The Structural and the Magnetic Properties of Aluminum Substituted Yttrium Iron Garnet

Abstract

In this paper, Y₃Al_xFe_5-xO₁₂ powders with x = 0.0, 0.2, 0.4, 0.6, 0.8, and 1.0 were prepared via solid state reaction method. X-ray diffraction, Vibrating Sample Magnetometry, and Mössbauer Spectroscopy were used to study their structural and magnetic properties. The XRD patterns of the samples show single phase structure with decreasing lattice constant when increasing Al concentration. The saturation magnetization decreases from 28.0 to 10.1 emu/g with increasing Al³⁺ from 0.0 to 1.0 due to the reduction of the superexchange interactions between iron ions in the a and d sublattices. Room temperature Mössbauer spectra for the samples were collected and analyzed. The hyperfine field values for octahedral and tetrahedral sites of the samples decreased with increasing Al concentration. Moreover, Mössbauer results have shown that Al³⁺ ions prefer to replace Fe⁺³ at the octahedral sites.

Keywords:
Mössbauer Spectroscopy; Hyperfine Interactions; Magnetic Properties; X-ray Diffraction

1. Introduction

Yttrium iron garnet (YIG) has received intensive studies since its discovery in 1956¹. YIG and substituted YIG provide remarkable performance in microwave devices due to their tunable magnetization and low dielectric losses^2,3. The magnetic properties of YIG with chemical composition {Y₃³⁺}_c[Fe₂³⁺]_a(Fe₃³⁺)_dO₁₂^2-, where Y³⁺ ions occupy dodecahedral sites and magnetic Fe³⁺ ions occupy octahedral [a-sublattice] and tetrahedral (d-sublattice) sites, are determined by the strength of the superexchange interactions between magnetic ions in the various sublattices^4-7. Accordingly, the substitution of Y³⁺ ions by other rare earth ions, and/or Fe³⁺ ions by nonmagnetic ions were adopted for successful modification of the magnetic properties of YIG for potential technological applications³.

Garnets were functionalized in either the form of bulk materials for microwave passive devices, or in the form of thin films for magnetic-bubble-type digital memories. Although the magnetization of the garnet films for bubbles is essentially the same as in the bulk state, the magnetic anisotropy of the films is quite different, depending on the characteristics of the films, and their synthesis routes. For details on the parameters of bubbles which play an important role in solid state device applications, and the relation of these parameters to the magnetic and physical characteristics of the films, the reader is referred to the review article by Eschenfelder⁸.

The replacement of Fe³⁺ magnetic ions with non-magnetic ions such as Al³⁺ has caught the attention of many researchers. The site selectivity of Al³⁺ ions in Al-substituted YIG was first reported by Gilleo and Geller in 1958^9,10, where it was found that Al³⁺ ions substitute Fe³⁺ ions preferentially at the tetrahedral (d) sites. In later detailed studies of the crystal chemistry of garnets, it was reported that the fraction of Al³⁺ ions at the tetrahedral sites decreased smoothly with the increase of Al concentration from 1.0 at x = 0 to 0.6 at x = 5^11,12. In addition, Cohen and Chegwidden (1966) concluded from their magnetization data that the Al³⁺ ions redistributed themselves among tetrahedral and octahedral sites with the increase of the temperature at which the garnet was heat treated¹³. In a more recent study, Kim et al. have investigated the magnetic and structural properties of the substituted Y₃Fe_5-xAl_xO₁₂ (x = 0.0, 0.25, 0.50, 0.75, and 1.0) garnets prepared by sol-gel method. In their study, both the lattice constant a and the saturation magnetization M_s decreased with increasing Al concentration. Moreover, room temperature (RT) Mössbauer spectra reflect cation distribution of Fe³⁺ and Al³⁺ at tetrahedral sites where six components were used to fit the sample with x = 1¹⁴.

