Journal of Nanomaterials

Volume 2012 (2012), Article ID 154192, 5 pages

doi:10.1155/2012/154192

Research Article

Effects of Annealing Temperature on Structure and Magnetic Properties of ( and 0.4) Thin Films

N. B. Ibrahim, Ftema W. Aldbea, and Mustaffa Hj Abdullah

School of Applied Physics, Faculty of Science and Technology, Universiti Kebangsaan Malaysia, 43600 Bangi, Malaysia

Received 14 January 2012; Revised 15 February 2012; Accepted 29 March 2012

Academic Editor: Weichang Hao

Copyright © 2012 N. B. Ibrahim et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

Abstract.

Terbium-substituted yttrium iron garnet ( ( and 0.4)) thin films have been successfully prepared by a sol-gel method followed by spin-coating process. The annealing of the films was performed at different temperatures like 700, 800, and and found that the films annealed at turned out to be crystallized into a pure garnet phase. All of the films were bearing grains of nanometer in size. Increasing the annealing temperature gave extra energy to the grains causing to be agglomerates. The lattice contraction occurred as the grain’s sizes were decreased due to the decrease of Fe²⁺ formation. The magnetic measurements show that all of the films are soft magnetic materials with low saturation magnetization values. The hysteresis loops of the films which were annealed at were found angular in shape similar to the single crystal-like YIG film.

1. Introduction

Yttrium iron garnet (Y₃Fe₅O₁₂, YIG) and its rare-earth-substituted films have been progressively studied due to their wide potential applications, such as in telecommunication and magneto-optical devices [1]. Y site in YIG has been substituted with different materials such Bi, Ca, and Ce [2–4]. Bulk Tb-substituted YIG (Tb-YIG) has the potential in sensor application. However there are few published reports on it [5–7] and none of them report the material in the thin film form. Marins et al. [5] have reported that the magnetic properties of powder calcined at 1000°C depend on the sintering temperature, and also the small coercive field value is related to the increased sintering temperature. Guillot et al. [6] have studied the magnetization of in polycrystalline and single crystal form at magnetic field of 180 kOe. They found that, in case of the polycrystalline (), the compensation points depend on the Tb concentration while for the single crystals () a strong magnetic anisotropy was observed with the change of easy direction of magnetization from to when was decreased. They also reported occurrence of abrupt field-induced transitions at low temperature when the external field was applied along the direction. Rodić et al. [7] reported that the compensation temperature of (, and 3) powder was proportional to the concentration of the terbium ion.

This paper reports the preparation of ( and 0.4) thin films by a cheap, and simple method, that is a sol-gel method followed by spin coating process. In order to obtain crystalline films, annealing process was employed. The effects of annealing temperature on the structures and magnetic properties of the films were studied.

2. Experimental Procedure

Yttrium (III) nitrate hexahydrate Y(NO₃)₃·6H₂O with 99.99% purity and iron (III) nitrate nanohydrate Fe(NO₃)₃·9H₂O with 98.0% purity were first dissolved in 2-methaoxythanol and refluxed at 80°C for 3 hours. The doping agent in the form of Tb(COOCH₃)₃·H₂O with 99.9% purity was first dissolved in 1 mL acetic acid and then added to the yttrium and iron solution. The ratio of yttrium and terbium was altered in order to obtain Tb0.2Y2.8Fe₅O₁₂ and Tb0.4Y2.6Fe₅O₁₂ solution followed by addition of 1 mL distilled water and 3 mL of nitric acid. Diethylamine was added to the solution to obtain a pH 3 solution. The solution was again refluxed at 80°C for 3 hours.

To obtain the films, 25 μL of the gel was dropped onto a clean quartz substrate. Using a spin coater, the substrate was spin first at 500 rpm for 15 seconds, then at 3500 rpm for 30 seconds. The film was heated at 90°C for 2 hours to get rid of residual solvent, and followed by 350°C for 15 min at heating rate of 3°C/min to burn-off the organic compounds. Then both Tb0.2Y2.8Fe₅O₁₂ and Tb0.4Y2.6Fe₅O₁₂ films were annealed at 700, 800 and 900°C in order to study the effect of the annealing temperature on their physical properties. The films were identified as series 1 for Tb0.2Y2.8Fe₅O₁₂ and series 2 for Tb0.4Y2.6Fe₅O₁₂ films.

An X-ray diffractometer (XRD) with Cu-Kα radiation was used to study the film’s structures and phases. A field emission scanning electron microscopy (FE SEM) was used to measure the grain’s size and thicknesses of the films. A vibrating sample magnetometer (VSM) was used to study the in-plane magnetic properties of the films.

3. Results and Discussion

The XRD results in Figures 1 and 2 show that both series were crystallized into pure YIG phase after being annealed at 900°C. The films which were annealed at temperatures less than 900°C were displaying mixed phases of YIG, Fe₂O₃, and YFeO₃ because of incomplete crystallization. No peaks belonging to Tb₂O₃ were found in the results, thus indicating the incorporation of Tb atoms in the garnet structure.

Figure 1: XRD spectrum for series 1 film.

Figure 2: XRD spectrum for series 2 film.

