Enhancement in Curie Temperature of Yttrium Iron Garnet by Doping with Neodymium.

The effect of the substitution of Y3+ by Nd3+ on the structural and magnetic properties of neodymium-doped yttrium iron garnet, NdxY3-xFe₅O12 with x in the range of 0⁻2.5, is presented. Oxide powders of Fe₂O₃, Nd₂O₃, and Y₂O₃ were mixed in a stoichiometric ratio and milled for 5 h using high-energy ball milling, before being uniaxially pressed at 900 MPa and annealed at 1373 K for 2 h to obtain NdxY3-xFe₅O12 (0 ≤ x ≤ 2.5). It was found that the mechanical milling of oxides followed by annealing promotes the complete structural formation of the garnet structure. Additionally, the X-ray diffraction patterns confirm the complete introduction of Nd3+ into the garnet structure with a neodymium doping concentration (x) of 0⁻2.0, which causes a consistent increment in the lattice parameters with the Nd3+ content. When x is higher than 2.0, the yttrium orthoferrite is the predominant phase. Besides, the magnetic results reveal an increase in the Curie temperature (583 K) as the amount of Nd3+ increases, while there was enhanced saturation magnetization as well as modified remanence and coercivity with respect to non-doped YIG.

1. Introduction

Yttrium iron garnet, Y3Fe5O12 (YIG) that contain only trivalent ions, has been receiving attention for a long time due to its remarkable properties, such as high electrical resistivity (ρ = 108 Ωm), low dielectric losses (tan δ = 1 × 10−4), high relative permittivity (εr = 20–100), medium saturation magnetization (Ms = 26 emu/g), and low coercivity (Hc = 17 Oe) [1,2,3,4].

The ferrimagnetic garnet, which has secondary symmetry, crystallizes in a cubic structure (space group Ia3d (Oh10) with eight formula units and three sub-lattices. Of these sub-lattices, one is occupied by Y3+ diamagnetic ions (or rare earth ions) in dodecahedral sites {24c} according to the Wyckoff notation. The second is occupied by Fe3+ magnetic ions that distribute in octahedral 16a sites, which are distorted along one of the three fold axes. This trigonal axis coincides with the [111] direction. Finally, the third tetrahedral site also contains Fe3+ ions (24d) [5,6,7,8]. The substitution of Y3+ by magnetic rare earth ions promotes the formation of a new magnetic sub-lattice, which in turn causes the material to have a compensation point below room temperature [9,10]. Furthermore, due to the incorporation of doping cations into the structure of YIG, this causes changes in the magnetic, structural, and magneto-optical properties [11].

In order to understand and adjust almost any intrinsic parameter of a garnet, such as specific magnetization and coercivity, several works have substituted trivalent yttrium cations by different rare earth elements: Ce3+, Dy3+, Gd3+, Sm3+, La3+, including Nd3+ and Pr3+ [12,13,14]. These materials were achieved by using different synthesis methods, such as solid-state reaction, sol–gel, micro emulsion, etc. [15,16]. Among all the methods available for synthesizing YIG, the high-energy ball milling followed by thermal annealing is chosen for its simplicity and versatility [17,18].

Among other trivalent cations, Nd3+ has received special interest due to its magneto-optical properties [10] as it has the same electronic charge than yttrium +3 and thus, it does not promote the electronic hopping caused by the creation of oxygen vacancies, which are undesirable for dielectric materials. Neodymium is a light rare-earth cation, with a magnetic moment of 3.62 µB [14]. Its configuration ([Xe] 4f35d16s2) has a low 5d energy level, which subsequently results in low 4f–5d transition energy. Hence, substituting Nd3+ in yttrium iron garnet (YIG) could improve their magneto-optical properties [10], bandwidth efficiency [19], and dielectric properties due to the increase in spontaneous polarization. Besides, the Nd3+ substitution could modify the values of magnetization due to ferromagnetic coupling with the total magnetic moment of iron. This would increase the Curie temperature (Tc) and hence, ensure less variation of magnetic properties with temperature (at T < Tc), which is usually present when Y3+ is substituted by a trivalent light rare earth cation [20]. In addition, the introduction of Nd3+ could decrease the sintering temperature below 1373 K, extending their applications in low-temperature co-fired ceramics (LTCC) [21].

