JP2008077765A - Anti-ferromagnetic coupling soft base layer - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a perpendicular magnetic recording medium including an anti-ferromagnetic coupling soft base layer. <P>SOLUTION: In the magnetic recording medium including a first magnetic layer, a spacer layer and a second magnetic layer in this order, the spacer layer includes a non-magnetic layer; the thickness of the spacer layer is selected so that anti-ferromagnetic coupling is established between the first and the second magnetic layers and both thicknesses of the first and the second magnetic layers are thinner than a critical thickness for forming stripe domains in the magnetic layers. <P>COPYRIGHT: (C)2008,JPO&INPIT

Description

  The present invention relates to a perpendicular recording medium such as a thin film magnetic recording disk having perpendicular recording, and a method of manufacturing the medium. The embodiment of the present invention is particularly applicable to a perpendicular magnetic recording medium having a soft base layer antiferromagnetically coupled.

  Perpendicular magnetic recording systems have been developed for computer hard disk drives because they provide a higher linear density than horizontal recording. Kanu G. FIG. 1, taken from page 322 of Ashar's “Magnetic Disk Drive Technology (1997)”, shows the magnetic bits and transitions in perpendicular and horizontal magnetic recording. In the case of horizontal recording, a demagnetizing field exists between the two magnetic bits. These demagnetizing fields try to pull the bits apart and create a transition space between the bits. That is, the transition parameter a shown in FIG. At very high bit densities, the length of the transition region becomes a limiting parameter. Since the perpendicular recording bits do not face each other, they can be written close to each other as shown in FIG.

  A typical perpendicular recording head is Kanu G. et al. As shown in FIG. 2, taken from page 323 of “Magnetic Disk Drive Technology (1997)” by Ashar, as shown in FIG. 2, the trailing (reading) read / write pole, its read / write pole and magnetic A conductive magnetizing coil that surrounds the yoke of the leading (leading) return pole or counter pole and write pole of the joint. As shown in FIG. 2, the perpendicular recording medium includes a magnetic medium and a base layer. The magnetic media can be a hard magnetic recording layer containing perpendicularly oriented magnetic domains, and the base layer enhances the magnetic field of the recording head and creates a magnetic path from the trailing write pole of the writing means to the leading or opposing pole. The soft magnetic base layer provided may be used. The magnetic flux passes through the hard magnetic recording track from the tip of the write pole, enters the soft base layer (SUL), and reaches the opposite pole. Such perpendicular recording media also includes a thin film intermediate layer between the hard recording layer and the soft base layer to prevent exchange interaction between the hard layer and the soft layer. The soft substrate is also useful for read operations. During the read back operation, the soft substrate generates a mirror image of the magnetic charge in the magnetic hard layer, equivalently increasing the magnetic flux from the media. This provides a higher playback signal.

  The soft base layer is located below the recording layer and forms a mirror image of the recording head. Along with the image head, each recording event essentially involves two heads. Along with this, the net recording magnetic field becomes much larger than the magnetic field generated by the horizontal head. The magnetic flux flows from the head through the SUL to the return pole and crosses the recording layer twice. The return pole is generally much wider than the write pole and dilutes the magnetic flux density returning through the recording layer. Nevertheless, writing may occur at the return pole. In that case, data is partially erased not only on the track to be recorded but also on the adjacent track, and data stored in the recording layer may be accidentally erased. The quality of the image, and the effectiveness of the soft base according to it, and the erasure of data, both depend on the permeability of the soft base. Thus, there is a need for perpendicular recording media having a soft base layer that forms a good mirror image of the recording head without erasing the data in the recording layer.

  The embodiments of the present invention are directed to a perpendicular recording medium having a SUL structure of an SUL design that is antiferromagnetically coupled. According to this design, the magnetic permeability of the SUL can be adjusted regardless of the saturation magnetization of the SUL, and therefore erasure of the recording layer can be essentially prevented without sacrificing the write function.

  As will be apparent, the invention is capable of other and different embodiments, and its details are capable of modifications in various obvious respects, all without departing from the invention. Accordingly, the drawings and descriptions are to be construed as illustrative in nature and not as restrictive.

