Patent Publication Number: US-9899050-B2

Title: Multiple layer FePt structure

Description:
RELATED APPLICATIONS 
     This application is a continuation of copending U.S. patent application Ser. No. 13/836,521 filed on Mar. 15, 2013, which issues as U.S. Pat. No. 9,520,151 on Dec. 13, 2016 and which is a continuation-in-part of U.S. patent application Ser. No. 13/418,167, filed Mar. 12, 2012, which is a divisional of U.S. Pat. No. 8,133,332 issued Mar. 13, 2012, the content of which are incorporated herein by reference in its entirety. 
    
    
     BACKGROUND 
     Materials with increased magnetic anisotropies are used in various applications such as, for example, applications in the data storage industry where there is a continuing goal to increase storage densities. Data storage media that can store information at densities above 1 Tbit/in 2  may require materials with magnetic anisotropies greater than conventional media materials. 
     SUMMARY 
     One embodiment described herein is directed to a method involving depositing a seed layer on a substrate, the seed layer comprising A1 phase FePt with a ratio of Pt of Fe greater than 1:1. A main layer is deposited on the seed layer, the main layer comprising A1 phase FePt with a ratio of Pt to Fe of approximately 1:1. A cap layer is deposited on the main layer, the cap layer comprising A1 phase FePt with a ratio of Pt to Fe of less than 1:1. The seed, main and cap layers are annealed to convert the A1 phase FePt to L1 0  phase FePt having a graded FePt structure of varying stoichimetry from approximately Fe 50 Pt 50  adjacent a lower portion of the structure proximate the substrate to Fe &gt;50 Pt &lt;50  adjacent an upper portion of the structure opposite the lower portion. 
    
    
     
       BRIEF DESCRIPTION OF THE DRAWINGS 
         FIG. 1  is a diagram illustrating an arrangement of a perpendicular medium according to an example embodiment; 
         FIG. 2  is a graph of a hysteresis loop for materials that can be used in the material stack of  FIG. 1 ; 
         FIG. 3A  is a side elevation view of a material stack used in a first embodiment; 
         FIG. 3B  is a side elevation view of another material stack used in another embodiment; 
         FIG. 4  is a graph of a typical hysteresis loop for materials that can be used in the material stack of  FIG. 3 ; 
         FIG. 5  is a schematic representation of a granular media; 
         FIG. 6  is a schematic representation of a process for producing exchange coupled composite media; 
         FIG. 7  is a schematic representation of a process for producing graded anisotropy media; 
         FIGS. 8 and 9  are schematic representations of a structure and process for producing graded anisotropy media according to an example embodiment; and 
         FIG. 10  is a flowchart illustrating a procedure according to an example embodiment. 
     
    
    
     DETAILED DESCRIPTION 
     There are known bulk permanent magnetic materials having crystalline phases with magnetocrystalline anisotropy that can store information at densities greater than 1 Tbit/in 2 . For bulk permanent magnetic materials, special heat treatments are typically used to control the phase formation and microstructure to optimize the material properties. In order to incorporate these materials into a data storage media, the correct crystalline phase must be obtained within a microstructure of fine, nanocrystalline, exchange decoupled or partially exchange decoupled grains while maintaining thermal stability. 
     L1 0  phase FePt containing alloys have magnetocrystalline anisotropy as high as 7×10 7  erg/cc, which is well suitable for magnetic recording media to achieve density over 1 Tb/in 2 . However, FePt typically forms the face centered cubic (fcc) phase (i.e., the A1 phase) when deposited at room temperature, and annealing is required to transform (i.e., chemically order) the material into the high anisotropy L1 0  phase. 
     This high temperature processing enhances diffusion, which can affect grain growth, grain morphology, grain segregation, and grain composition through intermixing. On the other hand, growth oriented [001], fully ordered L10, exchange decoupled FePt containing alloy media can have a coercivity over 4 Tesla, which is beyond current writer technology capabilities. One goal is to produce oriented, FePt containing media with a small grain size and with magnetic characteristics that are compatible with current writer technology. A second goal is to produce oriented, FePt containing media with a small grain size and with magnetic characteristics that are compatible with write assisted recording technology such as heat-assisted magnetic recording (HAMR). 
