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Article

Perpendicular Magnetization Behavior of Low- Temperature Ordered FePt Films with Insertion of Ag Nanolayers

by
Da-Hua Wei
Institute of Manufacturing Technology and Department of Mechanical Engineering, National Taipei University of Technology (TAIPEI TECH), Taipei 10608, Taiwan
Materials 2016, 9(3), 209; https://doi.org/10.3390/ma9030209
Submission received: 10 November 2015 / Revised: 16 March 2016 / Accepted: 16 March 2016 / Published: 18 March 2016
(This article belongs to the Section Advanced Composites)
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Abstract

:
FePt-Ag nanocomposite films with large perpendicular magnetic anisotropy have been fabricated by alternate-atomic-layer electron beam evaporation onto MgO(100) substrates at the low temperature of 300 °C. Their magnetization behavior and microstructure have been studied. The surface topography was observed and varied from continuous to nanogranular microstructures with insertion of Ag nanolayers into Fe/Pt bilayer films. The measurement of angular-dependent coercivity showed a tendency of the domain-wall motion as a typical peak behavior shift toward more like a coherent Stoner-Wohlfarth rotation type with the insertion of Ag nanolayers into the FePt films. On the other hand, the inter-grain interaction was determined from a Kelly-Henkel plot. The FePt film without insertion of Ag nanolayers has a positive δM, indicating strong exchange coupling between neighboring grains, whereas the FePt film with insertion of Ag nanolayers has a negative δM, indicating that inter-grain exchange coupling is weaker, thus leading to the presence of dipole interaction in the FePt–Ag nanogranular films. The magnetic characteristic measurements confirmed that the perpendicular magnetization reversal behavior and related surface morphology of low-temperature-ordered FePt(001) nanogranular films can be systematically controlled by the insertion of Ag nanolayers into the FePt system for next generation magnetic storage medium applications.

1. Introduction

Nanogranular magnetic materials with a perpendicular magnetic easy axis have the most potential as candidates for application in ultrahigh-density magnetic storage media due to the fact that areal recording density of hard disk drives (HDDs) needs to be increased to meet the requirement to store exponentially increasing digital data information. The currently used Co-based compounds media do not have enough thermal stability to resist thermal fluctuation and demagnetization effects due to the material intrinsic property of their magnetocrystalline anisotropy constant (Ku). In order to satisfy the future storage requirement, high-Ku materials have been considered as a possible solution that could maintain enough thermal stability not only to delay the superparamagnetic effect but also overcome thermal fluctuation [1,2]. The L10-ordered FePt intermetallic phase with excellent material intrinsic properties such as high Ku ~ 7 × 107 erg/cm3, μ0Ms ~ 1.43 T, and energy products’ BH values has undergone rapid development up to now due to its promising applications including monolithic microwave integrated circuits, spin electronic devices, and next generation ultrahigh-density magnetic information storage media [3,4,5,6,7,8,9,10,11]. However, the formation of the L10-ordered FePt phase usually requires an elevated treatment of either a substrate heating or a post-annealing temperature higher than 500 °C, which also results in the large grain size distribution and is not favorable for industrial productions. The large grains with a strong inter-grain coupling interaction will cause high read/write noises in the recording medium. Many approaches have been reported to use single-crystal substrates or optimum buffer/seed layers in order to form (001) textured Fe-based compound phases with preferred out-of-plane direction with the magnetic anisotropy that is perpendicular to the film plane [12,13,14,15,16,17,18,19,20,21,22,23,24]. For example, Speliotis et al. used MgO/Cr bilayers as a buffer layer to fabricate a (001) textured FePt film on amorphous glass substrate that exhibited good perpendicular anisotropy [25]. The method of Fe/Pt multilayer growth also used in this work can effectively lower the ordering temperature of martensite-based phase transformation from face-centered-cubic (fcc-disordered) to face-centered-tetragonal (fct-ordered) state due to the faster Pt and Fe atoms to interdiffuse at the Fe/Pt interface to form a chemically L10-FePt compound phase [26,27,28,29,30,31,32]. FePt alloy films added with Ag-top, Ag-under, and Ag-doped methods have been reported not only to improve the ordering phase transformation, but have also been employed as the seed of promoting the (001) preferred crystallographic orientation of FePt films [33,34,35,36,37,38,39,40,41]. The Ag element was also used to serve as a matrix phase to separate FePt grains due to immiscible Ag atoms from the FePt alloy. Even many works reported the microstructure modulation of the FePt-Ag system by the inactive atomic mobility of FePt reacted with Ag, but the corresponding evolution of the perpendicular magnetization reversal mechanism of the FePt-Ag nanocomposite structures is still deficient [42,43,44,45,46]. Due to the inactive atomic mobility of the FePt phase, the perfectly continuous film structures are usually formed at growth temperatures below 600 °C [47,48]. Thus, the high formation temperature is needed to achieve a granular structure of the ordered FePt with high coercivity, which is not suitable for industrial productions. The purpose of this work is to explore and control the exchange coupling interaction between the neighboring grains and formation of granular FePt films at a low substrate heating temperature without any post-annealing which is just formed by employing the insertion of Ag nanolayers. In this present article, a method for the fabrication of FePt nanogranular films with (001) crystallographic orientation along with the insertion of Ag nanolayers was employed to promote this self-organized nanogranular structure at a low process temperature of 300 °C. This work shows a significant performance for FePt films inserted with Ag nanolayers on the perpendicular magnetization behavior and microstructure control, and the corresponding intergranular exchange coupling and magnetization mechanism of the FeP–Ag nanocomposite films are also discussed.

