Certain devices use disk drives with heat assisted magnetic recording (HAMR) media to store information. For example, disk drives can be found in many desktop computers, laptop computers, and data centers. HAMR media store information magnetically as bits. In HAMR writing process, a fine laser spot may heat up the HAMR media above its Curie temperature in order to switch its magnetization orientation. Superparamagnetic trap may result which causes a grain within the HAMR media to have a wrong magnetization orientation once it is cooled. Superparamagnetic trap therefore impacts performance and reliability of the HAMR media.
Provided herein is an apparatus that is capable of reducing superparamagnetic traps and capable of maintaining epitaxial growth in a HAMR media. The apparatus includes a storage layer, an exchange tuning layer, and a write layer. The storage layer is magnetic. The exchange tuning layer is disposed over the storage layer. The exchange tuning layer is weakly magnetic at the elevated writing temperature. The write layer is disposed over the exchange tuning layer. The write layer is magnetic and the exchange tuning layer magnetically weakens magnetic coupling between the storage layer and the write layer. These and other features and advantages will be apparent from a reading of the following detailed description.
Before various embodiments are described in greater detail, it should be understood that the embodiments are not limiting, as elements in such embodiments may vary. It should likewise be understood that a particular embodiment described and/or illustrated herein has elements which may be readily separated from the particular embodiment and optionally combined with any of several other embodiments or substituted for elements in any of several other embodiments described herein.
It should also be understood that the terminology used herein is for the purpose of describing the certain concepts, and the terminology is not intended to be limiting. Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood in the art to which the embodiments pertain.
Unless indicated otherwise, ordinal numbers (e.g., first, second, third, etc.) are used to distinguish or identify different elements or steps in a group of elements or steps, and do not supply a serial or numerical limitation on the elements or steps of the embodiments thereof. For example, “first,” “second,” and “third” elements or steps need not necessarily appear in that order, and the embodiments thereof need not necessarily be limited to three elements or steps. It should also be understood that, unless indicated otherwise, any labels such as “left,” “right,” “front,” “back,” “top,” “middle,” “bottom,” “beside,” “forward,” “reverse,” “overlying,” “underlying,” “up,” “down,” or other similar terms such as “upper,” “lower,” “above,” “below,” “under,” “between,” “over,” “vertical,” “horizontal,” “proximal,” “distal,” and the like are used for convenience and are not intended to imply, for example, any particular fixed location, orientation, or direction. Instead, such labels are used to reflect, for example, relative location, orientation, or directions. It should also be understood that the singular forms of “a,” “an,” and “the” include plural references unless the context clearly dictates otherwise.
It is understood HAMR media may include both granular magnetic layers and continuous magnetic layers. Granular layers include grains that are segregated in order to physically and magnetically decouple the grains from one another. Segregation of the grains may be done, for example, with formation of segregants such as oxides, carbon (C), boron (B), boron nitride (BN), etc., at the boundaries between adjacent magnetic grains. As such, the segregated magnetic grains form a granular layer. When multiple granular layers stacked together they form a columnar structure, where the magnetic alloys are hetero-epitaxially grown into columns while the oxides segregate into grain (column) boundaries. HAMR media may include both granular layers and continuous layers. In some embodiments, the exchange tuning layer may also improve the epitaxial growth within the HAMR media.
As the technology of heat assisted magnetic recording (HAMR) media reaches maturity, it becomes increasingly difficult to continue to increase the storage capacity of recording media (e.g. disk drive disks) or to reduce the size of recording media while maintaining storage capacity. Such challenges may be overcome by increasing the bit density on the recording media. Unfortunately, increasing the bit density that may require segregants in order to separate the grains from one another may disrupt the epitaxial growth of the HAMR media. The epitaxial growth of the magnetic layers is challenged when segregant materials are introduced. As a result, increasing the thickness of the total magnetic layer may cause random orientation in the top layer of the HAMR media.