  Perpendicular recording media can include ferromagnetic and antiferromagnetic coupling in the soft magnetic base layer of the perpendicular recording media. The preferred embodiment of the present invention provides antiferromagnetic coupling in the soft magnetic base layer of perpendicular recording media. Embodiments of the present invention are particularly suitable for use in a magnetic disk recording system having a recording head having a head capable of performing read and / or write operations. Ferromagnetic coupling generally refers to indirect coupling between ferromagnetic layers or multilayer structures such that adjacent ferromagnetic layers or multilayer structures have magnetizations that generally point in the same direction. Antiferromagnetic coupling generally refers to indirect coupling between ferromagnetic layers or multilayer structures where adjacent ferromagnetic layers or multilayer structures generally have magnetizations that point in opposite directions.

AF coupling was evaluated by measuring the exchange energy density _Jex of the system, which represents the strength of the antiferromagnetic coupling between the two magnetic layers. In an embodiment of the present invention, adjacent ferromagnetic layers or multilayer structures, such as adjacent ferromagnetic layers or multilayer structures, when J _ex is greater than zero erg / cm ² between ferromagnetic layers or multilayer structures. There exists antiferromagnetic coupling between ferromagnetic layers or multilayer structures.

  The preferred embodiment of the perpendicular media of the present invention allows the SUL permeability to be adjusted independently of the saturation magnetization of the SUL, thereby erasing data in the magnetic layer without sacrificing write performance. Can be essentially prevented. If the strength of the RKKY interaction between the magnetic layers in the SUL is changed, the permeability of the SUL automatically changes (if the interaction is increased, the permeability is reduced). The decrease in permeability may reduce write performance, but at the same time reduces erasure. Therefore, there will be an optimum point at which erasure can be significantly reduced without significantly reducing write performance. Thus, changing the permeability is one way to optimize media performance by changing the erase and write performance.

  Embodiments of the present invention provide a magnetic recording medium suitable for achieving a high area recording density exhibiting a high SMNR. Embodiments of the present invention achieve such technical features by forming a soft base layer. “Soft magnetic material (soft magnetic material)” refers to a material that can be easily magnetized and demagnetized. Compared to a soft magnetic material, a “hard magnetic (hard magnetic material)” material refers to a material that cannot be easily magnetized or demagnetized.

  The base layer is “soft” because it contains the soft magnetic material defined above and is called “base layer” because it is located below the recording layer. In a preferred embodiment, the soft base layer is amorphous. The term “amorphous” means that the material of the base layer does not show a sharp sharp peak in the X-ray diffraction pattern compared to background noise. The “amorphous soft base layer” of the embodiment of the present invention is not limited to the microcrystal contained in the amorphous phase or other materials of the material unless the material exhibits a sharp sharp peak compared to the background noise in the X-ray diffraction pattern. Includes form.

  When a soft base layer is formed on a disk substrate by magnetron sputtering, there are several competing components that determine the net anisotropy of the base layer. They are the effects of the magnetron magnetic field, the magnetostriction of the film and the stress due to the shape of the substrate, etc. The first and second soft magnetic base layers can be made as a single layer or as multiple layers.

  The soft magnetic layer is deposited from a target material produced by a gas spray powdered alloy process (AP) or a molten raw material casting using a mold at temperatures from 1200 to 1550 ° C. and then solidified into an ingot. Can be formed. The ingot is then preheated in an annealing furnace to a temperature between 850 and 1200 ° C. suitable for rolling to a desired thickness for final processing to the correct target dimensions.

  The seed layer is a layer sandwiched between the substrate and the base layer. A suitable seed layer will also control the anisotropy of the soft base layer by facilitating the formation of microstructures that exhibit either short-range order or different magnetostriction affected by the magnetron field. The seed layer can also change local stresses in the soft base layer.

  In the base layer of the perpendicular recording medium according to the embodiment of the present invention, it is preferable that the easy axis of magnetization is in an axial direction that intersects the moving direction of the magnetic head. This means that the easy magnetization axis is more oriented in the moving direction of the read / write head than in the moving direction. Further, it is preferable that the base layer of the perpendicular recording medium has an essentially radial or horizontal anisotropy, which means that the soft magnetic material domain of the base layer intersects the moving direction of the read / write head rather than the moving direction. It means that it is more oriented in the axial direction. In one embodiment, the axial direction that intersects the moving direction of the read / write head is the axial direction that intersects the substrate surface of the recording medium.

