  19  is connected to the Ag base layer  12   b  and the copper electrode layer  18  via leads  20   a  and  20   b , and supplies a constant current in a direction perpendicular to a film surface of the CPPGMR element. A voltmeter  21  is connected to the Ag base layer  12   b  and the copper electrode layer  18  via the leads  22   a  and  22   b , and measures a voltage generated in a direction perpendicular to a film surface of the CPPGMR element. Electric resistance in a direction perpendicular to a film surface of the CPPGMR element can be measured from a current value of the constant current source  19  and a measured voltage value of the voltmeter  21 . Therefore, change of electric resistance of the CPPGMR element with respect to a magnetic field can be examined. 
         [0082]      FIG. 5  is an exemplary diagram for explaining change of electric resistance×element area with respect to an applied magnetic field in an element using CuZn for a spacer layer. The horizontal axis indicates the applied magnetic field H (kA/m), and the vertical axis indicates electric resistance×element area [mΩ·m 2 ]. When the applied magnetic field H (kA/m) is increased from −80 kA/m to +80 kA/m, the electric resistance×element area is about 51.6 [mQ·μm 2 ] in a region of −80 kA/m to −10 kA/m, linearly increased about from 53.2 to 55.0 [mΩ·μm 2 ] in a region of −10 kA/m to 0 kA/m, gradually decreased from 62 to 60.5 [mΩ·μm 2 ] in a region of 0 kA/m to +30 kA/m, and is about 51.6 [mΩ·μm 2 ] again in a region of +30 kA/m to +80 kA/m. When the applied magnetic field H (kA/m) is decreased from +80 kA/m to −80 kA/m, a curve nearly symmetrical to the curve obtained when the applied magnetic field H is increased is obtained with an applied magnetic field H of 0 kA/m as a centerline. 
         [0083]      FIG. 6  is a diagram for explaining change amount of magnetoresistance×element area (ΔRA) with respect to an annealing temperature. Here, the black dot, the black triangle mark, and the x mark indicate results of using CuZn, Cu 3 Al, and Ag for the spacer layer, respectively. In  FIG. 6 , a change amount of electric resistance per unit area of the element ΔRA is plotted with respect to an annealing temperature Ta. When Ag according to a conventional method is used for the spacer layer, ΔRA=8.5 [mΩ·μm 2 ] is obtained at Ta=400° C. However, when CuZn according to the present invention is used for the spacer layer, ΔRA=10.5 [mΩ·μm 2 ] which is a larger value than prior is obtained at Ta=400° C., the annealing temperature Ta is lower than prior art, and breakage of a thin film layer due to annealing at a high temperature can be prevented. 
       EXAMPLE 2 
       [0084]    In Example 2, a stacked structure similar to that in Example 1 is used, but Cu 3 Al is used as the spacer layer  14  in place of CuZn. That is, a film was formed on an MgO substrate from the bottom by a sputtering method so as to have a film configuration of Cr(10)/Ag(100)/CFGG(10)/Cu 3 Al(5)/CFGG(10)/Ag(5)/Ru(8). Subsequently, a crystal structure was examined by X-ray diffraction.  FIG. 7  is an X-ray diffraction pattern diagram of a CPPGMR element film having the stacked configuration in Example 2. When the pattern diagram is represented by 2θ in the X-ray diffraction, three sharp peaks around 39°, 41°, and 43° due to reflection on the MgO substrate are observed. A peak at 31° should be found due to reflection in a CFGG(002) direction, but is not found because of being buried in a noise. An obtuse peak around 64° is found due to reflection in a CFGG(004) direction. A peak at 43° is found due to reflection in an Ag(002) direction, an obtuse peak around 60° is found due to reflection in a Cu 3 Al(004) direction, and an obtuse peak around 64° is found due to reflection in a Cr(002) direction. Therefore, by examining a crystal structure, it has been found that each of a Cr layer, an Ag layer, a Cu 3 Al layer, and a CFGG layer is oriented in a (001) direction. 
         [0085]    In order to examine the structure of Cu 3 Al in detail, a sample of Cr(10)/Ag(10)/CFGG(5)/Cu 3 Al(20) having a thick Cu 3 Al layer was manufactured, and X-ray diffraction thereof was measured. As a result, as illustrated in  FIG. 7 , a (002) peak indicating a D 0   3  ordered structure of Cu 3 Al was not found, but it was indicated that Cu 3 Al had a disordered bcc structure. According to an equilibrium diagram, it is known that a phase of a D 0   3  type ordered structure exists in Cu 3 Al only at a high temperature. However, a thin film for CPPGMR was actually manufactured, and it was found that Cu 3 Al did not have a D 0   3  type ordered structure but was a disordered alloy having a bcc structure. 
         [0086]    Subsequently, the sample was annealed at 300 to 400° C. in a similar manner to Example 1, and then was subjected to fine processing to manufacture an element having a structure similar to that in  FIG. 4 . Change of electric resistance with respect to a magnetic field was examined. ΔRA obtained as a result of the measurement is illustrated in  FIG. 6  illustrating the result of Example 1. At an annealing temperature Ta=300° C., when Ag was used for the spacer layer, ΔRA=5.0 [mΩ·μm 2 ] was obtained, but when Cu 3 Al according to the present invention was used for the spacer layer, ΔRA=6.2 [mΩ·μm 2 ] which was a larger value than prior art was obtained. 
         [0087]    Note that the above embodiment uses an epitaxial film oriented in a (001) direction, but the crystal orientation is not limited thereto, but an epitaxial film oriented in an appropriate direction such as (110), (111), or (211) may be used. The structure of the substrate is not limited to a single crystal, but may be a polycrystal. Also in a case of the polycrystal, the crystal orientation may be oriented in an appropriate direction such as (001), (110), (111), or (211), or the crystal orientation not oriented at all may be possible. 
         [0088]    By adding a layer of an antiferromagnetic substance such as an IrMn alloy or a PtMn alloy on the upper ferromagnetic layer as a pinning layer in addition to the structure illustrated in  FIG. 1 , and suppressing magnetization reversal of the upper ferromagnetic layer by exchange anisotropy, the upper ferromagnetic layer and the lower ferromagnetic layer magnetized antiparallel can be stabilized. The pinning layer may be inserted into a portion under the lower ferromagnetic layer. 
       INDUSTRIAL APPLICABILITY 
       [0089]    The element utilizing a current-perpendicular-to-plane giant magnetoresistance (CPPGMR) effect according to the present invention is suitably used as a reading head for a magnetic disc, and can be used for detecting fine magnetic information. 
         [0000]    
       
         
               
             
               
               
               
             
           
               
                   
               
               
                 REFERENCE SIGNS LIST 
               
               
                   
               
             
             
               
                   
               
             
          
           
               
                   
                 11 
                 substrate 
               
               
                   
                 12, 12a, 12b 
                 base layer 
               
               
                   
                 13 
                 lower ferromagnetic layer 
               
               
                   
                 14 
                 spacer layer 
               
               
                   
                 15 
                 upper ferromagnetic layer 
               
               
                   
                 16a, 16b 
                 cap layer