Thongmee et al. have reported the hyperfine parameters and the saturation magnetization of the system Y₃Fe_5-xAl_xO₁₂ (0 < x < 1 and x = 1.5, 2.0, and 2.5). It was shown that the saturation magnetization decreased with Al³⁺ substitution for Fe³⁺. In addition, RT Mössbauer spectra for the samples with 0 ≤ x ≤ 0.8 were fitted with three magnetic components, two corresponding to octahedral sites and one to tetrahedral sites¹⁵. On the other hand, Motlagh et al. have shown that a systematic line broadening was observed in the Mössbauer spectra with the increase of Al³⁺ concentration, which can be attributed to the presence of hyperfine field distribution because of the random distribution of Al³⁺ in the octahedral and tetrahedral sites¹⁶.

Based on the previous studies, aluminum-substituted iron in YIG were synthesized by different methods such as sol-gel method^14,17,18, co-precipitation method¹⁹, and ball milling¹⁶. Mössbauer spectra for synthesized garnets were fitted with different numbers of components corresponding to Fe³⁺ in octahedral and tetrahedral sites. The results of the previous studies indicated that the site selectivity of Al³⁺ ions may be sensitive to the preparation method, heat treatment, and the level of Al substitution. In the present study, investigation of the structural, magnetic, and hyperfine interactions of Y₃Fe_5-xAl_xO₁₂ (0.0 ≤ x ≤ 1.0) synthesized by solid state reaction was carried out. Mössbauer spectroscopy was used to investigate the effect of Al substitution on the hyperfine magnetic fields and on the site preferred by the Al³⁺ ions. In addition, X-ray diffraction (XRD), scanning electron microscope (SEM), and Vibrating Sample Magnetometer (VSM) were used to characterize all the samples to examine their structural and magnetic properties.

2. Experimental Procedures

Y₃Al_xFe_5-xO₁₂ powders with x = 0.0, 0.2, 0.4, 0.6, 0.8, and 1.0 were synthesized by solid state reaction method. Metallic oxides Y₂O₃, Fe₂O₃ and Al₂O₃ were used to prepare Y₃Al_xFe_5-xO₁₂ powder samples. Appropriate weighted amounts of the metallic oxides were loaded into a hardened stainless-steel cup with ball to powder ratio of 10:1. The milling process was carried out at 250 rpm for 16 h. The resulting precursor was annealed at 1300°C for 2 h. X-ray diffraction (XRD) patterns were collected using Philips PW 1720 X-ray diffractometer operating at (40 kV, 40 mA), with Cu-Kα radiation (λ = 1.5405 Å). The samples were scanned over the angular range 15° < 2θ < 75° with 0.02° scanning step and speed of 1 deg/min. The XRD patterns were carried out using X’pert HighScore 2.0.1 software for phase identification, and Rietveld refinement of the crystal structure was performed using FullProf suite 2000 software.

The magnetic measurements at room temperature were performed using Vibrating Sample Magnetometer (VSM MicroMag 3900, Princeton Measurements Cooperation), providing a maximum applied magnetic field of 10 kOe. Room temperature (RT) Mössbauer spectra were collected over 1024 channels using a standard constant acceleration Mössbauer spectrometer, with a 50 mCi ⁵⁷Co in a Rhodium matrix γ-ray source. The spectra were calibrated using room temperature Mössbauer spectrum of α-Fe foil, and then analyzed using fitting routines based on least-squares analysis.

3. Results and Discussion

3.1 XRD Analysis

Figure 1 shows the powder XRD patterns of pure and Al substituted YIG with different Al concentrations (x = 0.0, 0.2, 0.4, 0.6, 0.8, and 1.0). Rietveld analysis of all patterns was used to determine the refined crystal parameters of all pure and the Al substituted YIG samples. The analysis revealed the presence of a single garnet phase (space group cubic symmetry Ia-3d) without any impurity phase.

Figure 1
Powder X-ray diffraction patterns of Y₃Al_xFe_(5-x)O₁₂ garnet samples.