  According to an embodiment of the present invention, the substrate used in the embodiment of the present invention may be glass, glass ceramic, NiP / aluminum, metal alloy, resin / polymer material, ceramic, glass polymer, composite material or Includes other non-magnetic materials. Glass-ceramic materials usually do not exhibit a crystalline surface. Glass and glass-ceramics are generally highly resistant to impact.

  A preferred embodiment of the present invention is a perpendicular recording medium comprising at least two amorphous soft base layers and a spacer layer between the base layer and the recording layer. The amorphous soft base layer should preferably contain a soft magnetic material and the recording layer should preferably contain a hard magnetic material. The amorphous soft base layer is relatively thick compared to the other layers. All layers between the amorphous soft base layer and the recording layer are called intermediate layers. The intermediate layer can include one or more layers of non-magnetic material. The purpose of the intermediate layer is to prevent interaction between the amorphous soft magnetic base layer and the recording layer. The intermediate layer may also enhance the desired properties of the recording layer. The horizontal recording medium does not have an amorphous soft magnetic base layer. Therefore, a layer called “base layer”, “seed layer”, “sub-seed layer” or “buffer layer” in the case of horizontal media corresponds to an intermediate layer of vertical media.

  The base layer and the magnetic recording layer can typically be continuously sputter deposited on the substrate in an inert gas atmosphere by magnetron sputtering. Typically, the carbon coating is deposited in argon with nitrogen, hydrogen or ethylene. Conventional topcoats for lubrication are typically thinner than about 20 angstroms.

  The seed layer, which can optionally be added as a layer sandwiched between the substrate and the soft base layer, promotes the formation of microstructures that exhibit either short-range order or different magnetostriction under the influence of a magnetron magnetic field, The anisotropy of the soft base layer may be controlled. The seed layer can also change local stresses in the soft base layer.

  An amorphous soft base layer produces a smoother surface than a polycrystalline base layer. Therefore, the amorphous soft base layer is one method for reducing the surface roughness of a magnetic recording medium for high density perpendicular magnetic recording. Amorphous soft base layer materials include base layers containing Cr-doped Fe alloys. Here, the Fe alloy includes CoFeZr, CoFeTa, FeCoZrB, and FeCoB.

  The advantage of using an amorphous material as the soft base material is that it lacks long-range order in the amorphous material. Due to the lack of long range order, amorphous alloys exhibit essentially no magnetic crystal structure anisotropy. Using an amorphous soft base layer is one way to reduce noise due to rippled domains and surface roughness. The surface roughness of the amorphous soft base layer is preferably less than 1 nm, more preferably less than 0.5 nm, and optimally less than 0.3 nm.

  In accordance with a preferred embodiment of the present invention, a test method for determining a plurality of different parameters is as follows. If a particular test method for determining a parameter is not explicitly presented below, conventional methods known to those skilled in the art can be used to determine that parameter.

  Write performance: In a preferred embodiment of the present invention, the preferred range of write performance includes a high value.

Residual magnetism: In a preferred embodiment of the present invention, the preferred range of saturation magnetization is 0.3-1 memu / cm ² , more preferably 0.4-0.7 memu / cm ² .

Magnetostriction λ _s : In the preferred embodiment of the present invention, the preferred range of λ _s depends on the SUL component. For example, as the boron content increases from about 8 to 12%, λ _s (× 10 ⁻⁵ ) changes from about 5.2 to 4.4.

  Stress σ: In the preferred embodiment of the present invention, the preferred range of σ depends on the sputtering conditions. For example, as the sputtering pressure increases from about 2 to 12 mTorr, σ varies from about −400 to about 800 MPa, and decreases to about 400 MPa as the sputtering pressure further increases to about 15 mTorr. In this regard, the July 2001 magazine IEEE Trans. Magn. Volume 37, pages 2302-2304, C.I. L. Platt, M.M. K. Minor, T .; J. et al. See Klemmer's paper "Magnetic and structural properties of FeCoB thin films".

  Stripe domain: Since this is a noise source, the SUL should be without a stripe domain. Strip domain refers to a stripe structure in an optically smooth SUL film without it. The strip domain is measured by a magnetic force microscope (MFM) using a soft magnetic tip magnetized perpendicular to the sample surface.