According to Hernández-Gómez et al. [22], the substitution of Y3+ by Nd3+ alters the magnetic properties of YIG. However, the maximum concentrations of Nd3+ that can be introduced into the YIG structure in order to maintain the garnet structure are x = 2.0 and x = 1.6 for the air and CO2 sintering atmospheres, respectively. Fratello et al. [23] successfully synthesized neodymium iron garnets by liquid phase epitaxy (LPE) at about 1173 K. They obtained films of Nd with the following characteristics YIG with a lattice parameter of 12.596 Å, Curie temperature of 567 K and a saturation magnetization of around 30 emu/g at room temperature. Komori et al. [24] synthesized the single crystals of neodymium iron garnet by low-temperature liquid phase epitaxy on Sm3(ScGa)5O12 and described the crystal structure garnet, in which the Nd3+ substituent cations were coordinated by eight oxygen atoms in distorted dodecahedrons. Arun et al. [25] studied the synthesis of NdY3−Fe5O12 by the sol–gel auto-combustion method. They described the crystallization process (garnet formation) and the Curie temperature of NdY3−Fe5O12 in the range of 527–560 K for Nd3+ doping concentrations of 0–1.5.

Although there are several papers focusing on NdY3−Fe5O12 materials, there is still interest in the study of higher concentrations of Nd3+ cations. In this present work, we studied Nd3+ concentrations of 0–2.5 in the garnet structure and their effect on magnetic properties, such as: specific magnetization, coercivity and Curie temperature. In addition to the above-mentioned studies, no research about high-energy ball milling for the synthesis of this material has been conducted. We estimate that mechano-chemical processing allows us to easily introduce Nd3+ in dodecahedral {24c} sites in the iron garnet structure, enhancing their magnetic properties. Furthermore, we used a short milling time in order to avoid the milling medium contamination and a low annealing temperature, which made the overall process more efficient [17,18,20]. Besides, we expect changes in the Curie temperature, because it depends on the Fe3+(a)-O2--Fe3+(d) super-exchange interaction [15], which can be affected by the mechano-chemical process. As the magnetic moment of Nd3+ cations in the sub lattice {24c} shows ferromagnetic coupling with the total magnetic moment of iron, it could increase the Curie temperature of the NdY3−Fe5O12.

Therefore, in this present study, the powders of NdY3−Fe5O12 with different compositions (with x ≤ 2.5) were produced by high-energy ball milling from oxide powders, which was followed by pressing and annealing. The effect of different concentrations of Nd3+ on the crystal structure, Curie temperature, and magnetic properties were systematically evaluated.

2. Materials and Methods

The powders of NdY3−Fe5O12 (0 ≤ x ≤ 2.5) were obtained from stoichiometric mixtures of Fe2O3 (Sigma Aldrich, St. Louis, MO, USA, 99% purity), Nd2O3 (Sigma Aldrich, St. Louis, MO, USA, 99.8% purity) and Y2O3 (Sigma Aldrich, St. Louis, MO, USA, 99.9% purity), according to the equation:

A total of 5 g of the starting mixture was placed together with steel balls with a diameter of 1.27 cm (ball-to-powder weight ratio of 10:1) in a cylindrical steel vial (50 cm3). Mixtures were milled for 5 h using a shaker mixer mill (SPEX model 8000D, SPEX® SamplePrep, Metuchen, NJ, USA) at room temperature and in air atmosphere.

These experimental conditions were selected according to previously described procedures [17,18]. In order to prevent excessive heating of the vials, the experiments were carried out by alternating 90 min of milling with 30 min of rest. Subsequently, the milled powders with different neodymium doping concentrations (0 ≤ x ≤ 2.5) were uniaxially pressed at 900 MPa and annealed at 1373 K for 2 h in air atmosphere at a heating rate of 10 K/min.