     The present disclosure is directed to a method of fabricating a data storage media that uses a multiple layer structure including seed and/or cap layers on top and/or bottom of an FePt containing recording layer, and anneals the multiple layer structure to convert it from A1 structure to predominantly FePt containing L1 0  phase material at a relatively low anneal temperature. 
     Taking advantage of the ability to intermix the seed layer and main recording layer upon annealing and form a graded composition L10 structure, the seed layer may be selected to optimize and set recording layer properties including the initial growth, grain size, roughness, orientation, ordering temperature, segregation, and magnetic moment of the recording layer without significantly damaging the post-annealing properties of the full layer stack. Further, the seed layer may be designed to provide desired, vertically non-uniform properties of the recording layer that are achieved only after the annealing process to form the L10 structure is completed; thus achieving desired gradient of magnetic properties such as anisotropy field (Hk), saturation magnetic moment (Ms), and Curie temperature (Tc), to form so-called ECC (exchange coupled composite) and graded moment HAMR media designs. 
     A top layer comprising a different material composition than the main recording layer can similarly be used to intermix with the main recording layer upon annealing, and form an L10 structure with graded composition, microstructure, and magnetic and thermal properties. Along with achieving desired gradients of magnetic properties including Hk, Ms, and Tc, for ECC and graded moment media, the segregation of the top layer may be adjusted to reduce the resulting Hex and roughness after annealing, and form a so-called CGC (continuous granular composite) media design. 
       FIG. 3A  is a side elevation view of a material stack  10  used in a first embodiment. A multiple layer structure  12  is formed on a substrate  14 . The multiple layer structure includes a first layer  16  (e.g., a seed layer) of Pt, a first layer  18  of A1 phase FePt on the first layer of Pt, and a second layer  20  (e.g., a cap layer) of Pt on the layer of FePt. The substrate can be, for example, glass, aluminum or its alloys, etc. The layers can be formed by physical vapor deposition methods, such as magnetron sputtering, pulsed laser deposition, or ion beam deposition. 
     In one example, layer  16  can have a thickness ranging from about 0.5 nm to about 5 nm. Layer  18  can have a thickness ranging from about 2 nm to about 10 nm. Layer  20  can have a thickness ranging from about 0.5 nm to about 5 nm. 
     The multiple layer structure is annealed to convert the A1 phase FePt to L1 0  phase FePt. In one example, the annealing step can be performed at about 300° C. for 4 hours. In other examples, the annealing temperature can be in a range from about 200° C. to about 600° C. The annealing temperature to convert the A1 phase FePt to L1 0  phase FePt may depend on the layer thicknesses and annealing times. Portions or all of the seed layer and cap layer may also interdiffuse during annealing, and may also transform to L10 structure and form high anisotropy material. The annealing process may occur in-situ, concurrent with layer deposition, by depositing on a heated substrate. 
     In reference now to  FIG. 1 , a diagram illustrates a perpendicular recording medium  105  according to an example embodiment. The medium  105  may include multiple underlayers between the substrate  113  and the multiple layer FePt containing recording structure  107 . Such embodiments may further include an adhesion layer (not shown), a soft underlayer (SUL)  112 , a heatsink layer (HS)  111 , a thermal resistor  109 , an orientation layer  110 , and a diffusion barrier  108 . 
     The adhesion layer, if needed, generally includes an amorphous metal layer that adheres well to the (glass) substrate  113 . The SUL  112  often includes a high M s  low anisotropy material generally having H c &lt;100 Oe. Such materials often include at least one of Fe and Co, and elements promoting an amorphous structure at room temperature, of which Ta, B, Zr, W are common selections. The heatsink layer  111  is used to carry heat away from the active region of the media and increase temperature gradient. Appropriate materials for the heatsink layer  111  have high heat conductivity and compatible microstructure and film growth properties. Some high conductivity options include Cu, Ag, Au, Mo, Ru, W, V, and their alloys. 