Figure 2 shows representative Rietveld refined patterns for the samples with x = 0 and 1. The theoretical pattern (black continuous line) is in good agreement with the experimental data (red dots), where the residual difference curve (in blue) is a straight horizontal line with small ripples only around the main structural peak positions. The goodness- of-fit quality determined by the value of χ², Bragg factor (R_B), as well as the refined lattice parameter a and unit cell volume V, and the x-ray density for all samples are listed in Table 1. The lattice constant and the cell volume decreased monotonically with increasing the concentration x of the doped Al³⁺ ion. Such decrease can be attributed to the smaller ionic radius of Al³⁺ relative to that of Fe³⁺ in both the octahedral (a) and tetrahedral (d) sites, where the bond length Al³⁺(a) - O^2- = 1.94 Å, whereas Fe³⁺(a) - O^2- = 2.02 Å, and Al³⁺(d) - O^2- = 1.76 Å, whereas Fe³⁺(d) - O^2- = 1.87 Ź². Also, the x-ray density obtained from the refinement analysis exhibited a similar monotonic decrease with increasing x, contrary to what is expected as a result of the decrease of the cell volume. This is due to the fact that the rate of decrease of the molecular weight with Al-substitution is higher than the rate of decrease of the cell volume as x increases. In addition, the observed broadening of the diffraction peaks for the Al-substituted YIG samples indicates that the substitution results in a poorer crystallinity of the YIG phase.

Figure 2
Refined XRD patterns for Y₃Al_xFe_(5-x)O₁₂ garnet samples with x = 0 and x = 1. The residual difference (Y_obs - Y_calc) between the experimental (Y_obs) and calculated data (Y_calc) is given in the lower part of the plots (blue line).

Table 1
Bragg factor R_B, χ², lattice constant a, unit cell volume, and density ρ for all garnet samples.

Composition (x)	χ2	RB	a (Å)	V (Å)3	ρ (g/cm3)
Y3Fe5O12	1.81	2.00	12.373(4)	1894.4	5.175
Y3Fe4.8Al0.2O12	1.44	2.40	12.336(8)	1877.6	5.164
Y3Fe4.6Al0.4O12	1.40	2.44	12.320(6)	1870.2	5.144
Y3Fe4.4Al0.6O12	1.49	2.23	12.308(1)	1864.5	5.118
Y3Fe4.2Al0.8O12	1.50	2.28	12.300(7)	1861.2	5.086
Y3Fe4Al1O12	1.32	2.89	12.287(9)	1855.4	5.045

3.2 SEM Analysis

SEM images of pure YIG and Al doped YIG samples for different concentrations are shown in Figure 3. The figure indicates that all samples are composed of particles with irregular shapes and relatively narrow particle size distribution. As x increased, however, the particle size became more uniform and exhibited a small reduction. Specifically, the sample with x = 0 consisted of particles with size in the range from ~ 0.8 µm to ~ 4 µm. The images of the samples with x = 0.2, 0.4, and 0.6 are generally similar to the image of the sample with x = 0, but they revealed the presence of a larger fraction of smaller particles with size ~ 1 µm, and an upper limit of particle size of nearly 3 µm. The SEM images of the samples with x = 0.8, and 1.0 showed further reduction of particle size, and the particles became almost spherical in shape. The particle size distribution in these samples is narrower and more uniform, and the majority of particles are characterized by particle size ≤ 1 µm in diameter. These results indicated that the Al substitution in YIG resulted in a small reduction of the particle size, uniform particle shape, and narrow particle size distribution.

Figure 3
SEM images for all synthesized garnet samples.

3.3 Magnetic Measurements

The magnetic hysteresis loops at RT of Y₃Al_xFe_5-xO₁₂ samples are shown in Figure 4. From the hysteresis loops, it can be noticed that all samples have negligible coercivity regardless of Al concentration x²⁰. This is indicative of the low RT crystal anisotropy of YIG²¹ , and demonstrates that Al substitution has negligible effect on the crystal anisotropy.

Figure 4
Magnetic hysteresis loops for Y₃Al_xFe_(5-x)O₁₂ garnet samples.

