Journal of Nanoscience

Volume 2014 (2014), Article ID 158946, 5 pages

http://dx.doi.org/10.1155/2014/158946

Research Article

Characterization of Erbium Substituted Yttrium Iron Garnet Films Prepared by Sol-Gel Method

Ramadan E. Shaiboub¹ and N. B. Ibrahim²

¹Physics Department, Faculty of Education, University of Algabel Alghrbi, Nalut, Libya

²School of Applied Physics, Faculty of Science and Technology, Universiti Kebangsaan Malaysia, 43600 Bangi, Selangor, Malaysia

Received 21 November 2013; Revised 4 March 2014; Accepted 13 March 2014; Published 6 April 2014

Academic Editor: Stephane Daniele

Copyright © 2014 Ramadan E. Shaiboub and N. B. Ibrahim. 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.

Yttrium iron garnet (YIG) thin films substituted erbium ions (Er⁺³) Er0.4Y2.6Fe₅O₁₂ films were prepared by a sol-gel method at different temperatures which varied from 800 to 1000°C for 2 hours in air. Magnetic and microstructural properties of the films were characterized with X-ray diffraction (XRD), the field emission scanning electron microscopy (FESEM), and vibrating sample magnetometer (VSM). The XRD patterns of the sample have only peaks of the garnet structure. The lattice constants decrease, while the particle size increases from 51 to 85 nm as the annealing temperature increases with average in thickness of 300 nm. The saturation magnetization and the coercivity of the samples increased from 26 (emu/cc) and 28 Oe for the film annealed at 800°C to 76 (emu/cc) and 45 Oe for film annealed at 1000°C, respectively.

1. Introduction

The study of yttrium iron garnet (YIG) thin films is becoming more important because of properties that can be extensively used in optical communication [1], magneto-optical devices, and applied in microwave [2]. YIG is the most representative and well-known compound among the rare-earth garnets and various magnetizations can be achieved by substitution process. Thin and thick films have been produced in garnets using different methods such as liquid phase epitaxy, sputtering, chemical vapor deposition, liquid phase epitaxy, laser ablation, and sol-gel. In recent years, sol-gel methods have attracted much attention due to use of lower synthetic temperature to produce finer and more homogeneous particles. The sol-gel synthetic method has been widely used to prepare nanostructured films and can be used to systematically vary the chemical composition of target compounds over pulsed laser deposition and sputtering techniques which are also compatible with the fabrication of nanoscaled thin films. So in this study, sol-gel method is used to achieve homogeneous systems with respect to the desired metals. YIG is a ferromagnetic material and it has a cubic structure with a space group Ia3d with the general unit formula (Y₃Fe₅O₁₂) [3]. The magnetic ions are distributed over three crystallographic sites with sublattice magnetization Ma [octahedral site, 16 Fe³⁺ ions in a], Md (tetrahedral site, 24 Fe³⁺ ions in d), and Mc {dodecahedral site, 24 Y³⁺ ions in c}. Ionic distribution in garnet is represented as {Y₃³⁺} [Fe₂³⁺] (Fe₃³⁺) . The interaction between the Fe³⁺ ions in [a] and (d) sites is strongly antiferromagnetic due to strong superexchange interaction. The magnetic moment of the rare-earth ions in the {c} sublattice couples antiparallel with the resultant moment of Fe³⁺ ions. In a YIG system, nonmagnetic Y³⁺ ions occupy dodecahedral {c} sites and magnetic Fe³⁺ ions occupy octahedral [a] and tetrahedral (d) sites. The magnetic moment caused by two Fe³⁺ ions in [a] site is aligned antiparallel to that caused by three Fe³⁺ ions in (d) site, leaving a net moment from Fe³⁺ in the d-site. Therefore, the saturation magnetization of YIG is given by the magnetic Fe³⁺ in the d-sites. The paramagnetic trivalent Er³⁺ ions can be substituted for nonmagnetic Y³⁺ ions in {c} sites, but not for Fe³⁺ ions in [a] or (d) sites [4]. The magnetic moment of Er³⁺ substituted for Y³⁺ in {c} sites, which can be parallel to the magnetic moment of Fe³⁺ in the d-sites, meaning that the saturation magnetization of Er:YIG is different from that of pure YIG. A number of researches have been done in substituting Bi³⁺, Ce³⁺ for Y³⁺ and Co³⁺, Co²⁺ for Fe³⁺ in YIG [5–12]. However, some works have been carried out to study Er-YIG powder nanoparticles [13–20] and few in thin film form. Erbium is chosen because its ionic radius (1.03 Å) is slightly less than ionic radius of yttrium (1.04 Å). Also, it has an extremely high verdet constant at (λ = 600 nm) and large Bohr magneton (9.6 μB) [21]. This paper focuses on the influence of low concentration of Er⁺³ ions substituted YIG thin films (Er0.4Y2.6Fe₅O₁₂) at different annealing temperatures.