     Above the heatsink  111 , additional layers are provided that accomplish multiple purposes; to provide a template for &lt;001&gt; growth and grain isolation of the magnetic layers, to prevent interdiffusion of heatsink material into the magnetic layers, and to act as a thermal resistor that controls the flow of heat into the heatsink. Some presently preferred embodiments employ an MgO containing layer that accomplishes all of these tasks. Other embodiments may use one or more different layers to accomplish these tasks. On top of these layers, the multiple layer Fe—Pt containing recording structure  107  is deposited and annealed, to form an L10 phase with c-axis and anisotropy axis oriented perpendicular to the substrate plane; A protective overcoat  106  and lubrication are subsequently applied. The overcoat  106  may be formed from a diamond-like carbon material. 
       FIG. 2  is a graph of magnetization versus applied magnetic field (i.e., a hysteresis loop) for a multiple layer structure as shown in  FIG. 1  in which the FePt layer comprises Fe 62 Pt 38 . During annealing, there may be some diffusion between the layers, which depends on annealing process, time, and temperature used. 
       FIG. 2  shows a coercivity of about 9130 Oe for the multiple layer structure. The hysteresis loop was measured by monitoring the magnetic moment change while the applied field is sweeping from −18000 Oe to +18000 Oe and then swept backwards using a vibrating sample magnetometer (VSM) at room temperature. The magnetic field was applied with its direction parallel to the film plane, which is called an in-plane measurement, and the coercivity is then called the in-plane coercivity. 
       FIG. 3B  is a side elevation view of a material stack  30  used in another embodiment. A multiple layer structure  32  is formed on a substrate  34 . The multiple layer structure includes a first layer  36  (e.g., a seed layer) of Fe, a first layer  38  of A1 phase FePt containing alloy on the first layer of Fe, and a second layer  40  (e.g., a cap layer) of Fe on the layer of FePt containing alloy. The multiple layer structure is annealed to convert the A1 phase FePt containing alloy to L1 0  phase FePt containing alloy. The substrate can be, for example, glass, aluminum or its alloys, etc. 
     In one example, layer  36  can have a thickness ranging from about 0.5 nm to about 5 nm. Layer  38  can have a thickness ranging from about 2 nm to about 10 nm. Layer  40  can have a thickness ranging from about 0.5 nm to about 5 nm. 
     The multiple layer structure is annealed to convert the A1 phase FePt containing alloy to L1 0  phase FePt containing alloy. In one example, the annealing step can be performed at about 300° C. for 4 hours. In other examples, the annealing temperature can be in a range from about 200° C. to about 600° C. The annealing temperature used to convert the A1 phase FePt containing alloy to L1 0  phase FePt depends on the layer thicknesses and annealing times. The annealing process may occur in-situ, concurrent with layer deposition, by depositing on a heated substrate. Portions or all of the seed layer and cap layer may also interdiffuse during annealing, and may also transform to L10 structure and form high anisotropy material. 
       FIG. 4  is a graph of magnetization versus applied magnetic field for a multiple layer structure of  FIG. 3  in which the FePt containing alloy layer comprises Fe 36 Pt 64 .  FIG. 4  shows a coercivity of about 1800 Oe for the multiple layer structure. 
     In the examples of  FIGS. 1 and 3 , atom diffusion at the two interfaces, between the seed layer and the FePt containing alloy layer, and between the cap layer and FePt containing alloy layer, facilitates the chemical ordering process for the whole stack. 
     The platinum seed and cap combination of  FIG. 1  is suitable for an iron rich FePt containing alloy middle layer, as diffusion may drive the whole film towards the stoichiometric composition of 50 to 50. In one example using platinum as the seed and cap layer, an in-plane coercivity value of 9130 Oe has been achieved after annealing at a temperature as low as 300° C. Similarly, the iron seed and cap combination of  FIG. 3  is effective for ordering a platinum rich FePt containing alloy middle layer. 
     Media grain size is reduced as the annealing temperature decreases. Thus the use of a low annealing temperature would limit the media grain size. A successful low temperature phase transformation method ensures small grain size for high recording areal density. 
     Since the inter-diffusion occurs in a direction perpendicular to the plane of the films, grain isolation materials such as SiO 2 , carbon, boron, or other oxide or nitride material can be applied to keep the FePt containing alloy grain size within several nm. These grain isolation materials can be applied by embedding them into the target material, and/or through co-sputtering from a separate target in the same chamber. 
       FIG. 5  is a schematic drawing of a media  42  having an FePt containing alloy layer  44  between Pt seed and cap layers  46 ,  48 . Grain isolation material  50  is shown to be positioned between grains  52  in the stack. 