Furthermore, in HAMR media performance may suffer from superparamagnetic traps. For example, during recording, a fine laser spot heats the magnetic grains above the Curie temperature. As the disk rotates away from the laser spot, the heated region quickly cools down at the presence of a magnetic field. As the magnetic grains cools down, their magnetization (Ms) and anisotropy filed (Hk) increase dramatically. The magnetization orientation of the uniaxial perpendicular magnetic grains can be switched by the magnetic writing field (Hwrite) from the transducer as long as Hwrite>Hk. As the grains cool down further, the Hk increase more, to a point where Hwrite<=Hk the magnetization is no longer switchable by the Hwrite. The magnetization orientation is frozen in the same direction as that of the Hwrite. The temperature where the Hwrite=Hk is called Twrite. The temperature Twrite is the temperature that the magnetization orientations is set. Thermal perturbation is a factor to be considered during the magnetization frozen process. At an elevated temperature the thermal fluctuation energy kTwrite, where k is the Boltzmann constant could be very comparable to the Zeeman energy, EZeeman=0.5 Hwrite.MsV, where V is the volume of a magnetic grain. As a result, the magnetization could be frozen into an undesired direction with very high probability. Such a phenomena is called superparamagnetic traps.
Accordingly, enhancing Hwrite, Ms, or V are alternatives to increase the EZeeman/kTwrite ratio in order to reduce the superparamagnetic trap effect. From media design stand point, Hwrite is fixed once a transducer is fabricated and shipped to a HAMR drive. Magnetization (Ms) of the media can be increased as long as there are no other negative impacts on the magnetic recording. The volume of the magnetic grain can be expressed as V=Dt, where D is average grain size and t magnetic layer total thickness. Increasing grain size may adversely impact storage areal density. Therefore, it is may be desirable to have a larger thickness (t). Unfortunately, as mentioned above, due to large amount of segregant volume percentage (vol %), the magnetic layer cannot be grown very thick because increasing the thickness results in the media losing its self-epitaxy. The embodiments presented herein mitigate the superparamagnetic trap effect.
According to some embodiments, the exchange tuning layer may be disposed between the storage layer and the write layer (also referred to as hard layer and soft layer). The exchange tuning layer may be nonmagnetic or weakly magnetic at the elevated temperature (e.g. Twrite). In some embodiments, the exchange tuning layer may include a material that is magnetic with higher Curie temperature than the storage layer but the exchange tuning layer may still be weakly magnetic or nonmagnetic at Twrite. The exchange tuning layer weakens the magnetic coupling between the storage layer and the write layer. It is appreciated that the exchange strength can be tuned by the magnetization (Ms) and the thickness of the exchange tuning layer. Thus, the magnetization orientation of the write layer may be switched during the write process first before the magnetization orientation of the storage layer is switched. The switching of the magnetization orientation of the write layer has an additive effect with the external field that is being applied (e.g., is in the same orientation as the external field) for writing into the storage layer, thus lowering a required external field to write to the storage layer, effectively increasing the transducer magnetic field. As a result, the Twrite may be reduced. Moreover, the Zeeman energy of the magnetic switching is now calculated as EZeeman=0.5Hwrite (Ms1V1+Ms2V2), where Ms1 and V1 stands for saturation magnetization and grain average volume of the storage layer, respectively, and Ms2 and V2 stands for saturation magnetization and grain average volume of the write layer, respectively. Thus the addition of the exchange tuning layer and the write layer to the storage layer enhances the Zeeman energy to kTwrite ratio. Hence superparamagnetic trap effect is reduced. Furthermore, a selection of the exchange tuning layer may promote epitaxial growth of the HAMR media. For example, the exchange tuning layer may include nonmagnetic or weakly magnetic material with face centered cubic (fcc) crystal structure or L10 crystal structure that further aids the growth of the top write layer. The exchange tuning layer may or may not contain segregants in some embodiments.