2. Experimental

The Er:YIG precursor sol was prepared by sol-gel method using reagent grade nitrates purchased from Aldrich, Milwaukee, WI, USA. Yttrium nitrate hexahydrate [Y(NO₃)₃6H₂O, 99.95% purity], iron (III) nitrate nanohydrate [Fe(NO₃)₃9H₂O, 98+% purity], and erbium nitrate pentahydrate [Er(NO₃)₃5H₂O, 99.9%, metals basis] were used as raw materials. 2-Methoxyethanol and acetic acid were used as solvents. Fe(NO₃)₃9H₂O and Y(NO₃)₃6H₂O were dissolved in the 2-methaxythanol and refluxed at 80°C for 3 hours. The Er(NO₃)₃5H₂O dissolved in acetic acid was added gradually into the Fe-Y solution. Then the refluxing process was carried out for 3 hours. A small quantity of diethylamine was added to the mixture solution, while the pH value was adjusted in the range of 2-3. After cooling down to room temperature, the solution was stirred for 3 days. The gel was transformed into thin film form (onto quartz substrates) using the spin coating technique. The rate of the spinning process was 3500 rpm and it was done for 30 second. After the spinning process, the films were heated at 90°C for 2 hours to remove the residual solvents and then at 350°C for 15 min at a heating rate of 3°C/min to burn off the organic materials, followed by annealing process at 800, 900, and 1000°C for 2 hours at a heating rate of 4°C/min to crystallize them as shown in Figure 1. The X-ray diffractions were done at = 20° to 80° to investigate the structural properties of the films. Magnetic measurements were carried out at room temperature using a vibrating sample magnetometer (VSM). The field emission scanning electron microscope (FESEM) was carried out at the magnification of 300,000x to examine the surface quality of the films.

Figure 1: The flowchart of the heat treatment process.

3. Result and Discussions

3.1. X-Ray Diffraction Measurements

Figure 2 shows the XRD spectra for Er0.4Y2.6Fe₅O₁₂ films annealed at 800–1000°C for 2 hours. All of the samples show single phases of the garnet structure with diffraction lines (hkl) corresponding to the cubic garnet structure. We obtained the single garnet phase at 800°C due to the good homogeneity of the gel prepared at pH = 2-3, while the single garnet phase of ErxY3−xFe₅O₁₂ () prepared by [22] was obtained at 850°C. The values of lattice constant of the films calculated from the XRD pattern were in the range of 12.339 to 12.359 Å and were found a little smaller than the pure YIG (12.376 Å) due to the ionic radii of Er³⁺   less than Y³⁺  . The effect of the heat treatment has been studied by several researches. They observed that the lattice parameter decreases with increasing heat treatment temperature [23]. The average lattice constants values of Er0.4Y2.6Fe₅O₁₂ films as a function of different annealing temperatures are shown in Table 1.

Table 1: The variation of annealing temperature with the coercivity (Hc), magnetization (), particle size, and lattice constants.

Annealing temp. (°C)
Hc (Oe)
(emu/cc)
Average particle size (nm)
Average lattice constants (Å)

800
28
26
51
12.359

900
36
60
59
12.358

1000
45
76
85
12.339

Figure 2: The XRD patterns of Er0.4Y2.6Fe₅O₁₂ films annealed for 2 h at different temperatures.

3.2. Microstructural Properties

The microstructures of all of the Er0.4Y2.6Fe₅O₁₂ films were studied using field emission scanning electron microscope (FESEM) as shown in Figures 3(a)–3(c). The particle size obtained for these samples increases with the annealing temperature increased. From the images of the FESEM micrograph, the resulting grains show that the particles stuck to each other when the annealing temperature is above 800°C and this implies that the particles are highly agglomerate due to their high surface energy [24]. The micrographs show that the particles stuck together, and these hard agglomerates are called aggregates. Agglomeration of fine particles can occur at the synthesis stage, during drying and subsequent processing of the particles. Agglomeration of fine particles is caused by the attractive van der Waals force and the driving force that tends to minimize the total surface energy of the system. The grains could not be seen clearly, and this may be because of masking caused by the gold coating on the film’s surface. The thicknesses of the films were decreased as the annealing increased and ranged from 408 nm to 249 nm. We can conclude that for different annealing temperatures, the crystallite sizes of Er0.4Y2.6Fe₅O₁₂ films are increased, while the films thicknesses were reduced. This is probably due to the different ionic radius of Er³⁺   which is less than Y³⁺  , which leads to some apparent variation about the crystalline lattice.