2. Experiments and Multilayer Film Structures

FePt binary alloy films are composed of [Fe(0.5 nm)/Pt(0.5 nm)]18 repeated periodic structures with 18 bilayers, and this means that 0.5 nm layers of Fe and Pt were deposited alternately for a total nominal thickness of 18 nm onto MgO(100) single-crystal substrates without any buffer layer via an electron beam evaporation system under a vacuum of 2 × 10−8 Torr. The FePt–1Ag sample, after 9 nm of FePt, had an ultrathin 0.5 nm layer of Ag inserted, so there was a single 0.5 nm layer of Ag inside the 18 nm of FePt. The FePt–2Ag sample, after each 6 nm of FePt, had an ultrathin 0.5 nm layer of Ag inserted, so there were two Ag nanolayers inside the 18 nm of FePt. The FePt–Ag nanocomposite structures were formed and all the details are listed in Table 1. All multilayer film structures were evaporated at a low substrate heating temperature of 300 °C with an evaporation rate of around 0.01 nm/s. The crystallographic orientation and structural characterization of FePt films were evaluated by ex situ X-ray diffraction (XRD) with Cu Kα radiation. The surface morphology of the FePt films was observed by the field emission scanning electron microscope (FE-SEM), and all grain analyses were acquired and processed using the digital micrograph (DM) software. The magnetic characteristics were measured by the vibrating sample magnetometer (VSM) with a maximum applied field of 20 kOe at room temperature. All the measurements were focused on the Fe/Pt multilayer film structures without and with insertion of two ultrathin Ag nanolayers, which was done in order to explore the perpendicular magnetization reversal mechanism of the FePt system with the insertion of Ag nanolayers accompanied by continuous to nanogranular microstructure types.

