Perpendicular magnetic recording medium

A perpendicular magnetic recording medium includes a substrate, an underlayer formed on the substrate, and containing at least one element selected from the group A consisting of Pt, Pd, Rh, Ag, Au, Ir and Fe, and at least one element or compound selected from the group B consisting of C, Ta, Mo, W, Nb, Zr, Hf, V, Mg, Al, Zn, Sn, In, Bi, Pb, Cd, SiO2, MgO, Al2O3, TaC, TiC, TaN, TiN, B2O3, ZrO2, In2O3 and SnO2, and a magnetic layer formed on the underlayer, containing at least one element selected from the group consisting of Fe, Co, and Ni, and at least one element selected from the group consisting of Pt, Pd, Au and Ir, and containing crystal grains having an L10 structure.

CROSS-REFERENCE TO RELATED APPLICATIONS

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to a perpendicular magnetic recording medium including a magnetic film suitable to high-density magnetic recording.

2. Description of the Related Art

With a recent increase in computer's processing speed, a magnetic storage device (HDD) for recording and reproducing information is required to have high speed and high density. The most popular HDD recording system at present is a longitudinal recording system in which magnetization lies in the longitudinal direction of a medium. To further increase the density, however, perpendicular magnetic recording is preferred because a demagnetizing field near the magnetization reversal boundary is small and sharp reversal magnetization is obtained. Also, thermal fluctuation, which is a problem in magnetic recording media in recent years, can be suppressed by the perpendicular medium since the film thickness of perpendicular medium can be made larger than that of longitudinal medium.

Conventionally, CoCr-based disordered alloys such as CoCrPt have been mainly studied as the material of a perpendicular magnetic film. However, since thermal fluctuation can become a future problem even in perpendicular media, a material having higher perpendicular magnetic anisotropy than those of the conventional CoCr-based materials is necessary. As promising candidates of the material, research is being extensively made on an ordered alloy in which an ordered phase is formed by a magnetic material selected from Fe, Co and Ni and a noble metal element selected from Pt, Pd, Au and Ir. In particular, FePt and CoPt as ordered alloys having an L10crystal structure have high magnetic anisotropies of 7×107and 4×107erg/cc, respectively, in the c-axis direction (<100> direction). Therefore, a perpendicular medium having a high thermal fluctuation resistance can be formed when one of these materials is used for a recording layer. Unfortunately, to use these materials as a perpendicular magnetization film, the c-axis as the easy axis of magnetization must be oriented perpendicularly to the film surface.

The following techniques are conventionally known as methods of forming a c-axis oriented film. For example, Jpn. Pat. Appln. KOKAI Publication No. 2001-189010 discloses a technique in which at least one (100)-oriented underlayer is formed between a substrate and magnetic layer. Also, Jpn. Pat. Appln. KOKAI Publication No. 11-353648 discloses a technique in which a Cr alloy underlayer containing Cr and Ti or the like is formed. Relatively good perpendicular magnetization films are obtained by this technique.

To allow an ordered alloy to achieve high magnetic anisotropy, however, it is generally necessary to be annealed at several hundred degrees during or after film deposition. This annealing increases the size of crystal grains and hence increases the magnetic cluster size, thereby making it difficult to improve recording resolution.

Accordingly, to realize a high-density perpendicular magnetic recording medium using an ordered alloy as a recording layer, it is necessary to decrease the magnetic cluster size by decreasing the crystal grain size or magnetically isolating the crystal grains in the recording layer, in addition to improving the c-axis orientation.

To magnetically isolate the crystal grains in an ordered alloy, an attempt to add a nonmagnetic element such as MgO to an ordered alloy magnetic layer has been disclosed in, for example, IEEE Transactions on Magnetics, vol. 37, No. 4, pp. 1283–1285. However, this technique is not enough to magnetically isolate magnetic grains. In addition, to order this ordered alloy, annealing at 500° C. or more after film deposition or substrate heating during film deposition is necessitated, which lowers productivity.

BRIEF SUMMARY OF THE INVENTION

It is an object of the present invention to provide a high-density perpendicular magnetic recording medium capable of providing high recording resolution by magnetically isolating magnetic grains in a magnetic film, and having high productivity and high thermal fluctuation resistance.

A magnetic recording medium according to an aspect of the present invention comprises a substrate; an underlayer formed on the substrate, and containing at least one element selected from the group A consisting of Pt, Pd, Rh, Ag, Au, Ir and Fe, and at least one element or compound selected from the group B consisting of C, Ta, Mo, W, Nb, Zr, Hf, V, Mg, Al, Zn, Sn, In, Bi, Pb, Cd, SiO2, MgO, Al2O3, TaC, TiC, TaN, TiN, B2O3, ZrO2, In2O3and SnO2; and a magnetic layer formed on the underlayer, containing at least one element selected from the group consisting of Fe, Co and Ni, and at least one element selected from the group consisting of Pt, Pd, Au and Ir, and containing crystal grains having an L10structure.