X-ray diffraction technique (XRD) was used to determine the crystal structure and phases present, which was conducted using an diffractometer (Model Equinox 2000, Inel Inc., Stratham, NH, USA) in the 2θ range of 20°–80°. This was equipped with a CoKα1 radiation source with λ = 1.78901 Å and a germanium monochromator at 30 kV and 20 mA. In addition, the crystallographic data were obtained from the inorganic crystal structure database (ICSD). Rietveld refinements were carried out on the X-ray diffraction patterns using the MAUD (Materials Analysis Using Diffraction) software (Version 2.26, Trento, Italy) to obtain the percentages of phases, crystallite sizes and the root mean square microstrain (μs) of the materials synthesized, which is a local deviation of d-spacings from the average value caused by local defects [26]. Morphology and particle size were qualitatively evaluated by means of scanning electron microscopy (Model JSM-6300, JEOL, Tokio, Japan). For the detection of the Nd–O and Fe–O bond vibrations, chemical characterization was performed by the Fourier transform infrared (FT-IR) spectroscopy technique, using a Perkin Elmer, Lowell, MA, USA, Spectrum GX equipment, in the wavenumber range of 400–1000 cm−1. The samples were contained within a KBr matrix. Furthermore, magnetization studies were performed at room temperature, using a vibrating sample magnetometer (Model EV7, MicroSense, Lowell, MA, USA) and applying a maximum field of ±18 kOe. The Curie temperature was determined by means of a temperature scan test under a magnetic field of 5 kOe for all the Nd doping concentrations when the value of the derivative of the magnetization curve is at its minimum with respect to temperature. The Curie temperature was taken as the intersection point with the temperature axis of the tangent to the magnetization curve with the most negative slope.

3. Results and Discussion

In Figure 1 are shown the XRD patterns for the NdY3−Fe5O12 (0 ≤ x ≤ 2.5) samples obtained by milling for 5 h and sintering at 1373 K for 2 h. For x < 2, we confirmed the complete formation of NdY3−Fe5O12 according with the ICSD #1008628 (Ia3d), which did not have peaks corresponding to the precursors (oxides). Therefore, the reaction shown in Equation (1) was completed.

Figure 1

X-ray diffraction patterns and Rietveld refinement of the NdY3−Fe5O12 (0 ≤ x ≤ 2.5) samples mechanically milled for 5 h, pressed at 900 MPa and annealed at 1373 K for 2 h.

In Figure 1, for a higher concentration of Nd3+ (x ≥ 2), we observed the formation of orthoferrite phases, which included: yttrium orthoferrite, YFeO3, ICSD #2101386 (Pnma); neodymium orthoferrite, NdFeO3, ICSD #280090 (Pnma); and hematite, Fe2O3, ICSD #5910082 (R-3cH). The formation of the orthoferrite phases instead of a garnet phase is due to the limit of the solubility of neodymium into the YIG structure. Despite the formation of YFeO3 and Fe2O3 phases, for the Nd concentration x = 2, it is possible to say we extended the solubility limit for neodymium doping by means of assisted mechanical milling compared to the results reported by T. Arun et al. [25] found that the maximum solubility of the Nd3+ in NdY3−Fe5O12 is x = 1.0. This increase in the solubility limit is attributed to the synthesis method, because the milling process produces an increase in the free energy of the system. The energy increase is mainly due to the storage of energy by means of lattice defects introduced by mechanical deformation and interfacial energy. Therefore, the particles become mechanically activated for chemical reactions during the annealing processes. In addition, Figure 1 shows the Rietveld refinement of the NdY3−Fe5O12 (0 ≤ x ≤ 2.5) samples, with the results confirming the successful synthesis of pure garnet phase for x < 2.

Additionally, a distortion of the crystal structure is observed as a broadening of the diffraction peaks. This is due to the strain induced in the lattice by the neodymium substitution at yttrium positions. This causes changes in the lattice parameters due to the differences between the ionic radii of Nd3+ (1.109 Å) and Y3+ (1.019 Å) for the dodecahedral position, which has a coordination number of VIII [27].