J _ex : exchange energy density, which represents the strength of the RKKY interaction. In the present _invention, a suitable value of _{J ex} is greater than zero erg / cm ^2, more preferably greater than 2 erg / cm ^2. More preferably, it is between 0 and 0.5 erg / cm ² . More preferably, it is between 0 and 0.2 erg / cm ² .

  Signal to Media Noise Ratio (SMNR): In the preferred embodiment of the present invention, the preferred range of SMNR includes high values.

  Reverse Overwrite (revOW): In the preferred embodiment of the present invention, the preferred range of revOW includes a high value.

  Erasing: In the preferred embodiment of the present invention, the preferred range of erasing includes low values.

  A preferred embodiment of the perpendicular recording medium of the present invention is shown in FIG. The layer structure of the preferred embodiment is as follows. Substrate, adhesive layer (1), anti-ferromagnetically coupled (AFC) soft base layer (2), nonmagnetic intermediate layer (3), recording layer (4) and carbon layer (5). Preferably, the AFC soft base layer includes a first soft base layer, a spacer layer, and a second soft base layer. The protective carbon layer 5 generally covers the magnetic recording layer 4.

  The adhesive layer can include Cr, CrTi, Ti and NiNb, among other materials for promoting adhesion. The thickness of the adhesive layer 1 is in the range of about 0.5 nm, preferably in the range of about 10 nm.

  The antiferromagnetically coupled soft base layer (AFC SUL) includes at least two ferromagnetic layers (FML) that are antiferromagnetically coupled with the nonmagnetic spacer layer (SL) interposed therebetween.

AFC SUL can take several different structures:
(1) FML / SL / FML (SL thickness is adjusted to achieve antiferromagnetic coupling between FMLs)
(2) FML / IFL / SL / FML or FML / SL / IFL / FML or FML / IFL / SL / IFL / FML (the interface layer IFL is for strengthening antiferromagnetic coupling between FMLs) (SL Is adjusted to achieve antiferromagnetic coupling between FMLs)
(3) FML / IFL / n × [SL / IFL / FML] (n = 2-20) (SL thickness is adjusted to achieve antiferromagnetic coupling between FMLs) (IFL is May or may not be)
_{(4) FML 1 / IFL /} n × [SL i / IFL / FML i + 1] (n = 2-20) ( _{Example: FML 1 / SL 1 / FML} 2 / SL 2 / FML 3 / SL 3 / FML 4. ..) (SL _i thickness can vary between 0-2.5 to achieve the full range of coupling between FML _i , where at least one SL _i is FML _i and FML adjusted to achieve antiferromagnetic coupling with _{i + 1} ) (IFL may or may not be present)
(5) FML ₁ / IFL / n × [SL _i / IFL / FML _{i + 1} ] (n = 2-20) (Example: FML ₁ / SL ₁ / FML ₂ / SL ₂ / FML ₃ / SL ₃ / FML ₄ . ..) (SL _{i has} a thickness of antiferromagnetic coupling between FML _i and FML _{i + 1} , J _ex (i) is weak near layer 4 and strong near the substrate throughout the AFC SUL (The IFL may or may not be adjusted.) Some of the embodiments of the structure of the AFC SUL are shown in FIGS. 4 (a)-(d).

  The ferromagnetic soft base layer is selected from a group including Fe including one or more elements selected from Co, B, P, Si, C, Zr, Nb, Hf, Ta, Al, Si, Cu, Ag, and Au. Alloy materials may be included. The thickness of the first and second soft magnetic base layers (FML) is preferably in the range of 5-400 nm, and more preferably in the range of about 40-150 nm.

When magnetostriction λ _s and stress σ in FML are large, vertical anisotropy occurs (because K _u = 3 / 2λ _s σ, where K _u represents uniaxial anisotropy) Note that if the thickness of the FML exceeds some criticality, it triggers the formation of stripe domains. In the course of the present invention, it has been found that antiferromagnetic coupling between FMLs suppresses the formation of stripe domains in FML. Furthermore, it has been observed that the critical thickness of FML, ie, the thickness at which stripe domains are formed in FML, increases with increasing antiferromagnetic coupling strength.