That magnetization of all samples is almost saturated at an applied field of 10 kOe, and the saturation magnetization (M_s) was determined directly from the hysteresis loops and listed in Table 2. The saturation magnetization for the pure YIG sample is consistent with previously reported results^3,21, and the saturation magnetization of the substituted samples decreased with the increase of Al³⁺ ions substituting Fe³⁺ ions at (d) and (a) sublattices. The monotonic decrease of M_s with increasing x (Figure 5) can be attributed to the progressive reduction of the superexchange interactions between iron ions at a and d sites, and the reduction of the magnetic dipole-dipole interaction^14,15. In an earlier investigation of the magnetic behavior of substituted garnets, it was proposed that the substitution of diamagnetic ions for Fe³⁺ ions at a given sublattice leaves the moments of the Fe³⁺ ions in that sublattice in parallel alignment, while the consequent weakening of the a-d interactions leads to a more important role played by intra-sublattice interactions and randomization of the canting of the Fe³⁺ moments of the other sublattice²². This tendency occurs at low substitution levels, and as x increases, the continued depletion of the iron sublattice by nonmagnetic ions reaches a point beyond which the intra-sublattice interactions become dominant over the a-d interactions^3,22. These effects may explain the deterioration of the saturation magnetization of YIG with increasing the level of Al substitution for Fe, where the magnetization behavior is dictated by the progressively increased importance of intra-sublattice interactions with increasing x.

Table 2
The saturation magnetization (M_s in emu/g) for Y₃Al_xFe_5-xO₁₂garnet samples.

x	0.0	0.2	0.4	0.6	0.8	1.0
Ms (emu/g)	28.0	22.3	19.0	15.5	12.1	10.1

Figure 5
The saturation magnetization as a function of concentration for Y₃Al_xFe_(5-x)O₁₂ garnet samples.

3.4 Mössbauer spectroscopy

Mössbauer spectroscopy was used to investigate the preferential site occupation of Al³⁺ ions in the garnet lattices. Accordingly, Mössbauer spectra (MS) of the system Y₃Al_xFe_5-xO₁₂ with x = 0.0, 0.2, 0.4, 0.6, 0.8, and 1.0 were recorded at room temperature (RT). Figure 6 shows the fitted Mössbauer spectra and the corresponding fitting parameters are listed in Table 3.

Figure 6
Mössbauer spectra for the Y₃Al_xFe_5-xO₁₂ samples (filled circles) together with the theoretical spectrum obtained from the fitting software (continuous red line). The component corresponding to octahedral sites is represented by the blue sextet, while that corresponding to tetrahedral sites is represented by the green sextet

Table 3
The hyperfine parameters and the percentage relative intensities (I) obtained at room temperature for Y₃Al_xFe_5-xO₁₂ garnet samples.

Site	Bhf (kOe) ± 5	CS (mm/sec) ± 0.01	Width (mm/sec) ± 0.02	I (%) ± 1%
x = 0.0
Octahedral(s)	497	0.38	0.34	27
	487	0.38	0.36	10
Tetrahedral	401	0.15	0.50	63
x = 0.2
Octahedral(s)	490	0.36	0.39	23
	474	0.39	0.39	13
Tetrahedral	395	0.15	0.58	64
x = 0.4
Octahedral(s)	480	0.36	0.43	22
	461	0.38	0.41	13
Tetrahedral	389	0.15	0.63	65
x = 0.6
Octahedral(s)	472	0.35	0.52	22
	448	0.39	0.55	13
Tetrahedral	382	0.16	0.79	65
x = 0.8
Octahedral(s)	468	0.35	0.40	5
	450	0.37	0.55	18
	422	0.44	0.59	11
Tetrahedral(s)	376	0.16	0.76	53
	341	0.14	0.71	13
x = 1.0
Octahedral(s)	462	0.30	0.41	4
	441	0.34	0.52	12
	411	0.38	0.61	13
Tetrahedral(s)	366	0.13	0.84	47
	327	0.11	0.90	24

The spectrum of pure YIG (x = 0) was fitted with three magnetic sextets corresponding to iron ions (Fe³⁺) in three different environments, two octahedral sites with B_hf = 497 kOe and 487 kOe and one tetrahedral site with B_hf = 401 kOe²³. The intensity ratio of %37: % 63 for the two sublattices is close to 2:3, which is consistent with previously reported results^23-26.