In order to quantify the detected phases and the accumulated microstrain (μs) induced by neodymium doping, a Rietveld refinement of the XRD patterns of sintered pellets was performed; the results are presented in Table 1. As expected, whether the microstrain or lattice parameter increases with the level of neodymium due to the effect of distortion on the internal energy of the unit cell.

Table 1

Rietveld refinement parameters for NdxY3−xFe5O12 (0 ≤ x ≤ 2.5) after milling and annealing.

Nd Doped Level, x	Phase	Space Group	Phase wt.%	Dm (Å)	Lattice Parameters (Å)	μs	χ2
0	Y3Fe5O12	Ia3d	100	1900(100)	a = 12.3718(3)	0.001300(5)	1.13
0.1	Nd0.1Y2.9Fe5O12	Ia3d	100	1900(100)	a = 12.3764(9)	0.001200(4)	1.07
0.2	Nd0.2Y2.8Fe5O12	Ia3d	100	1600(90)	a = 12.3966(1)	0.001300(5)	1.11
0.3	Nd0.3Y2.7Fe5O12	Ia3d	100	1700(20)	a = 12.3752(3)	0.001400(4)	1.05
0.4	Nd0.4Y2.6Fe5O12	Ia3d	100	1750(50)	a = 12.3909(3)	0.001300(5)	0.99
0.5	Nd0.5Y2.5Fe5O12	Ia3d	100	1650(90)	a = 12.3944(3)	0.001300(6)	1.00
1.0	Nd1.0Y2.0Fe5O12	Ia3d	100	1570(50)	a = 12.3953(3)	0.001100(8)	0.80
1.5	Nd1.5Y1.5Fe5O12	Ia3d	100	1360(40)	a = 12.4492(3)	0.001200(6)	0.84
2.0	Nd2.0Y3Fe5O12	Ia3d	81.7(8)	730(17)	a = 12.4557(5)	0.001300(7)	0.89
	YFeO3	Pnma	14.0(6)	915(0)	a = 5.588(3) b = 7.595(4) c = 5.274(2)	0.00097(0)
	Fe2O3	Pnma	4(1)	859(0)	a = 5.000(3), c = 13.600(9)	0.00090(0)
2.5	YFeO3	Pnma	89.0(1)	915(26)	a = 5.558(5), b = 7.569(6), c = 5.239(4)	0.00097(0)	0.84
	NdFeO3	Pnma	1.0(5)	1000(0)	a = 5.589(6), b = 7.7619(7), c = 5.4489(6)	0.00060(6)
	Fe2O3	R-3cH	10.0(9)	860(180)	a = 5.017(2), c = 13.673(9)	0.0009(5)

Dm: crystallite size; μs: microstrain.

Table 1 presents the results of Rietveld refinement of the NdY3−Fe5O12 (0 ≤ x ≤ 2.5) samples from the X-ray diffraction patterns, which were discussed previously and shown in Figure 1. As observed in Table 1, the formation of a garnet structure for x ≤ 2 is confirmed. Furthermore, there is a slight variation of the lattice parameter (a), microstrain (μs), and decrease in crystallite size (Dm) after an increase in the doping concentration (x). This can be attributed to the bigger size of the neodymium ion, Nd3+ compared to the yttrium ion, Y3+, which causes enough strain to reduce grain sizes and increases surface energy [23]. According to these results, we expect a simultaneous modification in the values of magnetization through the modification of the interchange interaction between the magnetic ions (iron) in octahedral and tetrahedral sites. In Table 1, χ2 demonstrated a good adjustment of the refinement.

Figure 2 shows the FT-IR transmittance spectra at room temperature in the wavenumber range of 1000–400 cm−1 for the NdY3−Fe5O12 samples (0 ≤ x ≤ 2.5) milled for 5 h and annealed at 1373 K for 2 h. As can be observed, for the non-doped sample (x = 0), the FT-IR spectra shows three intense vibrations corresponding to the tetrahedral sites, Fe–O bond and υ3 (664, 610, and 565 cm−1). Furthermore, a strong band at 400 cm−1 attributed to the isolated octahedral characteristic of the YIG was identified. The results are consistent with the space group Oh10 (Ia3d) of YIG, which exhibits 17 triply degenerate T1u modes that are active in the IR region [4,10]. Besides, there are no significant changes in bands and intensity for the absorption bands for doped samples (0.1 ≤ x ≤ 2.0).