  The spacer layer can include almost any nonmagnetic component, but can include Ru, Rh, Ir, Cr, Cu, Re, V, and alloys thereof. The thickness of the spacer layer is in the range of about 0.1-2.5 nm, more preferably in the range of about 0.3-1 nm.

The interface layer (IFL) can include Co, Fe, B, P, Si, C, Zr, Nb, Hf, Ta, Al, Si, Cu, Ag, Au, and alloys thereof. The saturation magnetism of this layer should preferably be at least 800 emu / cm ³ . The thickness of the interface layer is in the range of about 0.1-10 nm, preferably in the range of about 0.5-2 nm.

  The intermediate layer should preferably trigger the growth of the recording layer. For example, this layer comprises one or more layers having the fcc or / and hcp crystal structure and having the following composition: One or more elements are selected from Ru, Re, Ir, Cu, Ag, Au, Zr, Hf, Pr, Pd and Ti, and from a group including W, Mo, Ta, Nb, Cr and V Contains a small amount of selected bcc structure elements. The thickness of the intermediate layer is in the range of about 0.2-40 nm, preferably in the range of about 4-12 nm.

The recording layer can include one or more magnetic layers. Recording layer, controlled atmosphere, in general, are grown in a mixed gas of Ar or Ar and O _2. This layer can be grown at low temperatures, less than 400K (typically this temperature range is used for magnetic layers sputtered in a mixed atmosphere of Ar and O ₂ ) or at higher temperatures, typically above 420K. It can be grown at temperatures lower than 600K. The recording layer contains Co, B, C, Si, Ti, V, Cr, Mn, Fe, Ni, Cu, Ge, Zr, Nb, Mo, Ru, Rh, Pd, Ag, Hf, Ta, W, It contains one or more additional elements selected from Re, Ir, Pt, Au, B and C. This layer further comprises B, Mg, Si, Ti, V, Cr, Mn, Fe, Co, Ni, Cu, Ge, Y, Zr, Nb, Mo, Ru, Rh, Pd, Ag, Hf, Ta, At least one oxide material selected from the group comprising oxides of W, Re, Ir and Pt. For example, there is a CoCrPt + SiO _2. The thickness of the magnetic layer 4 is in the range of about 4-30 nm, preferably in the range of about 8-20 nm.

Optionally, for example, if layer 2 is not amorphous, an amorphous layer (AmL) is provided. This layer can include magnetic or non-magnetic materials, such as FeCoB, CZN, Ti _δ Cr _100-δ , Ta _δ Cr _100- , which have a composition that allows them to become amorphous. _δ (30 <δ <60), NiTa, NiNb, NiP and CrZr. The optional amorphous layer thickness is in the range of about 0-10 nm, and preferably in the range of about 0.2-20 nm.

  Advantageous features realized by embodiments of the present invention are presented in the following example.

  All examples described in this disclosure were made by DC magnetron sputtering except that the carbon film was formed by AC magnetron sputtering.

Applicants have studied vertical particle media with AFC SUL structure: FeCoB [57 nm] / Ru / FeCoB [57 nm] / Cu / IL / Mag. Here, the thickness of Ru was varied in the range of 0 to 2.2 nm, and it was found that the RKKY interaction between the FeCoB layers was a function of the thickness of Ru as shown in FIG. FIG. 5 shows how _Jex varies with the thickness of Ru. Thus, for the sputtering conditions used, the antiferromagnetic coupling is 0.3 ± 0.2 to 0.9 ± 0.2 nm and 1.7 ± 0.2 to about 2.6 ± 0.2 nm. Has been obtained. However, when the sputtering conditions are changed, for example, when the Ar sputtering pressure is increased, the roughness of the interface changes, and the Ru thickness at which the ferromagnetic layer in the SUL becomes in an antiferromagnetic coupling state changes. For this reason, we want to insist on all Ru thicknesses where the ferromagnetic layers in the SUL are in an antiferromagnetic coupling state.