(a)

(b)

(c)

Figure 3: FE-SEM micrograph and images of cross-section of Er0.4Y2.6Fe₅O12 films at different annealing temperatures: (a) 800°C, (b) 900°C, and (c) 1000°C.

3.3. Magnetic Properties

The magnetic properties of the samples at different annealing temperatures of Er0.4Y2.6Fe₅O₁₂ films were measured using vibration samples magnetometer (VSM) with a maximum applied field of 12 kOe at room temperature. Figure 4 shows the in-plane magnetization properties and typical hysteresis loop for all films. The hysteresis curves indicate that Er0.4Y2.6Fe₅O₁₂ films annealed at 800 to 1000°C are soft magnetic materials. The saturation magnetization () of the films increased from 26 (emu/cc) for the film annealed at 800°C to 76 (emu/cc) for film annealed at 1000°C when the particle size increased from 51 to 85 nm as shown in Table 1 and Figures 5(a) and 5(b). This rise can be related to the higher surface-to-volume ratio in the smaller particles, which results in the existence of nonmagnetization surface layer. Also the of the particles decreases as the particle sizes reduce due to the enhancement of the surface spin effects. The coercivity (Hc) increased from 28 to 45 Oe as the temperature rose to 1000°C as shown in (Figure 5(c)).

Figure 4: The in-plane hysteresis loop for Er0.4Y2.6Fe₅O₁₂ films annealed for 2 h at different annealing temperatures.

(a)

(b)

(c)

Figure 5: The variation of (a) saturation magnetization, (b) particle size, and (c) coercivity with different annealing temperatures.

4. Conclusion

We have studied the synthesis of YIG substituted (Er⁺³) Er0.4Y2.6Fe₅O₁₂ nanoparticles, with size between 51 and 85 nm at different temperatures varied from 800 to 1000°C prepared using a sol-gel method. The results show that, at low concentration of Er³⁺ ion, the best annealing temperature for crystallinity begins at 800°C. From the XRD, it can be observed that all the samples have only a single phase of garnet structure. The average values of lattice constants of the films were decreased as the temperature increased. The particle size obtained for these samples increases with the annealing temperature increasing and the particles are highly agglomerate due to their high surface energy. The saturation magnetization () decreases as the particle size is reduced due to the enhancement of the surface spin effects. The thicknesses of these samples reduced as the annealing rises to 1000°C.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

Acknowledgment

The authors would like to thank the University Kebangsaan Malaysia for the help in providing the instruments and the analytical techniques which are used in this work.

References

A. V. Nazarov, D. Ménard, J. J. Green, C. E. Patton, G. M. Argentina, and H. J. van Hook, “Near theoretical microwave loss in hot isostatic pressed (hipped) polycrystalline yttrium iron garnet,” Journal of Applied Physics, vol. 94, no. 11, pp. 7227–7234, 2003.

T. Aichele, A. Lorenz, R. Hergt, and P. Görnert, “Garnet layers prepared by liquid phase epitaxy for microwave and magneto-optical applications—a review,” Crystal Research and Technology, vol. 38, no. 7-8, pp. 575–587, 2003.

S. Geller and M. A. Gilleo, “The crystal structure and ferrimagnetism of yttrium-iron garnet, Y₃Fe₂(FeO₄)₃,” Journal of Physics and Chemistry of Solids, vol. 3, no. 1-2, pp. 30–36, 1957.

M. S. Lataifeh and A. al-sharif, “Magnetization measurements on some rare-earth iron garnets,” Applied Physics A: Materials Science & Processing, vol. 61, no. 4, pp. 415–418, 1995.

M. Gomi, K. Satoh, and M. Abe, “New garnet films with giant Faraday rotation,” in Proceedings of the 5th International Conference on Ferrites, pp. 919–924, Bombay, India, 1989.

T. Shintaku and T. Uno, “Preparation of Ce-substituted yttrium iron garnet films for magneto-optic waveguide devices,” Japanese Journal of Applied Physics, vol. 35, no. 9, pp. 4689–4691, 1996.