DETAILED DESCRIPTION OF THE INVENTION

FIG. 1is a sectional view of a magnetic recording medium according to an embodiment of the present invention. The magnetic recording medium shown inFIG. 1has a structure in which the seed layer21, the underlayer22, the magnetic layer3, and the protective layer4are formed on the substrate1.

FIG. 2is a sectional view of a magnetic recording medium according to another embodiment of the present invention. The magnetic recording medium shown inFIG. 2has a structure in which the seed layer21, the crystal orientation layer23, the underlayer22, the magnetic layer3, and the protective layer4are formed on the substrate1.

Note that the seed layer21and the crystal orientation layer23shown inFIGS. 1 and 2can be regarded as underlayers in a broad sense. Under the circumstances, the stacking order of the seed layer21, the crystal orientation layer23, and the underlayer22(i.e., the underlayer in the narrow sense having a specific composition defined in the present invention) is not particularly limited.

In the embodiments of the present invention, an amorphous material or a polycrystalline material such as glass or ceramics is used as a substrate. It is also possible to use a substrate obtained by depositing, e.g., a metal or ceramics on a substrate main body made of a hard material. In addition, a single-crystal substrate such as a Si, MgO, or Al2O3substrate can be used.

In the embodiments of the present invention, thin films, i.e., an underlayer and a magnetic layer are formed on the substrate. As a method for depositing a thin film, it is possible to use vacuum evaporation, sputtering, chemical vapor deposition, or laser ablation. Heating the substrate to a temperature of 200 to 500° C. during deposition of the underlayer and/or the magnetic layer is sometimes desirable because ordering of the magnetic layer progresses. Instead of heating the substrate, it is also possible to perform bias sputtering in which RF and/or DC power is applied to the substrate, or irradiation of the substrate with ions or neutral particles. These processes can be performed not only during film deposition but also after or before the film deposition.

In the embodiments of the present invention, the magnetic layer contains crystal grains having an L10structure comprising a magnetic metal element and a noble metal element as main components. The magnetic metal element is at least one element selected from the group consisting of Fe, Co and Ni, and the noble metal element is at least one element selected from the group consisting of Pt, Pd, Au and Ir. As this magnetic layer, a stacked structure of two or more magnetic layers having different characteristics can also be used. In this structure, one or both of exchange coupling interaction and magnetostatic coupling interaction can act between the stacked magnetic layers. Also, one or more nonmagnetic layers can be arranged between the two or more magnetic layers. Such a construction of the magnetic layer is chosen dependent on the magnetic characteristics required by the system or the manufacturing process.

Whether the crystal grains forming the magnetic layer have the L10structure or not can be checked by a general X-ray diffractometer. More specifically, the L10structure exists if a peak indicating a (001)- or (003)-plane is observed at an angle of diffraction matching the corresponding lattice spacing. These peaks cannot be observed in a disordered face-centered cubic lattice. The intensity of the peak indicating the (001)- or (003)-plane is satisfactory if it is observed as a significantly higher peak with respect to the background level. Also, even when a peak indicating another orientation plane such as (111) is observed, the c-axis is estimated to be oriented perpendicularly to the film surface if the peak indicating the (001)-plane is observed at higher intensity (i.e., intensity 100 times that of the other peak or higher.)

Note that, if the magnetic grain size decreases to about 10 nm and the crystal lattice coherency between adjacent magnetic grains is small, the structure sometimes looks amorphous from the result of X-ray diffraction even when the c-axis is oriented perpendicularly to the film surface. In such a case, the perpendicular orientation of the c-axis to the film surface can be checked by microstructure observation with a transmission electron microscope (TEM) or the like.

The thickness of the magnetic layer is determined by the requirement of the system. Generally, this thickness is preferably 200 nm or less, and more preferably, 50 nm or less. However, a thickness smaller than 0.5 nm is unsuitable for a magnetic recording medium because a continuous film is hard to be formed.

In the embodiments of the present invention, the underlayer reinforces the function of the magnetic layer in a magnetic recording medium. This underlayer can be formed as either a single layer film or a multilayered film.

The underlayer is made of a material mainly containing at least one element selected from the group A consisting of Pt, Pd, Rh, Ag, Au, Ir and Fe to which at least one element or compound selected from the group B consisting of C, Ta, Mo, W, Nb, Zr, Hf, V, Mg, Al, Zn, Sn, In, Bi, Pb, Cd, SiO2, MgO, Al2O3, TaC, TiC, TaN, TiN, B2O3, ZrO2, In2O3and SnO2is added.