Figure 2

FT-IR spectra of NdY3−Fe5O12 samples recorded at room temperature.

At higher concentrations (x > 2), a shift to the right was observed, while the asymmetric stretching modes of the tetrahedron also increases its intensity for doped samples. These facts are attributed to the distortion of the tetrahedron by the presence of Nd3+ at the dodecahedral site in the garnet structure. It occurs when the lattice size is increased by the introduction of neodymium ion as substitute for yttrium ion [10], and also, it may be caused by the method of preparation, which is namely mechanical activation annealing, as this causes the deformation of the structure.

For x = 2.5, we observed the vibrations of the Nd–O bonds corresponding to NdFeO3 at 553 cm−1 and the band of the Fe2O3 at 443 cm−1. Furthermore, we observed that the vibrations at 470 cm−1 and 418 cm−1 corresponded to YFeO3 of the Fe–O bonds [10]. We confirmed that the garnet structure does not form in doping concentrations higher than x > 2. In addition, there was an asymmetrical stretching vibration of the Fe–O tetrahedral groups at 636, 592, and 550 cm−1, which are due to the introduction of Nd3+ cations into the garnet-type Nd2YFe5O12 [28]. Furthermore, we observed vibrations of the NdY2Fe5O12 sample at 649, 601, and 557 cm−1 for NdY2Fe5O12. These results are in agreement with the X-ray diffraction patterns. The FT-IR spectra from the sample doped with a high content of Nd3+ (x = 2.5) does not show the typical vibration modes of garnet structure at 664, 610, and 565 cm−1 as the crystal structure is orthorhombic for this composition.

In order to describe the magnetic behavior of the synthesized materials, Figure 3 displays a field-dependent magnetization M(H) data measured at room temperature (magnetic hysteresis loops) with x = 0–0.4 in Figure 3a and x = 0.5–2.5 in Figure 3b. Two different behaviors are observed. The first shows a ferrimagnetic order where the specific magnetic saturation (Ms), which is around 26 emu/g, is reached by applying a magnetic field close to 2 kOe for x ≤ 2 (Figure 3a). The second shows a weak ferrimagnetic material for x = 2.5 with a specific magnetization of 1 emu/g (Figure 3b). These behaviors are attributed to the different crystal structures observed in XRD patterns in Figure 1 as there was a garnet structure for x ≤ 2 and orthoferrite structure for x = 2.5. Besides, it can be observed that the value of specific magnetization for x ≤ 2 is high, which was attributed to the interactions of super exchange of the (24d) sites. These sites are not influenced by the Nd3+ and instead depend on the angles between iron ions. However, the reduced magnetizations in 16a sites can be attributed to the lower strength of the Fe–O bond in tetrahedral sites. The substitution of Y3+ by Nd3+ improved the magnetic order of the structure by ferromagnetic coupling with the total magnetic moment of iron. However, when x = 2.5, there is a marked change in behavior.

Figure 3

M-H loops of the NdY3−Fe5O12 for different values of x: (a) 0–0.4 and (b) 0.5–2.5 recorded at room temperature.

In order to analyze the magnetic hysteresis loops shown in Figure 3, the variation of specific saturation magnetization (Ms) and coercivity (Hc) versus neodymium content (x) is presented in Figure 4. As observed, we obtained 17.5 Oe of coercivity for the non-doped sample, which is slightly lower than samples synthesized by other methods [11,12,13,14]. This result can be due to the lower crystallite size achieved by high-energy ball milling and the formation of a complete solid solution of yttrium iron garnet. In addition, we detected a systematic increase in the coercivity with an increase in neodymium concentration. This is attributed mainly to the microstrain in crystal structure of YIG since crystal deformation and grain boundaries are related to the movement of the domain wall. Thus, additional energy is required in the form of a larger applied field to overcome the decrease in the energy of the wall and to release it from grain boundaries. This results in an increase in the values of Hc for the multi-domain structure, where the regions of uniform magnetization are separated by domain walls [3].