     In another aspect, a data storage media is provided with enhanced writability. One way to enhance writability is to form so-called Exchange-Coupled Composite (ECC) or Domain Wall Assisted Magnetic Recording (DWAMR) media. ECC media include one magnetically hard phase (in this case ordered L1 0  FePt containing alloy) and one magnetically softer phase, which can be disordered or partially ordered FePt containing alloy or other high magnetization materials such as FeNi, FeCo, etc. As used in this description, for conventional magnetic recording, a magnetically hard material is a material that typically has a coercive force higher than 2000 Oe, and a magnetically soft material is a material that typically has a coercive force lower than 2000 Oe. For media designed for Heat-Assisted Magnetic Recording (HAMR), the definition of a hard and soft layer for ECC or DWAMR media requires more care. Because the switching process and the effective switching rely on a temperature change and because the effective head field gradient is in a large part controlled by the temperature gradient, the “softer layer” in a HAMR recording system is in part the material with the lower Curie temperature (Tc), and in part the material with the lower magneto-crystalline anisotropy field (Hk) or high temperature switching field {Hsw(T)}. Thus the HAMR ECC softer and harder layers are more easily specified by different values of either Tc or Hk, rather than a room temperature coercive force. The softer phase of similar FePt containing alloys may be observable as having lower ordering parameter, Fe—Pt stoichiometry such that the Fe:Pt ratio is significantly different than 1:1, or by addition of other alloying elements such as Cu or Ni (though others are practicable) that lower Hk and Tc compared to a similar pure FePt alloy. 
     To make ECC media, the softer phase material is deposited over the L1 0  FePt containing alloy. An optional thin exchange coupling control layer of another material can be deposited before the soft phase material such that the exchange coupling control layer is positioned between the hard and soft layers to tune the interlayer exchange coupling strength. The exchange coupling control layer can be, for example, Pt, PtSi, Pd, or PdSi, or a low Ms FePt containing alloy. In some embodiments, the cap layer may comprise the exchange control layer. 
       FIG. 6  is a schematic representation of a process for producing exchange coupled composite media. The process starts with a material stack  54  including a FePt containing alloy layer  56  sandwiched in between two Pt layers  58 ,  60 , which is annealed to convert the FePt to the L1 0  phase in later  62 . Next, the cap layer is removed, for example, by plasma etching (e.g., sputtering) or ion beam milling (e.g., ion bombardment). Then a magnetically softer layer  64  is deposited over the ordered FePt containing alloy hard layer. Optionally, a thin layer  66  of Pt, Pd, or some non-magnetic or low Ms material such as silicon containing material, can be deposited over the ordered FePt containing alloy hard layer prior to the deposition of the magnetically softer layer to control the exchange coupling between the soft or hard layer. The bottom Pt partially diffuses into FePt containing alloy, any leftover of Pt would be minimal and non-ferromagnetic so it should not affect media magnetic property. 
       FIG. 6  shows the use of an iron rich middle layer that is converted to a stoichiometric composition of about 50 to 50; Fe:Pt˜1. Such conversion can be implemented by annealing. Annealing may involve a post-deposition heating of the multiple layer structure in a vacuum chamber. Alternatively, annealing may involve heating the multiple layer structure by heating the substrate prior to or concurrent with deposition of the FePt containing alloy layer(s) so that the annealing process begins as soon as the atoms of the multiple layer structure are deposited. It should be noted that the temperature of the substrate may be different from what is sometimes referred to as the “deposition temperature.” The deposition temperature may include the temperature of the plasma, which is quite high, or the average adatom energy in electron-volts, which translates to a temperature. In the present embodiments, the adatoms arrive by the deposition process, and then begin the annealing process after contact with the substrate. In such a case, the annealing temperature may be defined by the temperature of the substrate they reside on. 
     In another aspect, a graded anisotropy (GA) media is proposed to address the writability issue. Inter-diffusion of iron and platinum atoms is used to produce a composition gradient as well as a chemical ordering gradient, which in turn provides an anisotropy gradient. 