At least one element selected from Pt, Pd, Rh, Ag, Au, Ir, Fe and Cr (the group A) as the main component of the underlayer or an alloy formed by these elements has a lattice constant close to that of the magnetic layer having an L10structure. Therefore, (100)-orientation of the crystal grains in the underlayer permits to improve the c-axis orientation of the magnetic crystals of the L10structure, making it possible to provide an excellent perpendicular magnetization film. The functions of the element or compound of the group B added to the group A element will be explained below. In the following explanation, the group B elements and compounds are classified into (1) additive elements having a high-melting point, (2) additive elements having a low melting point, and (3) compounds.

(1) In an underlayer in which at least one additive element having a relatively higher melting point is added to the group A element, the crystal grain size can be reduced. As a consequence, the crystal grain size in the magnetic layer having the L10structure can also be reduced. When the group A element and the high-melting point additive element are simultaneously deposited, the composition of the group A element and the additive element is uniform in a vapor phase. Then, these elements are condensed from the vapor phase to a solid phase on the substrate or on the film surface. At this stage, nuclei relatively high in the concentration of the high-melting point additive element are first formed dispersedly. After that, a matrix relatively high in the concentration of the group A element having a lower melting point is sequentially condensed so as to surround the nuclei. Consequently, the underlayer grows to be an inhomogeneous texture made up of a large number of columnar clusters in which the group A atoms are concentrically condensed around cores of the two-dimensionally dispersed nuclei. When such an underlayer is inserted between the substrate and the magnetic layer, the magnetic layer becomes a two-dimensionally isolated structure with reflecting the texture of the underlayer. Since the main component of the underlayer is the group A element, the lattice matching between the clusters and the magnetic crystal grains does not degrade. Therefore, it is possible to reduce the crystal grain size and to isolate the crystal grains while the c-axis orientation of the magnetic crystal having the L10structure is maintained. Of the group B elements added to the group A element, C, Ta, Mo, W, Nb, Zr, Hf, and V are preferable as the additive element having a high-melting point.

(2) In an underlayer in which at least one additive element having a relatively lower melting point is added to the group A element, the crystal grain size can be reduced. As a consequence, the crystal grain size in the magnetic layer having the L10structure can also be reduced. When the group A element and the low-melting additive element are simultaneously deposited, the composition of the group A element and the additive element is uniform in a vapor phase. Then, these elements are condensed from the vapor phase to a solid phase on the substrate or on the film surface. At this stage, a core relatively high in the concentration of the group A element having a relatively higher melting point are first condensed. After that, atoms of the low-melting point additive element are condensed mainly along the grain boundaries so as to surround the core. Consequently, the underlayer grows to be a structure formed of crystal grains of the group A element and the precipitates of the low-melting additive element in the grain boundaries. When such an underlayer is inserted between the substrate and the magnetic layer, the magnetic layer becomes a two-dimensionally isolated structure with reflecting the texture of the underlayer. Since the main component of the underlayer is the group A element, the lattice matching between the grains and the magnetic crystal grains does not degrade. Therefore, it is possible to reduce the crystal grain size and to isolate the crystal grains while the c-axis orientation of the magnetic crystal having the L10structure is maintained. Of the group B elements added to the group A element, Mg, Al, Zn, Sn, In, Bi, Pb, and Cd are preferable as the low-melting additive element.

(3) In an underlayer in which at least one compound selected from SiO2, MgO, Al2O3, TaC, TiC, TaN, TiN, B2O3, ZrO2, In2O3and SnO2is added to a group A element, the crystal grain size can be reduced. As a consequence, the crystal grain size in the magnetic layer having the L10structure can also be reduced. Since the solid solubility limit of the above compound with respect to the group A element is very small, the compound rarely forms another compound with the group A element but causes phase separation. Therefore, when the compound and the group A element are simultaneously deposited, the underlayer grows to be a structure formed of crystal grains of the group A element and the precipitates of the compound at the grain boundaries. S When such an underlayer is inserted between the substrate and magnetic layer, the magnetic layer becomes a two-dimensionally isolated structure with reflecting the texture of the underlayer. Since the main component of the underlayer is the group A element, the lattice matching between the grains and the magnetic crystal grains does not degrade. Accordingly, it is possible to reduce the crystal grain size and to isolate the crystal grains while the c-axis orientation of the magnetic crystal having the L10structure is maintained.