According to some embodiments, the write layer 120 may include material such as FePt, FePtMo, FePtCo, FePtNi, FeCoPt, CoPt, CoNiFe, CoFe, CoCrPt, CoCrPtRu, or alloy thereof. The crystalline structure of the write layer could be of a cubic structure, such as bcc, fcc, or L10 etc. In other embodiments, the write layer 120 may include material such as CoFe, CoNi, CoCr, or alloy thereof, FeCoCrNiPt or alloy thereof, CoCrPt or alloy thereof, etc., of cubic structure such as fcc structure, bcc, derivative of bcc structure known as B2, etc. It is appreciated that the write layer 120 and the storage layer 110 may have a substantially similar or the same Curie temperature, e.g., the Curie temperature of the write layer 120 may be within 30% of the Curie temperature of the storage layer 110. In some embodiments, the write layer 120 has a higher room temperature saturation magnetization than the storage layer 110. Furthermore, the room temperature anisotropy field Hk for the write layer 120 is lower than the anisotropy field of the storage layer 110, in some embodiments. At room temperature, Hk of the write layer may be approximately at 0-5 kOe. The thickness of the write layer 120 may range between 0.2-3 nm. In some embodiments, the thickness may range between 0.2-5 nm.
It is appreciated that the write layer 120 may be a continuous layer or one or more granular layers. For example, the write layer 120 may include grain decoupling material, e.g., B, C, carbide such as SiC, BC, TiC, TaC, etc., nitride such as BN, SiN, TiN, etc., oxide such as SiO2, B2O3, WO3, Ta2O5, TiO2, etc., or any combination thereof.
According to some embodiments, the storage layer 110 may include magnetic material of L10 structure, e.g., FePt, FePtCu, FePtAg, FePtCuAg, FePtMo, FePtCo, FePtNi, CoPt, FeCoPt, and CoPdPt or alloy thereof. It is appreciated that the write layer 120 and the storage layer 110 may have a substantially similar or the same Curie temperature, e.g., the Curie temperature of storage layer 110 may be within 30% of the Curie temperature of the write layer 110. In some embodiments, the storage layer 110 has a lower room temperature saturation magnetization than the write layer 120. Furthermore, the anisotropy field for the storage layer 110 is higher than the anisotropy field for the write layer 120, in some embodiments. The thickness of the storage layer 110 may range between 1-10 nm. In some embodiments, the thickness may range between 1-5 nm. The thickness of the storage layer 110 may range between 2-15 nm.
It is appreciated that the storage layer 110 may be a continuous layer or one or more granular layers. For example, the storage layer 110 may include grain decoupling material, e.g., B, C, carbide such as SiC, BC, TiC, TaC, etc., nitride such as BN, SiN, TiN, etc., oxide such as SiO2, B2O3, WO3, Ta2O5, TiO2, etc., or any combination thereof.
In some embodiments, the exchange tuning layer 130 may include material such as PtX where X is a magnetic material with high Curie temperature but where PtX is nonmagnetic or weakly magnetic. In some embodiments X may be Co that has a high Curie temperature. X may also include material such as Cu, Ru, Ni, Rh, Nd, Ag, etc., or any combination thereof. It is appreciated that the alloy of PtX may be selected for the exchange tuning layer 130 such that the magnetic coupling between the storage layer 110 and the write layer 120 is weakened and tunable by varying its thickness. In some embodiments, the exchange tuning layer 130 may include MgO. In some embodiments, the exchange tuning layer 130 may include CuAu, or an alloy of transition metals with cubic structure. The crystalline structure of the materials used for exchange tuning layer 130 could be cubic, such as, bcc, fcc, bcc-derivative, fcc-derivative, L10, etc.