       FIG. 7  is a schematic representation of a process for producing graded anisotropy media. The process starts with a material stack  70  including an iron rich FePt containing alloy layer  72  sandwiched in between a Pt seed layer  74  and a Fe cap layer  76 . The stack is annealed to produce a graded layer  78  having a substantially stoichiometric composition of 50 to 50 (Fe:Pt˜1) near the bottom and an iron rich composition (Fe:Pt&gt;1) near the top. Such conversion can also be implemented by annealing in the form of heating the substrate prior to or concurrent with deposition of layers  72 ,  74 , and  76  so that the annealing process begins as soon as the atoms of the multiple layer structure are deposited. It is well known that a concentration gradient can help the interdiffusion of atoms of different elements. In the annealing process, thermal energy helps to create vacancies and enhance the mobility of atoms to allow for atomic reorganization. The gradient can be tuned by adjusting seed and cap thickness and composition, as well as by adjusting the annealing temperature or time. 
     FePt containing alloy media anisotropy strongly depends on the composition, and maximizes around Fe 50-55 Pt 50-45  (Fe:Pt˜1). The anisotropy decreases when the material composition is off stoichiometry. For the purposes of this description, perfect L1 0  FePt stoichiometry refers to Fe 50 Pt 50  (Fe:Pt=1). 
     With the process of  FIG. 7 , it is possible to establish gradient anisotropy media with a composition gradient. This can be, for example, achieved by using Pt diffusion from the bottom and Fe diffusion from the top layer, and results in close to equal stoichiometry at the bottom (high anisotropy, K) and an Fe rich composition on the top (low anisotropy, K). A similar approach can be implemented by sandwiching iron deficient FePt containing alloy film between a Fe or Fe-rich seed layer and a Pt or Pt-rich cap layer, with Fe diffusion from the bottom and Pt diffusion from the top. 
     Some embodiments of the invention include a magnetic recording layer that has been transformed from A1 to L1 0  crystal structure by annealing the multiple layer thin film stack in a vacuum chamber at temperatures as low as 300° C., applied after deposition of the layers onto a substrate has been completed. 
     There are alternative annealing procedures that may be applied to a multiple layer structure so as to transform the A1 FePt containing alloy structure to L1 0  and provide an effective high anisotropy magnetic recording layer. One such embodiment is to heat a substrate prior to (or during) deposition of the multiple layer structure. The heat diffuses from the substrate into the layers as they are deposited, thus providing the annealing. 
     As described below, embodiments such as shown in  FIGS. 6 and 7  may be formed using alternate structures and manufacturing techniques. These variations may result in the magnetic recording layer (e.g., FePt containing layers  56  and  72  in  FIGS. 6 and 7 , respectively) having an increased magnetic moment, increased light absorption, altered Curie temperature, and enhanced c-axis orientation. These variations may also facilitate incorporation of segregant/isolation materials into the magnetic recording layer. 
     For example, increased magnetic moment (M s ) in the magnetic recording layer can be achieved by raising the Fe:Pt ratio to a value larger than 1:1 and by reducing the amount of segregant material in the magnetic layer. Combining these factors, a graded recording layer with regions combining high moment and low segregant volume may significantly increase measured remanant moment (M r t). 
     As shown in  FIG. 7 , some embodiments include a Pt (seed) layer  74  at the bottom of the multiple layer stack  70 , that assists L1 0  ordering as it partially interdiffuses into the first FePt containing alloy layer  72  to form a recording layer  78  with graded Fe:Pt ratio, and accordingly graded anisotropy and graded magnetic moment. Such diffusion may not necessarily require a pure Pt seed layer, but may be achievable with a seed layer  74  that has a different Fe:Pt ratio than the first layer  72  so that there is a driving force for diffusion. The seed layer  74  can also include nonmagnetic segregating/isolating materials that separate the magnetic grains at grain boundaries (see isolation material  50  in  FIG. 5 ), but do not change the Fe:Pt ratio of the layer  74 . For stability during high temperature annealing, nonmagnetic materials such as carbon, carbides, boron and borides, oxides, and nitrides may be used as segregation/isolation materials. Metals above their solubility limit may also be employed. 