In the embodiments of the present invention, it is preferable that the crystal grains of the L10structure in the magnetic layer are (001)-oriented, and the crystal grains in the underlayer mainly containing the group A element are (100)-oriented. In a perpendicular magnetic recording medium, the magnetic crystal grains preferably have the L10structure in which the c-axis is oriented in the direction perpendicular to the film surface. However, not all grains need to satisfy this condition. The ratio of grains having the L10structure is preferably 60% or more, and more preferably, 80% or more.

In the embodiments of the present invention, the total molar fraction of the group B element or compound added to the group A element in the underlayer is preferably 0.1 to 50 mol %. If the molar fraction is less than 0.1 mol %, an addition effect does not appear significantly. If the molar fraction is larger than 50 mol %, the lattice matching with the magnetic layer degrades, which deteriorates the c-axis orientation.

In the embodiments of the present invention, at least one element or compound selected from the group B can be added to the magnetic layer as well as the underlayer. In this case, a similar texture to that in the underlayer is formed even in the deposition process of the magnetic layer, so that the magnetic clusters or magnetic crystal grains finer than those in the underlayer can be formed. The total molar fraction of the group B element or compound added to the magnetic layer is preferably 0.1 to 40 mol %. If the molar fraction is less than 0.1 mol %, an addition effect does not appear significantly. If the molar fraction is larger than 40 mol %, the lattice matching between the magnetic layer and underlayer degrades, which deteriorates the c-axis orientation.

In addition to the group B element or compound, Cu or the like can also be added to the magnetic layer. When only Cu is added to the magnetic layer, the effect of magnetically isolating the grains as described above cannot be obtained. However, as disclosed in Applied Physics Letters, volume 80, number 12, pp. 2147–2149, the annealing temperature required for ordering can be reduced.

In the embodiments of the present invention, a crystal orientation layer, containing Cr as a main component and at least one element selected from the group C consisting of Ti, Ni, Cu, Co and Zr to be added to Cr, can also be formed between the underlayer mainly containing the group A element and the substrate. Insertion of the crystal orientation layer mainly containing Cr improves the (100)-orientation of the underlayer mainly containing the group A element, and also improves the (001)-orientation of the magnetic layer. Accordingly, the easy axis of magnetization of the magnetic layer is advantageously oriented in the direction perpendicular to the substrate, so that more preferable characteristics as a perpendicular magnetic recording medium can be provided. The total molar fraction of the group C element added to the crystal orientation layer is preferably 1 to 50 mol %. If the molar fraction is less than 1 mol %, an addition effect does not appear significantly. If the molar fraction is larger than 50 mol %, no effect of improving orientation can be obtained.

EXAMPLES

Examples of the present invention will be described below.

In the following examples, to evaluate the degree of magnetic isolation between magnetic grains forming a magnetic layer, a Va/V ratio was evaluated. Here, Vais an activation volume of magnetization reversal and V is a crystal grain volume. The smaller the value of Va/V, the better the magnetic isolation.

The crystal grain volume V of a medium was measured with a transmission electron microscope (TEM). The following method was used to obtain an activation magnetic moment VaIsB(Va: activation volume, IsB: bulk saturation magnetization) from measurement by a vibrating sample magnetometer (VSM).

A remanence coercivity Hcris represented by
Hcr(t)=H0(1−(ln(f0t)/β)0.5),
where t is a period when a magnetic field is applied, H0is a coercivity at time zero, f0is a frequency factor (109sec), β=KuVa/kBT, Ku is magnetic anisotropy energy density, kBis a Boltzmann constant, and T is an absolute temperature. If H0meets H0=2Ku/IsB, then VaIsB=β×(2kBT)/H0.

Therefore, VaIsBcan be calculated by obtaining β and H0by fitting with respect to varioustvalues.

To adapt normal VSM measurement results to this method, coercivity values were measured by changing a sweep rate tswp, and the resultant coercivity values Hc(tswp) were converted into remanence coercivity values Hcr(t). This conversion was performed by solving an equation disclosed in a reference (M. P. Sharrock: IEEE Trans. Magn. 35 p. 4414 (1999)) in a self-consistent manner. The activation volume Vawas calculated by assuming that IsBwas 800 emu/cc in the resultant VaIsBvalue.

In the examples, the state of magnetic isolation was evaluated by classifying the value of Va/V into the following six grades.

A: 1.0 or more, and less than 2.0B: 2.0 or more, and less than 2.5C: 2.5 or more, and less than 3.0D: 3.0 or more, and less than 3.5E: 3.5 or more, and less than 5.0F: 5.0 or more

In this example, a magnetic recording medium shown inFIG. 1was fabricated.

A glass disk substrate was used as a substrate1, and an NiAl layer about 10 nm thick was formed as a seed layer21.