3. Results and Discussion

Figure 1 shows the FE-SEM images for the [Fe/Pt]18 multilayer films (Figure 1a) without and (Figure 1b) with the insertion of two ultrathin Ag (0.5 nm each) nanolayers, respectively. The grain size histograms for evaluating the average size and distribution of the FePt films without and with the insertion of Ag nanolayers are shown in Figure 1c,d corresponding to Figure 1a,b, respectively. A clear change in the surface morphology of the FePt films is observed and modified with the insertion of Ag nanolayers, and the average grain size of the FePt decreases with the insertion of Ag. The grains of the FePt film without the insertion of Ag are connected with each other, and the structure appears like a continuous film, as shown in Figure 1a. On the other hand, the surface morphology transforms from continuous to nanogranular structures in the FePt with the insertion of Ag nanolayers as shown in Figure 1b. It indicates that the continuous growth of the pure FePt film is interrupted by the insertion of the Ag nanolayers and results in the formation of nanogranular FePt grains with (001) preferred crystallographic orientation. FePt L10 anisotropic rectangular-like nanogranular grains with the insertion of Ag are aligned along the direction of MgO[100] with (001) preferred orientation, and the major facet planes are (100) and (010), as shown in Figure 1b. The nanograin boundaries of FePt-Ag domain particles will work as functional pinning sites to enhance coercivity effectively. The grains in the fraction in Figure 1a range in size from 42 to 60 nm, with an average size of 51 ± 9 nm, as shown in Figure 1c; the grains in the fraction in Figure 1b contain grains ranging in size from 12 to 22 nm, with an average size of 17 ± 5 nm, as shown in Figure 1d. The grain size histograms for fractions are shown in Figure 1c,d and confirm a significant degree of FePt size reduction with the insertion of Ag nanolayers. The FePt–Ag nanocomposite films with nanogranular microstructure composed partial single-domain particles with sizes of tens of nanometers. Hence, the magnetization reversal process could be relative closer to the coherent rotation. The pure FePt film with a continuous microstructure will belong to the magnetic domain wall displacement; in other words, it is a closer multidomain structure.
Figure 2 shows the out-of-plane (full symbols) and in-plane (open symbols) magnetization curves for the [Fe/Pt]18 multilayer films (Figure 2a) without and with the insertion of (Figure 2b) a single and (Figure 2c) two ultrathin Ag (0.5 nm each) nanolayers, respectively. Compared with the out-of-plane and in-plane magnetization curves, it is clear shown that the out-of-plane direction is the magnetic easy axis. The perpendicular anisotropy manifests for all FePt films without and with the insertion of ultrathin Ag nanolayers. The out-of-plane coercivity, magnetic squareness, saturation magnetization, and uniaxial magnetic anisotropy energy (Ku) values for FePt films without and with the insertion of ultrathin Ag nanolayers are apparently different. The clear Ag insertion effects and their corresponding magnetic data are listed in Table 1. The perpendicular magnetization reversal behavior and the microstructure effect of FePt films without and with the insertion of ultrathin Ag nanolayers will be investigated and discussed below.
The obvious variation of the magnetization processes in FePt films without and with the insertion of two ultrathin Ag nanolayers is clearly demonstrated by the initial magnetization curves, as shown in Figure 3. The out-of-plane coercivity of the pure FePt shows a value of 2998 Oe (without Ag), as shown in Figure 3a and listed in Table 1. It is clearly shown that with the insertion of a single and two ultrathin Ag nanolayers into 18 nm FePt multilayer films, the out-of-plane coercivity increases to 4220 and 5264 Oe, respectively. The out-of-plane saturation magnetization (Ms﬩) value decreased with the insertion of a single and two Ag nanolayers into the FePt system, ranging from 950 to 900 emu/cm3 and 875 emu/cm3, and the remanent magnetization (Mr﬩) also decreased from 932 to 876 emu/cm3 and 835 emu/cm3 following the slope of Ms. This result can be understood as Ag is a non-magnetic element, and it slightly dilutes the magnetization of the FePt films. The uniaxial magnetic anisotropy energy (Ku) also slightly decreased from 2.5 × 107 to 2.3 × 107 erg/cm3 and 2.1 × 107 erg/cm3 with the FePt insertion of single and two Ag nanolayers, which was due to the crystallographic texture and misalignment of the anisotropy axis of the FePt changing slightly due to the insertion of Ag. The out-of-plane remanent squareness ratio (Mr﬩/Ms﬩) for the pure FePt was close to unity (0.98), and decreased to 0.97 and 0.95 with the insertion of a single and two Ag nanolayers into the FePt system, which implied the decrease of the exchange coupling of the FePt system with the insertion of Ag nanolayers. The normalized initial magnetization curve will be used to elucidate the magnetization reversal mechanism, as shown in Figure 3b. For the FePt films with the insertion of Ag nanolayers, they became much harder to saturate compared the pure FePt films at the same applied magnetic field. It could be understood if the magnetization reversal behavior was dominated by pinning sites, and the domain wall movement would not move unless the external applied magnetic field was larger than the pinning field. If the magnetization reversal behavior is close to the rotation of the Stoner-Wohlfarth (S-W) mode, the single domain grains only reversed their magnetization behavior when the external applied magnetic field exceeded the anisotropy energy [49,50,51,52,53]. Thus, the pure FePt film without the insertion of Ag nanolayers shows a close to nucleation type of initial magnetization curve, and FePt film with the insertion of Ag nanolayers shows a close to typical pinning type of initial magnetization curve.