  The origin of the RKKY interaction is conduction electron polarization induced by localized spins. The atoms in the magnetic layer at the interface with the nonmagnetic layer (spins localized at the interface) polarize conduction electrons in the nonmagnetic layer. Depending on the thickness of the nonmagnetic layer, the exchange interaction changes from ferromagnetism to antiferromagnetism, as shown in FIG. The exchange is mostly a phenomenon at the closest point, and occurs with a typical value (a few angstroms) of the interatomic distance in the solid. A thicker spacer layer may be used, but in order to break or stabilize the exchange interaction between two magnetic layers separated by the spacer layer, a one atomic layer spacer comprising one material between the two magnetic layers If a layer exists, it is sufficient.

  FIG. 6 is a plot of SMNR versus Ru layer thickness, showing that the recording characteristics of the media are not degraded even when the Ru thickness is less than 1.1 nm.

  FIG. 7 is a plot of overwrites as a function of write current for SULs with several different AFCs and shows how the overwrites in the media decrease as the antiferromagnetic coupling between FeCoB SUL layers increases. .

FIG. 8 is a plot of erasure as a function of antiferromagnetic coupling expressed in J _ex (erg / cm ² ), with media erasing as the antiferromagnetic coupling between the soft base layers of the FeCoB layer increases. Shows a marked improvement.

  Thus, the present invention has demonstrated that bonding between FeCoB layers is an important parameter for preventing erasure and that the presence of an interface layer is important for adjusting optimal recording characteristics.

  Applicants have further investigated vertical particulate media having the AFC SUL structure: FeCoB [y] / Ru / FeCoB [y] / Cu / IL / Mag. Here, the thickness x of Ru was changed from 0 to 0.8 nm, and the thickness of FeCoB was changed from 56 to 130 nm. It has been observed that when the thickness of a single FeCoB layer exceeds 125 nm, stripe domains occur in the FeCoB layer. The thickness at which the stripe domain is formed is referred to as the critical thickness for forming the stripe domain. When a Ru layer having a thickness of about 0.85 nm was inserted between two FeCoB layers, the critical thickness of each FeCoB layer was 70 nm. Note that the RKKY bond between FeCoB is negligible if the Ru thickness is about 0.85 nm. On the other hand, when an about 0.5 nm thick Ru layer was inserted between two FeCoB layers, the critical thickness of each FeCoB layer was 115 nm. This increase in critical thickness is attributed to a large antiferromagnetic coupling between FeCoB layers across the Ru spacer layer of 0.5 nm. In this way, applicants can reduce the Ru layer thickness by using AFC SUL and reduce the total SUL thickness of antiferromagnetic coupling without the formation of stripe domains, as shown in FIG. It has been demonstrated that it can be increased.

In Figure 10, _Applicant has plotted SUL critical thickness without stripe domain as AFC function expressed in _{J ex.} Figure 10 is the critical SUL thickness is initially _is proportional to _{J ex,} shows how the saturation for large _{J ex.}

  While this application has disclosed the upper and lower limits of several numerical ranges that support any range within the disclosed numerical ranges, the exact upper and lower limits of the ranges are presented verbatim in the specification. Absent. This is because the present invention can be carried out anywhere within the numerical range disclosed by the present invention. Finally, the patents and publications cited in this application are hereby incorporated by reference in their entirety.

The schematic diagram which shows the recording bit of horizontal (a) and vertical (b). Schematic showing a vertical pole head with magnetic media and base layer. 1 is a schematic diagram of an embodiment of a perpendicular recording medium of the present invention having a film structure having a substrate, an adhesive layer, an AFC soft base layer, a nonmagnetic intermediate layer, a recording layer, and a carbon layer. (A)-(d) is a schematic diagram which shows different embodiment of the AFC SUL structure provided with FML (ferromagnetic layer), SL (spacer layer), IFL (interface layer), and Ru (ruthenium layer). FIG. 4 is a graph showing RKKY coupling between FeCoB layers as a function of Ru thickness in one embodiment of the invention. FIG. The graph which shows a mode that the recording characteristic of the medium of one Embodiment of this invention does not deteriorate even when the thickness of a Ru spacer layer becomes thinner than 1.1 nm. The graph which shows a mode that an overwrite reduces as the antiferromagnetic coupling between FeCoB layers increases with the media of one embodiment of this invention. The graph which shows a mode that erasure | elimination improves notably as the antiferromagnetic coupling between FeCoB layers increases with the medium of one embodiment of this invention. FIG. 5 is a graph showing the critical thickness of a soft base layer without stripe domains as a function of Ru spacer layer thickness in one embodiment of the present invention. The initial critical thickness of the SUL, but increases in proportion to J _ex, graphs showing the state of saturation in the area J _ex is large.