An underlayer22was formed to have a thickness of about 20 nm by using a material comprising Pt, Pd, Rh, Ag, Au, Ir or Fe of a group A element as a matrix material and 0 to 60 mol % of C, Ta, Mo, W, Nb, Zr, Hf, V, Mg, Al, Zn, Sn, In, Bi, Pb, Cd, SiO2, MgO, Al2O3, TaC, TiC, TaN, TiN, B2O3, ZrO2, In2O3or SnO2of a group B element or compound added to the matrix material.

An FePt layer about 10 nm thick was formed as a magnetic layer3, and a carbon layer about 10 nm thick was formed as a protective layer4.

The magnetic recording medium of this example was fabricated by the following method. A vacuum chamber of a sputtering apparatus was evacuated to 2×10−5Pa or less, and then film deposition was performed under an Ar atmosphere at 5 Pa. During the film deposition, the substrate was heated to 300° C. by an infrared heater. To deposit the seed layer21, the magnetic layer3and the protective layer4, Ni50Al50, Fe50Pt50and C were used as targets, respectively. To deposit the underlayer22, a composite target of the group A element and group B element or compound was used. The composition of the group B element or compound was adjusted by changing the composition of the target. The applied power to each target was set to 100 W, and the films were deposited through DC or RF magnetron sputtering.

Tables 1 and 2 show the results of media each having an underlayer containing only a group A element (no group B element or compound was added), and media each having an underlayer in which the amount of a group B element or compound was set to 10 mol % with respect to a group A element.

As shown in Tables 1 and 2, each medium having an underlayer containing only a group A element (no group B element or compound was added) had a high Va/V value (classification F), indicating a small degree of magnetic isolation between the magnetic grains in the magnetic layer. In contrast, each medium having an underlayer in which 10 mol % of a group B element or compound was added to a group A element had a low Va/V value, indicating that magnetic isolation between the magnetic grains was improved.

FIG. 3and Table 3 show the relationship between the amount of group B element or compound and Va/V for a medium having an underlayer represented by Pt—X (X is a group B element or compound).FIG. 4and Table 4 show the relationship between the amount of group B element or compound and Va/V for a medium having an underlayer represented by Pd—X (X is a group B element or compound).

In each medium using Pt—X or Pd—X as an underlayer, the Va/V value significantly reduced when the addition amount of a group B element or compound was 0.1 mol % or more, indicating a remarkable effect on magnetic isolation between the magnetic grains forming the magnetic layer.

TABLE 3Relationship between amount of X elementto Pt—X underlayer and Va/VAdditionamountCTaMoWNbSiO2MgOAl2O3None010.30.133.83.634.34.244.60.52.83.53.62.83.43.633.912.32.83.22.42.92.92.92.962.22.42.82.12.42.82.52.6102.32.12.322.42.52.42.3202.22.22.42.12.52.22.22.3302.22.22.32.12.42.422.34022.12.122.22.322.22.1501.8221.92.222.22.1601.72222.22.22.42.2

TABLE 4Relationship between amount of X elementto Pd—X underlayer and Va/VAdditionamountCTaMoWNbSiO2MgONone012.20.13.643.83.23.94.24.50.52.63.83.12.63.74412.332.72.43.23.63.962.32.82.42.22.92.93.1102.32.32.52.32.42.32.6202.42.32.42.32.42.42.2302.32.42.52.22.52.42.3402.12.32.52.32.42.52.2502.22.32.42.22.32.32.2602.22.42.32.12.42.22.1

The XRD profile of a medium having a PtTa underlayer was measured to obtain (111) reflection and (001) reflection of each of FePt and Pt, thereby calculating integrated intensity ratios IFePt(111)/IFePt(001)and IPt(111)/IPt(100).FIG. 5and Table 5 show the relationships between the amount of Ta to the PtTa underlayer and the integrated intensity ratios.

As is apparent fromFIG. 5and Table 5, the integrated intensity ratio of each of FePt and Pt abruptly increased and the perpendicular orientation deteriorated when the Ta amount to the underlayer exceeded 50 mol %. The same tendency was found in a medium using an underlayer made of a combination of another matrix material and an additive element.

From the above results, to promote magnetic isolation between the magnetic crystals in the magnetic layer made of an ordered alloy, it is preferable to use an underlayer which contains a group A element as a matrix material and 0.1 mol % or more of a group B element or compound added to the matrix material. To fabricate a perpendicular magnetic recording medium, the upper limit of the addition amount of a group B element or compound to the underlayer is preferably set to 50 mol %.

A magnetic recording medium shown inFIG. 1was fabricated in this Example.

A glass disk substrate was used as a substrate1, and an MgO layer about 10 nm thick was formed as a seed layer21.

An underlayer22was formed to have a thickness of about 20 nm by using a material comprising Pt or Pd of a group A element as a matrix material and 10 mol % of C, Ta, Mo, W, Nb, SiO2, MgO or Al2O3of a group B element or compound added to the matrix material.