For the purpose of understanding the magnetization reversal behavior of the FePt films without and with ultrathin Ag nanolayer dependence, the angular dependence of coercivity for the FePt multilayer films without and with the insertion of a single and two Ag nanolayers was explored, as shown in Figure 4. The ideally theoretical Kondorsky (incoherent switching by domain wall motion in highly exchange coupled systems) and Stoner-Wohlfarth (S-W, coherent rotation for isolated particles) models are two boundary conditions also shown in Figure 4. The angular dependence of the coercivity profile for the FePt film without the insertion of Ag shows a typical peak behavior, which is closer to the domain-wall-motion mode; in other words, it is closer to multidomain structures. When the FePt films were inserted with a single and two Ag nanolayers, the profiles were more similar to coherent S-W rotation and less similar to domain-wall motion due to the Ag element which could decouple the inter-grain exchange coupling between the FePt neighboring grains. Thus, the magnetization reversal behavior of FePt–Ag nanocomposite films becomes more independently associated with incoherent rotation. The tendency is toward weakened domain-wall motion behavior, while an enhanced rotation mode is found in the perpendicular magnetization reversal process for the FePt–Ag nanocomposite system.
Figure 5 shows the Kelly-Henkel plot (δM measurement) for FePt films without and with the insertion of two ultrathin Ag nanolayers, respectively. The δM measured mode is used to determine the inter-grain interaction in many hard magnetic materials, which is defined as [54,55,56]:
δM = MDCD(H) − [1 − 2MIRM(H)]
where MDCD(H) and MIRM(H) are the normalized dc-demagnetization remanence and isothermal remanence as a function of the external magnetic field, respectively. The positive δM peak indicates ferromagnetic inter-grain interactions. On the other hand, the negative δM peak exhibits dipole interactions associated with incoherent rotation. It can be seen from Figure 5 that FePt film without the insertion of Ag has a positive δM (strong ferromagnetic interaction), whereas FePt film with the insertion of Ag nanolayers has a negative δM at all applied magnetic fields (dipole interaction). The parameter δM value is well known to lead media noise, and this value of δM can be simply controlled by the insertion of Ag nanolayers into the FePt system in this work. The reduction of exchange interactions between neighboring grains in the FePt films has been achieved by controlling the insertion of Ag nanolayers, and a lower value of δM is desirable. The above results suggested that the microstructure and the magnetization reversal mechanism including inter-grain exchange coupling of the FePt(001) films could be tuned and affected by the insertion of Ag nanolayers into the Fe/Pt multilayers. This is due to the microstructural modification of FePt films promoted by the insertion of Ag nanolayers even at a low processing temperature of 300 °C, so the inter-grain exchange coupling weakened and the corresponding magnetic reversal mechanism changed.
Figure 6 shows the X-ray diffraction patterns for the [Fe/Pt]18 multilayer films (Figure 6a) without and (Figure 6b) with the insertion of two ultrathin Ag nanolayers directly evaporated onto MgO(100) substrates, respectively.
The slow scan curves of the FePt(002) diffraction peak in the θ–2θ scan as shown in Figure 6c,d correspond to Figure 6a,b, respectively. In addition to the fundamental (002) peak, the (001) superlattice peak of the L10-ordered FePt phase has been clearly observed for both films. The unlabeled sharp peaks are due to the MgO(001) single-crystal substrate. In Figure 6, no peaks except the (00n) diffraction peaks are observed in the whole diffraction patterns (θ–2θ scan), indicating the Fe/Pt multilayer film structures without and with the insertion of Ag nanolayers are strongly textured to the (001) planes, and this also confirms the structures did epitaxially grow onto the MgO substrates. The FePt peaks are relatively broad for the FePt films with the insertion of Ag nanolayers compared to the FePt without Ag. Additionally, the full width at half maximum (FWHM) value of the slow scan curves of FePt(002) for FePt with the insertion of Ag (1.647°) is larger than that of pure FePt without Ag (1.447°), as shown in Figure 6c,d. According to the results mentioned above, which indicate the grain size of FePt films is decreased with the insertion of Ag nanolayers into the FePt films, this fact is consistent with the FE-SEM observation.