Explanation of symbols

1 Adhesive layer (AL)
2 AFC soft base layer 3 Interface layer (IL)
4 Recording layer (RL)
5 Carbon layer (CL)

Claims (20)

  A magnetic recording medium includes a first magnetic layer, a spacer layer, and a second magnetic layer in this order, the spacer layer includes a nonmagnetic layer, and the spacer layer has a thickness of the first magnetic layer. The thickness of both the first and second magnetic layers is selected to achieve antiferromagnetic coupling between the layer and the second magnetic layer, and is critical for the formation of stripe domains in the magnetic layer The magnetic recording medium smaller than the thickness.   The magnetic recording medium of claim 1, wherein erasure of the magnetic recording medium is less than about 5%.   2. The magnetic recording medium of claim 1, wherein the critical thickness of the first and second magnetic layers is in the range of about 40-150 nm.   4. The magnetic recording medium according to claim 3, wherein the first and second magnetic layers are Co, B, P, Si, C, Zr, Nb, Hf, Ta, Al, Si, Cu, Ag, Au, Nd. The magnetic recording medium comprising a Fe-containing alloy of a material selected from the group comprising Sm, Tb, Dy, Ho and combinations thereof.   2. The magnetic recording medium according to claim 1, wherein the spacer layer has a thickness in the range of about 0.1-4 nm.   6. The magnetic recording medium according to claim 5, wherein the spacer layer includes a material selected from the group including Ru, Rh, Ir, Cr, Cu, Re, V, and combinations thereof.   2. The magnetic recording medium according to claim 1, further comprising an interface layer between the first magnetic layer and the spacer layer or between the second magnetic layer and the spacer layer.   8. The magnetic recording medium of claim 7, wherein the interface layer has a thickness in the range of about 0.1-10 nm.   2. The magnetic recording medium according to claim 1, further comprising an additional magnetic layer and an additional spacer layer, wherein the additional magnetic layer is ferromagnetically coupled with the additional spacer layer interposed therebetween. media.   2. The magnetic recording medium according to claim 1, further comprising an additional magnetic layer and an additional spacer layer, wherein the anti-additive magnetic layer is antiferromagnetically coupled with the additional spacer layer interposed therebetween. Magnetic recording media.   A method of manufacturing a recording medium, which includes a step of obtaining a substrate, a step of depositing a first magnetic layer, a step of depositing a spacer layer, and a step of depositing a second magnetic layer in this order, The spacer layer includes a non-magnetic layer, and the thickness of the spacer layer is selected to establish antiferromagnetic coupling between the first magnetic layer and the second magnetic layer, and 2. The method of claim 2, wherein the thickness of both magnetic layers is less than a critical thickness at which stripe domains are formed in the magnetic layer.   12. The method of claim 11, wherein erasure of the magnetic recording media is less than about 5%.   12. The method of claim 11, wherein the critical thickness of the first and second magnetic layers is in the range of about 40-150 nm.   14. The method of claim 13, wherein the first and second magnetic layers are Co, B, P, Si, C, Zr, Nb, Hf, Ta, Al, Si, Cu, Ag, Au, Nd, Sm. The method comprising an Fe-containing alloy of a material selected from the group comprising Tb, Dy, Ho and combinations thereof.   12. The method of claim 11, wherein the spacer layer thickness is in the range of about 0.1-4 nm.   16. The method of claim 15, wherein the spacer layer comprises a material selected from the group comprising Ru, Rh, Ir, Cr, Cu, Re, V, and combinations thereof.   12. The method of claim 11, further comprising depositing an interface layer between the first magnetic layer and the spacer layer or between the second magnetic layer and the spacer layer.   18. The method of claim 17, wherein the interface layer thickness is in the range of about 0.1-10 nm.   The magnetic recording medium according to claim 1, wherein at least one of the first and second magnetic layers is amorphous.   The magnetic recording medium according to claim 1, wherein at least one of the first and second magnetic layers is crystalline.

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