A. Tate, T. Uno, S. Mino, A. Shibukawa, and T. Shintaku, “Crystallinity of Ce-substituted YIG films prepared by RF sputtering,” Japanese Journal of Applied Physics, vol. 35, no. 6, pp. 3419–3425, 1996.

T. Shintaku, A. Tate, and S. Mino, “Ce-substituted yttrium iron garnet films prepared on Gd₃Sc₂Ga₃O₁₂ garnet substrates by sputter epitaxy,” Applied Physics Letters, vol. 71, no. 12, pp. 1640–1642, 1997.

C.-Y. Tsay, C.-Y. Liu, K.-S. Liu, I.-N. Lin, L.-J. Hu, and T.-S. Yeh, “Low temperature sintering of microwave magnetic garnet materials,” Journal of Magnetism and Magnetic Materials, vol. 239, no. 1–3, pp. 490–494, 2002.

H. Hayashi, S. Iwasa, N. J. Vasa et al., “Fabrication of Bi-doped YIG optical thin film for electric current sensor by pulsed laser deposition,” Applied Surface Science, vol. 197-198, pp. 463–466, 2002.

M. Huang and S.-Y. Zhang, “Growth and characterization of cerium-substituted yttrium iron garnet single crystals for magneto-optical applications,” Applied Physics A: Materials Science and Processing, vol. 74, no. 2, pp. 177–180, 2002.

M. C. Sekhar, J.-Y. Hwang, M. Ferrera et al., “Strong enhancement of the Faraday rotation in Ce and Bi comodified epitaxial iron garnet thin films,” Applied Physics Letters, vol. 94, no. 18, Article ID 181916, 2009.

N. I. Tsidaeva, “The magneto-optical activity of rare-earth ion in Y-substituted erbium and neodymium iron garnets,” Journal of Alloys and Compounds, vol. 408–412, pp. 164–168, 2006.

J. Ostoréro and M. Guillot, “High field induced magnetic anisotropy of Al-substituted erbium iron garnet single crystals,” IEEE Transactions on Magnetics, vol. 37, no. 4, pp. 2441–2444, 2001.

P. Novák, V. A. Borodin, V. D. Doroshev, M. M. Savosta, and T. N. Tarasenko, “NMR of ⁵⁷Fe in erbium-yttrium iron garnets,” Hyperfine Interactions, vol. 59, no. 1–4, pp. 427–430, 1990.

P. Feldmann, M. Guillot, H. le Gall, and A. Marchand, “Faraday rotation in erbium-yttrium iron garnet,” IEEE Transactions on Magnetics, vol. 17, no. 6, pp. 3217–3219, 1981.

N. Tsidaeva and V. Abaeva, “The investigation of mechanisms of the magneto-optical activity of rare-earth iron garnet single crystals,” Journal of Alloys and Compounds, vol. 418, no. 1-2, pp. 145–150, 2006.

P. Feldmann, H. le Gall, M. Guillot, and A. Marchand, “Anisotropy of the Faraday rotation in erbium-yttrium iron garnet below the compensation temperature,” Journal of Applied Physics, vol. 53, no. 3, pp. 2486–2488, 1982.

J. Ostoréro and M. Guillot, “Magnetooptical properties of Sc-substituted erbium-iron-garnet single crystals,” Journal of Applied Physics, vol. 83, no. 11, pp. 6756–6758, 1998.

P. Feldmann, H. le Gall, J. M. Desvignes, M. Guillot, and A. Marchand, “Faraday rotation in single crystal erbium iron garnet,” Journal of Magnetism and Magnetic Materials, vol. 21, no. 3, pp. 280–284, 1980.

A. di Biccari, Sol-gel processing of RxY3-xAlyFe5-yO12 magneto-optical films [M.S. thesis], Materials Science & Engineering Department, Blacksburg, Va, USA, 2002.

H. Xu, H. Yang, and L. Lu, “Effect of erbium oxide on synthesis and magnetic properties of yttrium-iron garnet nanoparticles in organic medium,” Journal of Materials Science: Materials in Electronics, vol. 19, no. 6, pp. 509–513, 2008.

H. G. Beh, R. Irmawati, Y. Noorhana, and K. P. Lim, “Phase evolution and crystallite size of La-substituted YIG at different calcination temperatures,” International Journal of Engineering and Technology, vol. 9, no. 9, pp. 261–265, 2009.

S. Verma, S. D. Pradhan, R. Pasricha, S. R. Sainkar, and P. A. Joy, “A novel low-temperature synthesis of nanosized NiZn ferrite,” Journal of the American Ceramic Society, vol. 88, no. 9, pp. 2597–2599, 2005.