     An FePt containing bottom/seed layer  74  has many useful features. High percentage Pt materials (Fe:Pt&lt;&lt;1) have been found to be better templates for crystallographically oriented growth of FePt than high percentage Fe materials (Fe:Pt&gt;&gt;1). An isolated grain template enables growing subsequent isolated grain layers with less required segregation material. Bottom layers  74  containing Fe and Pt can form ordered material with less annealing and are less affected by incomplete diffusion of Pt than is a 100% Pt seed layer, thus increasing the flexibility of adjusting gradations of the Fe:Pt ratio in the final recording layer after completion of annealing. High percentage Pt materials also generally absorb more light, increasing the laser heating of the recording layer and reducing the transmitted light absorbed in the heatsink or substrate. This reduces the heat-assisted laser power and increases the temperature gradient; both can enhance performance of present HAMR recording system designs. 
     Similarly, a top (cap) layer can include an Fe or Pt layer as represented by layers  20  and  40  in  FIGS. 3A and 3B . In other embodiments, cap layers may also include Fe and Pt in a stoichiometric ratio different than that of the middle (first) layer  72  so that there is diffusion upon annealing that forms an ordered FePt containing alloy with graded composition. One example embodiment, shown in  FIG. 7 , includes a cap layer  76  made of FePt having a higher Fe:Pt ratio than middle layer  72 . The cap layer  76  may also include a lower segregant concentration than the middle layer  72 . The FePt containing alloy cap layer  76  may provide, after annealing, a graded magnetic recording design with a high moment upper region owing to higher Fe concentration and lower segregant concentration as compared to the lower portion of the recording layer. This enables a thinner total thickness of the recording layer and decreases the effective HMS (head-to-media spacing) because the center of moment of the layer is raised. Further, such methods can be combined to employ layers  72 ,  74 , and  76  to form a post-annealing example embodiment that comprises L10 phase throughout the multiple layer recording stack, and a graded microstructure including highest M s  at the top of the stack, highest absorption at the bottom of the stack, and a highest anisotropy Fe:Pt=1.0 region in between. 
     Another property that can be usefully tuned by grading composition with addition of Fe-rich or Pt-rich caps and seed layers is Curie temperature, Tc. Curie temperature has been measured to decrease more rapidly as composition becomes Pt-rich than when it is Fe-rich. Thus, the described method can also be used to form a structure that is graded with respect to Tc, and correspondingly to the anisotropy at an elevated recording temperature, such as is used in HAMR. 
     Copper is known to be capable to add substitutionally into the FePt lattice and maintain the L10 ordered structure while rapidly reducing Tc. Ni and other metallic elements can also act in this manner. In some preferred embodiments, the strength of the graded Tc can be significantly enhanced and controlled by addition of Cu to the Pt-rich or Fe-Rich seed and cap layers, and subsequent diffusion of Cu into the L10 structure that is formed after annealing. By this manner, embodiments of the invention are enabled to provide even more strongly graded Hk(t) as desired for so-called ECC media. 
     In reference now to  FIG. 8 , a schematic represents a structure and process for producing graded anisotropy media according to an example embodiment. In this embodiment, a material stack  80  includes a composite seed layer  81  at the bottom. The seed layer  81  may include at least a portion of FePt containing alloy having a stoichiometry different than the subsequent layers (e.g., main layer  84 ). The seed layer  81  is shown here as a multiple layer structure (e.g., bilayer) with a lower portion  82  proximate the substrate or underlayers (not shown) beneath an upper portion  83 . It will be appreciated that the seed layer  81  may alternatively be formed as a single layer of FePt containing alloy, e.g., with at least a portion having a higher concentration of Pt than Fe so as to increase optical absorption. The seed layer  81 , whether a single or multiple layer structure, may also include any of Au, Ag, Ru, Pd, Pt, V, Mo, W, etc., so as to increase optical absorption. Whether a single or multiple layer structure, the seed layer  81  may also optionally include segregation material. The Curie temperature can be controlled by addition of Cu to the seed layer  81 . 
     The lower portion  82  of the seed layer  81  is formed from a nonmagnetic Pt or low Fe:Pt ratio alloy having similar orientation, optical absorption, and optionally segregation properties as previously described. The upper portion  83  of seed layer  81  is formed of a high Fe:Pt ratio material, and faces the second, main Fe:Pt layer  84 . The main Fe:Pt layer  84  has a stoichiometry different than the seed layer  81 , e.g., with an approximately 50/50 ratio of Fe to Pt. The main layer  84  is also generally thicker than the seed layer  81 . The main layer  84  is deposited as A1 phase FePt, and is annealed (e.g., contemporaneously with deposition) in order to form the desired L1 0  phase FePt layer. 