Figure 4

(a) Specific magnetization (Ms); and (b) coercivity of the NdY3−Fe5O12 samples (0 ≤ x ≤ 2.5) milled for 5 h and annealed at 1373 K.

The magnetic properties of the garnets depend on several parameters, such as the composition of the material, the particle size, method and temperature of synthesis [8,9,20]. In the studied case, large size particles were obtained (~3 µm) with low coercivity (˂40 Oe). From these measurements, it is possible to establish that the substitution of Y3+ by Nd3+ increased the magnetic anisotropy in the lattice with a positive small contribution of Nd ions to spontaneous magnetization.

For the specific saturation magnetization, the values of Ms are around 26 emu/g when x is 0–0.15 (Figure 4). Meanwhile, for x = 2.0, a slight decrease in the specific magnetization is produced, which reaches 25.4 emu/g due to the formation of YFeO3 and Fe2O3 phases. Finally, for x = 2.5, the specific magnetization falls down to 1 emu/g. This is when we obtained a mixture of yttrium orthoferrite (89 wt.%), neodymium orthoferrite (1 wt.%), and iron (III) oxide (10 wt.%), which showed the magnetic behavior corresponding to the mixture of oxides without formation of a solid solution (0 ≤ x ≤ 2.0) [29,30,31].

The garnet structure has three sub-lattices—namely, octahedral [16a], tetrahedral (24d), and dodecahedral {24c}—that are aligned along the [111] direction. According to the Neél theory, for doped heavy rare earth ions (moment and spin are related by a negative g factor) being added into garnet, the {24c} sub lattice is formed by the Y3+ ions, which are coupled anti-ferromagnetically to the total iron moment [8,15]. The total magnetic moment (MYIG) for the garnet structure of YIG is defined by the equation where M, M, and M are the magnetic moments of cations in tetrahedral (d), octahedral [a], and dodecahedral sites {c}, respectively. According to theoretical results from Wolf, rare earth ions, such as Ce3+, Pr3+, and Nd3+, have positive parallel alignment at the effective moments formed by Fe3+ ions [16]. The Nd3+ is a magnetic ion (3.62 μB) that is a substitute for Y3+, which is a diamagnetic ion (by steric aspects, it cannot substitute Fe3+). Hence, we expect an increase in the saturation magnetization of yttrium–neodymium iron garnet at room temperature by increasing Nd3+ concentration. However, the experimental results shows that the specific magnetization remains nearly constant with a change in the neodymium content. This behavior is attributed to the synthesis method and other factors that promote changes in the magnetic order of the cationic moments due to structural distortions modifying the net magnetic moment.

Figure 5 shows the particle morphologies from the SEM of the powder mixtures milled for 5 h for obtaining NdY3−Fe5O12 (0 ≤ x ≤ 2.0) and annealed at 1373 K for 2 h. In this figure, we observed particles of approximately 3 µm in diameter with a nearly uniform size distribution. Additionally, we saw the formation of agglomerates covered by smaller particles with a smooth surface, which had an irregular and rounded morphology (almost identical for all samples). This indicates that the concentration of Nd3+ into the YIG does not modify the morphology of the particles, although changes could occur in crystallite sizes.

Figure 5

SEM micrographs of milled powder annealed at 1373 K for 2 h for obtaining NdY3−Fe5O12 with different values of x: (a) x = 0, (b) x = 0.5, (c) x = 1.0, and (d) x = 2.0.

Finally, we evaluated the effect of adding Nd3+ ion to the YIG crystal structure and its relationship with the Curie temperature, with the results shown in Figure 6. For temperatures higher than Tc, a complete random orientation of the magnetic moments takes place (paramagnetic state), which results in zero magnetization. For this reason, the increase in Tc can be explained by the increasing concentration of Nd3+ ions due to the positive contribution of Nd ions that increased the magnetic moment of samples.