The spectrum for the sample with x = 0.2 was fitted also with three magnetic sextets as mentioned above. A reduction was observed in the values of the hyperfine magnetic field at the iron nucleus in both sublattices due to the substitution of Al^3+20,27,28. Specifically, the hyperfine fields associated with Fe³⁺ ions at octahedral sites reduced to 490 kOe and 474 kOe, and that associated with Fe³⁺ ions at tetrahedral sites reduced to 395 kOe. Moreover, a little broadening in the line widths was observed for all components, resulting from the statistical distribution of nonmagnetic ions around the Fe³⁺ occupied sites.

Three magnetic components were also used to fit the Mössbauer spectra for the samples with x = 0.4 and x = 0.6. The hyperfine field values for all sites continue to decrease with increasing the concentration of Al³⁺ ions. This result is consistent with the drop in the saturation magnetization values compared to that of the pure YIG sample. The relative intensities of the octahedral and tetrahedral components suggest that Al³⁺ ions may replace the Fe³⁺ ions at the octahedral sites. This result can be also confirmed by the large broadening in the sextet of the tetrahedral site, which could be due to the local fluctuation of the chemical environment of this site arising from the substitution of Al³⁺ at the octahedral sites²⁸.

The spectrum for the sample with x = 0.8 was fitted with five magnetic components, three octahedral components with B_hf = 468 kOe, 450 kOe, and 422 kOe and two tetrahedral components with B_hf = 376 kOe and 341 kOe with intensity ratio of %32: % 68. The evolution of the new component with B_hf = 422 kOe could be attributed to Fe in the octahedral sites with Al in its environment which causes a reduction in B_hf from about 500 kOe down to this value. This also can be proven by observing the significant drop in the intensity that is associated with B_hf = 468 kOe. Moreover, a new component, with B_hf = 341 kOe, was observed, and could be associated with Fe³⁺ ions in tetrahedral sites surrounded with a chemical environment involving Al³⁺ ionic substitution for Fe³⁺ ions.

The spectrum for the sample with x = 1.0 can be fitted as a superposition of five magnetic components as in the case for x = 0.80, in addition to a weak magnetic component, with intensity less than 1%, attributed to an α-Fe₂O₃ phase. The fact that this phase was not detected by XRD is an indication that its fraction in the sample was below the delectability limit of the diffraction technique, and that Mössbauer spectroscopy is more sensitive to detecting traces of Fe-containing phases. The increase in the intensity, 71%, and the line broadening of the tetrahedral components supports also the fact that Al³⁺ ions replaced Fe³⁺ ions in the octahedral sites. Moreover, the center shifts of the octahedral and tetrahedral sites show some decrease. This can be attributed also to the local fluctuation of the chemical environment induced by the statistical distribution of Al³⁺ ions in the garnet lattice.

4. Conclusions

The Y₃Al_xFe_5-xO₁₂ garnets with Ia3d space group were been prepared by solid state reaction and. The lattice constant was found to decrease with increasing Al³⁺ concentration. The substitution of Fe³⁺ by Al³⁺ at octahedral sites was confirmed by Mössbauer spectroscopy. The distribution of Al³⁺ ions among octahedral and tetrahedral sites, contrary to the reported preference for tetrahedral sites, may indicate the sensitivity of the ionic distribution to the preparation procedure and heat treatment, in agreement with the results of Cohen and Chegwidden (1966). Moreover, the saturation magnetization M_s decreased with the increase of the concentration of Al³⁺ ions due to the weakening of the superexchange interactions between the Fe³⁺ ions induced by the depletion of the Fe sublattices by nonmagnetic Al³⁺ substitution.

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Publication Dates

• Publication in this collection
  15 Mar 2018
• Date of issue
  May-Jun 2018

History

• Received
  06 Sept 2017
• Reviewed
  30 Dec 2017
• Accepted
  17 Feb 2018