A magnetic layer3was formed to have a thickness of about 5 nm by using a material comprising FePt as a main component and 0 to 50 mol % of C, Ta, Mo, W, Nb, SiO2, MgO or Al2O3added to the main component.

A carbon layer about 10 nm thick was formed as a protective layer4.

The Va/V values of magnetic recording media each having an underlayer in which the addition amount of a group B element or compound (C, Ta, Mo, W, Nb, SiO2, MgO, or Al2O3) was 10 mol % with respect to a group A element (Pt or Pd), and an FePt—X magnetic layer in which the addition amount of a group B element or compound X (X is C, Ta, Mo, W, Nb, SiO2, MgO, or Al2O3) was 10 mol %, were evaluated following the same procedures as in Example 1. As a consequence, the evaluation of the Va/V value of each medium was class A or B, indicating that magnetic isolation further improved by the addition of a group B element or compound to the magnetic layer in addition to the underlayer.

FIG. 6and Table 6 show the relationship between the amount of each group B element or compound to the magnetic layer and Va/V in a medium having a Pt—20% MgO underlayer and a magnetic layer represented by FePt—X (X is C, Ta, Mo, W, Nb, SiO2, MgO, or Al2O3).

In each medium, the Va/V value significantly reduced when the addition amount of a group B element or compound to the magnetic layer containing FePt as a main component, formed on the underlayer containing a group A element and a group B element or compound, was 0.1 mol % or more. This indicates that magnetic isolation between the magnetic grains in the magnetic layer further improved.

TABLE 6Relationship between amount of X element to FePt—Xmagnetic layer on Pt-20% MgO underlayer and Va/VAdditionamountCTaMoWNbSiO2MgOAl2O3None020.11.81.91.81.71.81.81.81.80.51.71.91.81.71.81.81.71.811.441.81.71.411.71.81.61.861.411.451.551.41.561.71.31.8101.451.441.51.441.41.71.41.7201.441.431.541.411.431.441.51.51301.431.441.521.451.41.421.41.52351.421.441.581.441.451.441.41.5401.41.411.531.431.421.431.41.51451.451.411.521.41.41.451.31.52501.381.41.561.31.341.41.31.41

TABLE 7Relationship between amount of X element to FePt—Xmagnetic layer on Pt-10% W underlayer and Va/VAdditionamountCTaMoWNbSiO2MgOAl2O3None020.11.81.71.81.81.81.81.81.810.51.51.51.71.51.71.81.81.6211.31.41.71.41.71.81.61.7161.41.31.71.41.51.61.61.6101.31.41.451.31.451.51.41.45201.31.31.411.31.461.41.331.47301.31.31.411.31.511.41.461.52351.41.31.441.41.531.51.321.45401.31.31.431.31.451.61.351.45451.31.41.411.41.461.61.341.45501.21.41.421.31.411.561.31.4

TABLE 8Relationship between amount of X element to FePt—Xmagnetic layer on Pt-10% Ta underlayer and Va/VAdditionamountCTaMoWNbSiO2MgOAl2O3None02.10.11.61.71.81.71.71.81.81.80.51.31.51.71.61.71.71.61.811.31.41.51.51.71.71.61.861.31.41.51.31.551.51.41.7101.41.31.41.31.511.51.31.57201.31.41.41.31.41.41.31.51301.41.41.41.41.51.41.31.54351.51.31.41.31.51.51.41.52401.41.31.41.41.41.41.41.51451.31.41.41.31.41.41.41.5501.31.31.31.31.41.41.41.46

TABLE 9Relationship between amount of X element to FePt—Xmagnetic layer on Pt-6% C underlayer and Va/VAdditionamountCTaMoWNbSiO2MgOAl2O3None02.20.11.71.71.81.81.91.91.81.80.51.51.61.71.71.61.81.61.611.31.51.51.61.51.81.51.561.31.31.41.51.51.81.41.4101.31.41.41.41.51.41.41.4201.41.31.51.41.41.41.31.3301.41.31.41.41.51.51.41.4351.41.31.51.41.51.41.31.3401.41.41.41.41.41.41.31.3451.41.41.41.41.31.41.31.3501.41.31.31.41.31.31.21.2

TABLE 10Relationship between amount of X element to FePt—Xmagnetic layer on Pt-20% SiO2underlayer and Va/VAdditionamountCTaMoWNbSiO2MgOAl2O3None02.20.11.81.71.91.71.91.91.81.80.51.61.61.71.51.81.91.81.711.51.41.61.41.81.91.71.761.41.41.41.31.81.51.71.6101.51.31.41.41.51.51.71.4201.51.31.51.41.561.31.41.4301.41.31.41.31.61.351.41.3351.41.41.41.31.581.361.41.3401.41.41.41.41.551.421.51.4451.31.21.21.31.541.351.41.4501.21.21.41.21.31.31.31.4