It is appreciated that the exchange tuning layer 130 may be a continuous layer or one or more granular layers. For example, the exchange tuning layer 130 may include grain decoupling material, e.g., B, C, carbide such as SiC, BC, TiC, TaC, etc., nitride such as BN, SiN, TiN, etc., oxide such as SiO2, B2O3, WO3, Ta2O5, TiO2, etc., or any combination thereof. According to some embodiments, the exchange tuning layer 130 maintains the granular structures, magnetization orientation and anisotropy between the storage layer 110 to the write layer 120. The alloy of CuAg, PtX or MgO may be used to promote epitaxial growth between the storage layer 110 and the write layer 120. For example, the exchange tuning layer 130 may be a face centered cubic crystalline structure, thus enabling epitaxial growth between the storage layer 110 and the write layer 120 in (001) orientation. In some embodiments, the storage layer 110 and the write layer 120 may have a crystalline growth structure in (002) orientation of L10 structure and the exchange tuning layer 130 may have a crystalline structure growth in (200) orientation of a cubic structure. The exchange tuning layer 130 may be a thin layer, e.g., 20 Å or less. In some embodiments, the exchange tuning layer 130 may be between 0-5 nm in thickness.
It is appreciated that the write layer 120 may have a lower anisotropy field than the storage layer 110. Furthermore, the write layer 120 may have a higher or the same room temperature saturation magnetization as the storage layer 110. However, the write layer 120 has a higher or the same Curie temperature as the storage layer 110. Accordingly, the exchange tuning layer 130 may be selected such that it exchange tunes the storage layer 110 by weakening the magnetic coupling between the storage layer 110 and the write layer 120 such that the write layer 120 is magnetically switched first prior to the storage layer 110 switching when the HAMR media is being written to (i.e. in presence of external magnetization field and during the heating process). During the HAMR write process, e.g., during heating and subsequently cooling period through high temperature with near field transducer (NFT), the vertical coupling between the write layer 120 and the storage layer 110 is weakened by the exchange tuning layer 130. As such, the magnetic switching by the write layer 120 in addition to the external magnetization field aids in writing (i.e. switching the magnetization orientation) to the storage layer 110. Thus, a weaker external magnetization field may be used in comparison to an apparatus that does not use the exchange tuning layer 130. Consequently, a lower writing temperature (Twrite) may be achieved because the exchange tuning layer 130 now aids in writing to the storage layer 110 by decoupling or weakening the magnetization coupling between the storage layer 110 and the write layer 120.
In other words, the exchange tuning layer 130 tunes the magnetic property of the HAMR media 100. The effective anisotropy field of the bi-layer may be defined by the following equation if there is no exchange tuning layer:
where Ku(Twrite) is anisotropy field at the writing temperature Tw, V is the volume of a magnetic grain, Ms(Twrite) is room temperature saturation magnetization at writing temperature and subscripts 1 and 2 denote the storage layer and the write layer, respectively. It is appreciated that Ku2(Twrite) negligible because the write layer is of cubic structure. As a result, the Hk(eff) of the bi-layer is dramatically reduced. Addition of the exchange tuning layer 130 reduces the magnetic coupling between the storage layer and the write layer, therefore, effectively increasing the Hk(eff) in the above equation. The exchange tuning layer causes the write layer 120 that is soft to switch first, therefore aiding the external field in writing to the storage layer 110. Since the numerator is reduced and the denominator is increased the effective anisotropy field is reduced, thereby effecting increasing the transducer field. Accordingly, the HAMR media will be switched at a lower temperature, thereby improving performance by reducing superparamagnetic trap effect.
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While the embodiments have been described and/or illustrated by means of particular examples, and while these embodiments and/or examples have been described in considerable detail, it is not the intention of the Applicants to restrict or in any way limit the scope of the embodiments to such detail. Additional adaptations and/or modifications of the embodiments may readily appear to persons having ordinary skill in the art to which the embodiments pertain, and, in its broader aspects, the embodiments may encompass these adaptations and/or modifications. Accordingly, departures may be made from the foregoing embodiments and/or examples without departing from the scope of the concepts described herein. The implementations described above and other implementations are within the scope of the following claims.