4. Conclusions

The perpendicular magnetization reversal behavior and the exchange-coupling interaction of the low-temperature-ordered FePt films without and with the insertion of Ag nanolayers have been successfully demonstrated. The grain size and corresponding inter-grain interaction of the FePt alloy films can be reduced by the insertion of ultrathin Ag nanolayers into the FePt system. The most notable effect of the insertion of Ag nanolayers into FePt is that the surface topography changes from continuous to nanogranular microstructures. The coercivity improvement is mainly due to the formation of nanogranular FePt grains induced by the insertion of Ag nanolayers. The change in the magnetization process from less similar to domain wall displacement to more similar to the rotation mode with the insertion of Ag nanolayers into the FePt system was clearly demonstrated as the surface topography varied from continuous to nanogranular microstructures. This research work could provide a simple method for fabricating nanogranular FePt(001) films via the insertion of Ag nanolayers and with tunable related magnetization reversal behavior in general at a relatively low processing temperature of 300 °C in the potential industrial development for ultrahigh-density perpendicular spin electronic devices and information storage medium applications.

Acknowledgments

The author (Da-Hua Wei) acknowledges financial support of the main research projects of the Ministry of Science and Technology (MOST) under Grant Nos. 104-2221-E-027-006 and 104-2731-M-027-001.

Conflicts of Interest

The author declares no conflict of interest.