TABLE 11Relationship between amount of X element to FePt—Xmagnetic layer on Pt-10% Mo underlayer and Va/VAdditionamountCTaMoWNbSiO2MgOAl2O3None02.30.11.71.81.91.721.881.891.881.90.51.61.71.91.711.811.881.871.9111.51.51.81.441.511.871.841.8561.41.31.41.311.511.861.781.82101.51.31.31.31.51.581.361.64201.41.41.41.31.421.311.331.42301.41.31.41.311.51.381.321.48351.51.31.41.321.51.341.321.51401.41.31.31.361.461.41.311.47451.31.31.31.321.431.391.31.46501.21.31.21.291.351.371.321.45

TABLE 12Relationship between amount of X element to FePt—Xmagnetic layer on Pt-20% Al2O3underlayer and Va/VAdditionamountCTaMoWNbSiO2MgOAl2O3None02.30.11.91.851.881.791.911.871.841.910.51.681.821.861.731.91.861.821.911.611.741.561.441.881.811.741.7861.421.711.511.311.841.791.71.77101.411.421.421.31.581.781.641.71201.41.321.461.371.361.61.421.54301.481.31.451.321.381.441.441.31351.461.321.411.361.31.411.411.37401.431.311.41.351.341.481.41.34451.41.371.41.341.331.431.351.32501.381.341.371.321.321.381.341.29

TABLE 13Relationship between amount of X element to FePt—Xmagnetic layer on Pt-60% Nb underlayer and Va/VAdditionamountCTaMoWNbSiO2MgOAl2O3None02.40.11.751.781.871.741.771.871.881.90.51.581.771.741.671.641.861.841.8711.411.721.711.421.611.851.831.8661.41.651.641.341.421.791.81.54101.391.351.541.331.331.541.671.44201.381.321.421.31.321.461.371.4301.451.391.471.361.351.441.341.45351.471.381.51.351.341.411.391.45401.441.411.441.341.331.471.391.46451.451.451.461.311.361.431.341.39501.431.411.451.321.351.41.331.35

TABLE 14Relationship between amount of X element to FePt—Xmagnetic layer on Pt-20% MgO underlayer and Va/VAdditionamountCTaMoWNbSiO2MgONone02.20.11.891.91.881.911.931.91.920.51.641.841.871.91.841.891.8911.621.741.781.551.741.881.8361.541.721.641.441.651.871.81101.511.461.521.421.531.81.74201.581.411.51.41.561.541.44301.561.41.571.51.511.521.42351.581.541.581.481.511.561.45401.591.521.541.471.51.511.41451.541.51.511.461.491.491.4501.51.481.491.441.441.471.32

TABLE 15Relationship between amount of X element to FePt—Xmagnetic layer on Pt-6% W underlayer and Va/VAdditionamountCTaMoWNbSiO2MgONone02.20.11.91.841.881.731.881.891.910.51.641.631.841.641.851.881.8711.521.521.751.441.781.841.8561.441.441.621.431.741.791.64101.41.431.541.411.551.641.54201.481.421.571.471.571.541.46301.421.421.531.481.511.521.43351.471.411.511.441.51.51.4401.491.41.561.41.561.491.45451.51.431.511.411.511.481.42501.431.441.491.391.491.41.4

TABLE 16Relationship between amount of X element to FePt—Xmagnetic layer on Pt-10% SiO2underlayer and Va/VAdditionamountCTaMoWNbSiO2MgONone02.30.11.91.951.841.891.881.841.910.51.841.741.751.661.871.811.911.621.541.641.571.741.751.7461.441.511.571.441.71.731.59101.411.441.541.41.51.61.44201.481.421.51.411.561.421.43301.491.411.571.451.531.41.4351.521.481.541.461.521.411.41401.441.471.521.451.531.41.42451.411.421.51.461.51.421.4501.391.41.491.451.461.371.38

TABLE 17Relationship between amount of X element to FePt—Xmagnetic layer on Pt-6% C underlayer and Va/VAdditionamountCTaMoWNbSiO2MgONone02.30.11.911.841.821.881.921.871.880.51.721.721.71.861.91.861.8811.61.681.641.811.841.851.8161.431.621.521.741.741.771.8101.41.431.461.531.541.521.43201.471.451.411.511.511.511.42301.451.421.41.541.561.51.4351.411.411.451.551.551.511.45401.531.41.431.521.521.51.42451.461.41.421.51.511.51.43501.41.371.381.481.431.491.4