     A high ratio Fe:Pt cap layer  85  completes the structure, the cap layer  85  being generally thicker than the main layer  84 . The cap layer  85  may be a single or multiple layer structure, and may also optionally include segregation material. The Curie temperature can be controlled by addition of Cu to the cap layer  85 . In this case, it may be better to grade anisotropy by going to Fe:Pt&gt;1 or Fe:Pt&gt;&gt;1 than by reducing annealing to get disorder. This structure with FePt containing alloy layers of differing stoichiometry enables the desired template properties of the high Pt alloy without the significant reduction of Ms from Pt diffusing into region  86 . 
     After annealing, which is indicated by arrow  89 , the resulting structure  88  has two graded regions  86  and  87 , each with varying FePt containing alloy stoichiometry from top to bottom. In these regions  86 ,  87 , darker shaded areas indicate higher relative concentrations of Fe. Annealing converts at least the second A1 FePt containing alloy layer  84  to an L1 0  phase region within  86 . As previously described, the annealing can occur as part of layer deposition, e.g., heating a substrate while depositing respective materials  82 - 85  so that the annealing occurs contemporaneously with the material deposition. As before, the annealing can occur in range from about 200° C. to about 600° C. The annealing may occur at least on or about when the second layer  84  is being deposited, although heat may also be applied during some or all of the deposition of layers  81  and/or  85 . 
     In reference now to  FIG. 9 , a schematic represents additional details about the example structure and process embodiments shown in  FIG. 8 . In  FIG. 9 , stacks  90 ,  91  represent respective pre- and post-anneal structures similar to  80  and  88  in  FIG. 8 . For example, layers  95 - 98  in structure  90  may be analogous to layers  82 - 85  shown in FIG.  8 . In  FIG. 9 , vertical bands  92 ,  93  represent segregation/isolation material that separates grain boundaries. As seen in this view, the isolation material  92  is not deposited in the topmost layer of stack  90 , although in other arrangements isolation material may be deposited but in lower concentrations than the lower layers. After annealing, the layers of stack  90  interdiffuse, so that the amount of segregant  93  in annealed stack  91  is the same, but is now spread between the layers and is thinner in top region  94 . Thus, this region  94  has higher M s  than nearby regions of recording stack  91  because in this region  94 , Ms increases due to the increase in Fe concentration, and further increases due to the decrease in nonmagnetic volume. Although the pre-annealing amount of segregation of layers  82 ,  83 , and  84  of  FIG. 9  were shown as equal for clarity, it should be clear that in other embodiments the amount of segregant of different layers before annealing may be different. 
     In reference now to  FIG. 10 , a flowchart illustrates a procedure according to an example embodiment. The procedure involves depositing  100  a first layer formed of at least Pt (e.g., Pt or PtFe containing alloy) on a substrate. This may include a material of high or low Fe:Pt ratio. A second layer of A1 phase FePt containing alloy is deposited  101  on the first layer. A cap layer of magnetically soft material (e.g., FePt containing alloy with a high Fe:Pt ratio.) may optionally be deposited  102  on the second layer. The substrate is heated  103  while depositing at least the A1 phase FePt containing alloy the annealing the first and second layers and convert the A1 phase FePt containing alloy to L1 0  phase FePt containing alloy. 
     The annealing may cause the first and second layer to form a graded FePt containing alloy structure of varying stoichiometry (e.g., varying gradually in Fe:Pt ratio from top to bottom). The first layer may be formed of FePt containing alloy of a different stoichiometry than the second layer of L10 phase FePt containing alloy. For example, the first layer may be formed as a bilayer structure with first and second FePt containing alloy portions. The first FePt containing alloy portion is proximate the substrate and has a Fe:Pt ratio lower than that of the second layer. The second FePt containing alloy portion is proximate the second layer and has a Fe:Pt ratio higher than that of the second layer. 
     While the embodiments have been described in terms of several examples, it will be apparent to those skilled in the art that various changes can be made to the disclosed examples, without departing from the scope of the invention as set forth in the following claims. The implementations described above and other implementations are within the scope of the following claims.