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Materials 09 00209 g001 1024
Figure 1. Field emission scanning electron microscope (FE-SEM) surface morphology images for the [Fe/Pt]18 multilayer films (a) without and (b) with two ultrathin Ag (0.5 nm each) nanolayers. The corresponding grain size histograms for evaluating average size and distribution of the FePt films (c) without and (d) with insertion of two Ag nanolayers are related to (a) and (b), respectively.
Figure 1. Field emission scanning electron microscope (FE-SEM) surface morphology images for the [Fe/Pt]18 multilayer films (a) without and (b) with two ultrathin Ag (0.5 nm each) nanolayers. The corresponding grain size histograms for evaluating average size and distribution of the FePt films (c) without and (d) with insertion of two Ag nanolayers are related to (a) and (b), respectively.
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Figure 2. Out-of-plane and in-plane magnetization curves for the [Fe/Pt]18 multilayer films (a) without and with insertion of (b) a single and (c) two ultrathin Ag (0.5 nm each) nanolayers denoted as FePt–1Ag and FePt–2Ag, respectively. The magnetic field was applied in the out-of-plane direction (full symbols, ●) and in the in-plane direction (open symbols, o) to the film, respectively.
Figure 2. Out-of-plane and in-plane magnetization curves for the [Fe/Pt]18 multilayer films (a) without and with insertion of (b) a single and (c) two ultrathin Ag (0.5 nm each) nanolayers denoted as FePt–1Ag and FePt–2Ag, respectively. The magnetic field was applied in the out-of-plane direction (full symbols, ●) and in the in-plane direction (open symbols, o) to the film, respectively.
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Figure 3. (a) Out-of-plane magnetization curves and corresponding (b) normalized initial magnetization curves for the [Fe/Pt]18 multilayer films without and with insertion of two ultrathin Ag (0.5 nm each) nanolayers.
Figure 3. (a) Out-of-plane magnetization curves and corresponding (b) normalized initial magnetization curves for the [Fe/Pt]18 multilayer films without and with insertion of two ultrathin Ag (0.5 nm each) nanolayers.
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Figure 4. Angular dependence of coercivity for the [Fe/Pt]18 multilayer films without and with insertion of a single and two ultrathin Ag (0.5 nm each) nanolayers. The angle is referred to that between the easy axis (film normal) and the applied field direction.
Figure 4. Angular dependence of coercivity for the [Fe/Pt]18 multilayer films without and with insertion of a single and two ultrathin Ag (0.5 nm each) nanolayers. The angle is referred to that between the easy axis (film normal) and the applied field direction.
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Figure 5. Kelly-Henkel (δM) plot for the [Fe/Pt]18 multilayer films without and with insertion of two ultrathin Ag (0.5 nm each) nanolayers. The magnetic field was applied in the out-of-plane direction to the film.
Figure 5. Kelly-Henkel (δM) plot for the [Fe/Pt]18 multilayer films without and with insertion of two ultrathin Ag (0.5 nm each) nanolayers. The magnetic field was applied in the out-of-plane direction to the film.
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Figure 6. X-ray diffraction scan patterns (XRD) for the [Fe/Pt]18 multilayer films (a) without and (b) with two ultrathin Ag (0.5 nm each) nanolayers. The corresponding slow scan curves of the FePt (002) peak in the θ–2θ scan (c) without and (d) with insertion of two Ag nanolayers are related with (a) and (b), respectively.
Figure 6. X-ray diffraction scan patterns (XRD) for the [Fe/Pt]18 multilayer films (a) without and (b) with two ultrathin Ag (0.5 nm each) nanolayers. The corresponding slow scan curves of the FePt (002) peak in the θ–2θ scan (c) without and (d) with insertion of two Ag nanolayers are related with (a) and (b), respectively.
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Table
Table 1. Out-of-plane coercivity (Hc﬩) saturation magnetization (Ms﬩), remanent magnetization (Mr﬩), remanent squareness ratio (Mr﬩/Ms﬩), and uniaxial magnetic anisotropy energy (Ku) values for the [Fe/Pt]18 multilayer films without and with the insertion of a single and two ultrathin Ag (0.5 nm each) nanolayers.
Table 1. Out-of-plane coercivity (Hc﬩) saturation magnetization (Ms﬩), remanent magnetization (Mr﬩), remanent squareness ratio (Mr﬩/Ms﬩), and uniaxial magnetic anisotropy energy (Ku) values for the [Fe/Pt]18 multilayer films without and with the insertion of a single and two ultrathin Ag (0.5 nm each) nanolayers.
Structures (Denoted)Film Structures (Thickness nm)Hc﬩ (Oe)Ms﬩ (emu/m3)Mr﬩ (emu/m3)Mr﬩/Ms﬩ (ratio)Ku (erg/m3)
FePt[Fe/Pt]1829989509320.982.5 × 107
FePt–1Ag[Fe/Pt]9/Ag0.5/[Fe/Pt]942209008760.972.3 × 107
FePt–2Ag[Fe/Pt]6/Ag0.5/[Fe/Pt]6/Ag0.5/[Fe/Pt]652648758350.952.1 × 107

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Wei, D.-H. Perpendicular Magnetization Behavior of Low- Temperature Ordered FePt Films with Insertion of Ag Nanolayers. Materials 2016, 9, 209. https://doi.org/10.3390/ma9030209

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Wei D-H. Perpendicular Magnetization Behavior of Low- Temperature Ordered FePt Films with Insertion of Ag Nanolayers. Materials. 2016; 9(3):209. https://doi.org/10.3390/ma9030209

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Wei, Da-Hua. 2016. "Perpendicular Magnetization Behavior of Low- Temperature Ordered FePt Films with Insertion of Ag Nanolayers" Materials 9, no. 3: 209. https://doi.org/10.3390/ma9030209

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Wei, D. -H. (2016). Perpendicular Magnetization Behavior of Low- Temperature Ordered FePt Films with Insertion of Ag Nanolayers. Materials, 9(3), 209. https://doi.org/10.3390/ma9030209

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