Figure 6

Temperature dependence of magnetization of the NdY3−Fe5O12 (0 ≤ x ≤ 2.0) at 5 kOe of applied field.

The Tc of the un-doped sample obtained was 549 K, which is consistent with other authors [4,15]. By increasing the Nd3+ content, an increase in Tc was found as Tc increased from 549 K for the non-doped YIG to 583 K for doped sample with x = 2.0. Hence, this can be explained by the major contribution of the 5d orbitals of Nd3+, which is larger than the 6s. As previously mentioned, Nd3+ increased the magnetic moment and enhanced the Tc (up to 583 K) for high contents of neodymium (x = 2).

Therefore, the values of Tc in the samples are attributed to the interactions between magnetic moments, which also are related to the lattice parameter and grain size of the samples. Thus, the values of magnetization decrease when the temperature increases because the order of magnetic moments of atoms is randomized. In fact, the importance of the substitution is to modulate the magnetic and magneto-optic properties of YIG. In the studied material, the Tc decreased from 547 to 543 K for x = 0.1 and 0.2, respectively, which is shown in Figure 7. This is due to changes in the length and angle of Fe3+(a)-O2--Fe3+(d) so the interaction and effective magnetic moments formed by Fe3+ decrease. This also changes the entropy of the material with a low Nd3+ content. After this point, there is a consistent increase in Tc as the doping level increases, which reaches a maximum of 583 K at x = 2.0 where the formation of orthoferrite and hematite phases is observed.

Figure 7

Curie temperature (Tc) of the NdY3−Fe5O12 (0 ≤ x < 2.5).

The results reveal that NdY3−Fe5O12 (0 ≤ x ≤ 2.0) shows simultaneously high values of magnetization and high Curie temperature. Finally, for x = 2.5, where mainly the orthoferrite structure is detected by XRD, the Curie temperature falls down to 562 K. This result is not presented in Figure 6 since the specific magnetization at 5 kOe is 1 emu/g and would be observed as a horizontal line on the same axis scale.

Another factor explaining the behavior of the Curie temperature is the contribution of the 5d orbitals of Nd3+. As Y3+ is a diamagnetic ion, the exchange interaction is zero, meaning that the joined structure causes distortion of the crystal lattice. Taking into account all the above-mentioned points, it is possible to modulate some properties—such as Ms, Hc, and Tc—for applications that demand specific values for these parameters.

4. Conclusions

Neodymium-doped yttrium iron garnet, NdY3−Fe5O12 (0 ≤ x ≤ 2), has been successfully prepared by high energy ball milling for 5 h, followed by annealing at 1373 K for 2 h. This temperature is around 200 K lower than the temperature required to obtain a garnet structure by means of solid state reaction. X-ray diffraction and Rietveld refinement confirmed that a high neodymium-doped garnet material is synthesized, while the garnet structure is retained for almost all the doping levels (x ≤ 2) of the prepared powders. We observed the formation of orthoferrite phases of Nd and Y with Nd3+ contents of x > 2 and small amounts of hematite. FT-IR analysis confirms the structural changes detected with an increase in Nd3+, which is used as a substituent cation. All the studied samples show ferrimagnetic behavior attributed to the intrinsic structure, garnet or orthorhombic phases. The saturation magnetization obtained for the doped samples is in the range of 25.4–27.9 emu/g, while the coercivity was between 17 and 33 Oe. Both values are in good agreement with the magnetic parameters obtained by similar methods for pure yttrium iron garnet and represent important magnetic contributions.

Moreover, integrating the neodymium ions into the structure of YIG increases the Curie temperature up to 583 K for x = 2, with high magnetic parameters, such as specific magnetization and coercivity. The presence of Nd3+ as the doping cation primarily affects the Curie temperature of the neodymium-doped yttrium iron garnet, while the specific magnetization remains constant. This extends the range of potential applications of these ferrites due to their tunable magnetic properties.