The lattice parameters for both series were calculated from the XRD spectra and Bradley and Jay’s extrapolation method was employed to minimize the errors [8]. The lattice parameter value for each was obtained and a graph presenting the lattice parameter versus was plotted. The extrapolated value at the -axis was considered as the desired value. While the films annealed at 700 and 800°C were displaying mixed phases, only the of Tb-YIG was used to calculate the lattice parameter. Figure 3 shows the results for both series. The lattice parameter of both series was increased with the increase in annealing temperature. Similar results have also been reported for nanoparticle oxide system [9, 10]. According to Rajendran et al. [11], oxygen vacancies can occur at the particle’s surface during the film preparation and may cause the formation of Fe²⁺. The oxygen vacancies could occur due to the preparation condition. The annealing processes were carried out in air; thus increasing the annealing temperature could promote the formation of Fe²⁺ ions. As Fe²⁺ ions are larger than Fe³⁺, the increment of their formation will further expand the unit cell. To confirm this, XPS measurements were performed on the films annealed at 900°C. Figure 4 is clearly exhibiting the results confirming the formation of Fe²⁺ in both films.

Figure 3: The plot of lattice parameter versus annealing temperature for series 1 and 2.

(a)

(b)

Figure 4: The XPS spectra for films annealed at 900°C.

The thickness of the films was measured from the film’s cross section. The films were cut and the back scattered images from the cross sections were taken using the FESEM. Figure 5 shows the typical FESEM cross-section a micrograph of a Tb-YIG film showing different contrast of the film and substrate. Figure 6 shows that the thickness decreases as the temperature increases for series 1 (). The thinning of the films as the temperature increases could be due to the densification process, where the small empty spaces or pores were filled by the grains [12]. However for series 2 (), increasing annealing process from 700 to 800°C increases the film thickness due to the increment of the grains (see Figure 8). Further temperature increment to 900°C decreases the film thickness due to the densification process.

Figure 5: A typical cross-sectional view of a Tb-YIG film () showing the contrast (back scattered electron) between the film and substrate.

Figure 6: The relation between film thickness and annealing temperature for series 1 and 2.

The grains sizes were measured from the surface micrographs obtained from the FESEM. Figure 7 shows the FE SEM micrographs of Tb0.2Y2.8Fe₅O₁₂ and Tb0.4Y2.6Fe₅O₁₂ films annealed at 900°C. The relation between grain size and annealing temperature is shown in Figure 8. All of the films have grains sizes in nanometer range (9–60 nm). Both series show a similar graph pattern. The grains become larger as the annealing temperature increases. The nanometer size grains possess large overall surface area which means that their total surface energy is also high. However the energy can be minimized when the annealing process was carried out, thus allowing the grains to agglomerate. Further increasing the annealing temperature reduced the surface energy of the grains and thus allowed them to become more agglomerate.

(a)

(b)

Figure 7: FESEM micrographs of Tb0.2Y2.8Fe₅O₁₂ and Tb0.4Y2.6Fe₅O₁₂ films, annealed at 900°C.

Figure 8: The relation between particle size and annealing temperature for series 1 and 2.

The VSM was used to measure the in-plane magnetic properties of both series at room temperature (25°C). No demagnetization corrections were required as the films were very thin compared to the lateral dimensions; hence the in-plane demagnetization was leaned towards zero. However the linear ramp due to the paramagnetic quartz substrate was subtracted from the data. Figures 9 and 10 show the hysteresis loops of series 1 and 2, respectively. The samples are soft magnetic materials with low saturation magnetization () values. Also the films annealed at 900°C show angular shape hysteresis loops which are similar to those reported by Ibrahim et al. [4] for their single crystal-like YIG film. Their film’s easy axis does not lie in the film plane. The angular hysteresis shows that it is possible to magnetize in-plane up to certain limit () by growth of easy domains giving the initial steep region. Further magnetization would need rotation away from the easy directions giving the second stage which is the harder process. As shown in Figure 11 the of both series increase with the annealing temperature. Tb0.2Y2.8Fe₅O₁₂ and Tb0.4Y2.6Fe₅O₁₂ films annealed at 700 and 800°C have similar ; the low values of magnetization could be due to the existence of the antiferromagnetic Fe₂O₃ phase in the samples. Increasing the annealing temperature improves the film crystallization and thus increases the ; however it is lower than 138.3 emu/cm³ for YIG film containing micrometer grain size range [13]. Similar reduction has also been reported by Sánchez et al. for their nanograin YIG. Nanograin YIG possesses high surface-to-volume ratio; thus increasing the surface spin effects the films [14].

Figure 9: The hysteresis loop of series 1.

Figure 10: The hysteresis loop of series 2.

Figure 11: The plot of versus annealing temperature of both series.

Figure 12 shows the plot of coercivity field () versus annealing temperature of both series. It can be clearly seen that both series show similar trends. The becomes smaller as the annealing temperature increases. As measured from the FE SEM images, the increment in annealing temperature led to bigger grain sizes. Theoretically it has been proved that the coercivity of small particle () is proportional to ( is the particle size and is a constant that lies between and 1) [15]. The increment of grain size with the annealing temperature also reduced the strain in the films resulting in reducing the values.

Figure 12: The plot of versus annealing temperature of both series.

4. Conclusion

The structure and magnetic properties of Tb0.2Y2.8Fe₅O₁₂ and Tb0.4Y2.6Fe₅O₁₂ films prepared onto quartz substrates by a sol-gel method followed by spin-coating process have been reported. The films subjected to the annealing temperature of 900°C were found to be crystallized into pure garnet phase. The films have grains sizes in the range of 9–60 nm. Increment in the annealing temperature from 700 to 900°C led to the increased formation of Fe²⁺. The films annealed at 900°C show hysteresis loops similar to the single crystal-like YIG. Although the substitution of Tb ions into YIG films reduced their values, the films have potential in microwave application due to their low coercivity values and soft magnetic nature.

Acknowledgments

This work was supported by Malaysian Ministry of Science, Technology and Innovation via science fund Grant 03-01-02-SF0538. The authors would like to thank Mr. Mohamad Azri Tukimon for XPS analysis and Mr. Mohamad Hasnul Naim for FE-SEM measurements.

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