TABLE 18Relationship between amount of X element to FePt—Xmagnetic layer on Pt-10% Ta underlayer and Va/VAdditionamountCTaMoWNbSiO2MgONone02.30.11.911.841.911.871.881.911.870.51.841.791.841.811.871.91.8411.721.541.811.541.721.881.8161.541.51.641.431.511.641.52101.531.421.421.321.441.521.44201.51.411.461.311.421.431.3301.571.41.431.381.471.461.36351.541.431.41.41.451.441.34401.521.461.451.371.451.421.33451.51.471.421.351.431.451.3501.471.441.41.31.421.441.31

TABLE 19Relationship between amount of X element to FePt—Xmagnetic layer on Pt-6% Mo underlayer and Va/VAdditionamountCTaMoWNbSiO2MgONone02.40.11.741.791.91.841.781.891.90.51.521.711.821.81.741.881.8511.441.431.711.471.651.871.8161.411.341.631.321.521.531.76101.451.311.41.31.441.341.43201.431.31.411.321.431.321.32301.461.351.451.351.461.341.31351.451.361.421.311.471.351.31401.451.351.451.341.461.351.3451.411.341.461.311.441.351.3501.41.331.341.291.431.321.25

TABLE 20Relationship between amount of X element to FePt—Xmagnetic layer on Pt-10% Nb underlayer and Va/VAdditionamountCTaMoWNbSiO2MgONone02.40.11.811.871.781.741.871.871.880.51.721.841.751.641.811.851.8711.621.821.721.531.641.841.8461.531.641.631.421.611.71.82101.511.431.521.421.541.621.54201.551.421.51.411.561.541.43301.51.541.511.41.511.541.42351.511.521.571.41.561.51.41401.521.51.561.41.551.521.4451.51.431.511.451.511.561.4501.471.41.431.381.51.51.38

The XRD profile of a medium having a Pt-20% MgO underlayer and FePtTa magnetic layer was measured to obtain (111) reflection and (001) reflection of each of FePt and Pt, thereby calculating integrated intensity ratios IFePt(111)/IFePt(001)and IPt(111)/IPt(100).FIG. 21and Table 21 show the relationships between the Ta addition amount to the magnetic layer and the integrated intensity ratios.

As can be seen fromFIG. 21and Table 21, the integrated intensity ratio of FePt abruptly increased when the Ta addition amount to the underlayer exceeded 40 mol %, and the perpendicular orientation deteriorated.

From the above results, to promote magnetic isolation between the magnetic crystals forming the magnetic layer made of an ordered alloy, it is preferable to use an underlayer containing a group A element and a group B element or compound, and a magnetic layer to which 0.1 mol % or more of a group B element or compound is added. Also, to fabricate a perpendicular magnetic recording medium, the upper limit of the addition amount of a group B element or compound to the magnetic layer is preferably set to 40 mol %.

In this example, a magnetic recording medium shown inFIG. 2was fabricated.

A glass disk substrate was used as a substrate1, and an NiAl layer about 10 nm thick was formed as a seed layer21.

A crystal orientation layer23was formed to have a thickness of about 20 nm by using a material comprising Cr and 0 to 60 at % of Ti, Ni, Co, Cu or Zn added to Cr.

An underlayer22was formed to have a thickness of about 5 nm. The underlayer comprises Pt (the group A) and 20 mol % of SiO2(the group B).

A magnetic layer3was formed to have a thickness of about 5 nm. The magnetic layer comprises Fe45Pt50Cu5ternary alloy and 6 at % of Mo added thereto.

A carbon layer about 10 nm thick was formed as a protective layer4.

The XRD profile of each of media having various Cr—X crystal orientation layers (X was Ti, Ni, Co, Cu, or Zn) with different amount of the additive element was measured. Then, (111) reflection and (001) reflection of each of FePt and Pt were measured to calculate the integrated intensity ratios IFePt(111)/IFePt(001)and IPt(111)/IPt(100).FIG. 22and Table 22 show the relationships between the addition amount of each additive element to the crystal orientation layer23and the integrated intensity ratios. InFIG. 22and Table 22, Ti(Pt), for example, means that Ti is an additive element and Pt is a measuring object in the integrated intensity ratio.

FIG. 22and Table 22 reveal that the perpendicular orientation significantly improved when the amount of an additive element to the crystal orientation layer23was 1 to 50 mol %. Note that, the evaluation of the Va/V values of all the media were A.

As described above, insertion of the crystal orientation layer in which 1 to 50 mol % of Ti, Ni, Co, Cu or Zn are added to Cr is more preferable since magnetic isolation of the magnetic grains in the magnetic layer and the perpendicular orientation improve.