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J. Korean Ceram. Soc. > Volume 55(3); 2018 > Article
Sivakumar, Naidu, Nazeer, Rafi, kumar, Sathyaseelan, Killivalavan, and Begam: Structural Characterization and Dielectric Studies of Superparamagnetic Iron Oxide Nanoparticles


Superparamagnetic iron oxide nanoparticles (SPIONs) have been prepared without using surfactants to assess their stability at different time intervals. The synthesized particles were characterized by X-ray diffraction, Fourier-transform infrared spectroscopy, ultraviolet-visible-near infrared spectroscopy, and energy dispersive spectroscopy. Field emission scanning electron microscopy and high-resolution transmission electron microscopy images of the samples were also investigated. The average particle size was measured to be 12.7 nm even in the polydispersed form. The magnetic and dielectric characteristics of the Fe3O4 nanoparticles have also been studied and discussed in detail.

1. Introduction

In the past decades, attention has been increasingly paid to the design and assembly of magnetic nanomaterials with controlled shapes and morphologies. Magnetic nanoparticles present opportunities in technological applications such as protein and enzyme immobilization, bio-separation, immunoassays, hyperthermia, drug delivery, and magnetic resonance imaging (MRI). They exhibit interesting properties owing to the presence of iron cations in two valence states, namely Fe2+ and Fe3+, in the inverse spinel cubic structure.1,2)
Magnetite (Fe3O4) nanoparticles can be synthesized by several routes, including co-precipitation, sol-gel method, colloidal route, solvothermal synthesis, hydrothermal method, micro-emulsion method, and thermal decomposition.3) J.B. Mamani et al.4) prepared magnetic fluids of Fe3O4 using chemical synthesis and revealed that both in vitro and in vivo studies have yielded homogeneous magnetic nanoparticles with an average diameter of 12.6 nm. Furthermore, their magnetization measurements confirmed the existence of the superparamagnetic behavior of Fe3O4 nanoparticles above the blocking temperature (TB = 80 K), where there is no coercivity. This property could be effectively exploited for the monitoring and tracking of magnetic nanoparticles in MRI and for magnetohyperthermia techniques.
Iron oxide nanoparticles synthesized by the mechanical ultrasonication method exhibited particle sizes of 6 nm with spherical morphology.5) Their magnetic saturation and coercivity at room temperature (RT) were found to be 3.7 emu/g and 114 Oe, respectively. In addition, there are a variety of reports on the synthesis of Fe3O4 nanoparticles.6-23)
Sara Gil et al.24) demonstrated that Fe3O4 nanoparticles could be coated with di-carboxylic terminated polyethylene glycol to construct MRI dual modality molecular probes for vivo colorectal and gastric carcinoma detections. M. Morel et al.25) showed that oleic acid-coated magnetite nanoparticles generally agglomerate. Furthermore, the agglomeration observed in the HRTEM images was attributed to the Van der Waals force between the particles.
The main objective of the present work is to synthesize superparamagnetic iron oxide nanoparticles without using surfactants. Most of the reports emphasize the use of capping agents during synthesis to improve stability. To the best of our knowledge, only few reports on SPIONs synthesis using the co-precipitation technique without any encapsulating agent exist. Although the properties of iron oxide nanoparticles have been studied well, the stability of their magnetic and dielectric properties have not been investigated.

2. Experimental Procedure

2.1. Materials used

The starting materials ferric chloride hexahydrate (FeCl3·6H2O), ferrous sulfate heptahydrate (FeSO4·7H2O), ammonia (NH3), and ethanol (C2H6O) were obtained from Fisher scientific, India. The purity of the reactant chemicals was ≥ 99.9%.

2.2. Synthesis of SPIONs

To synthesize SPIONs, 1.49 g of FeCl3·6H2O and 0.765 g of FeSO4·7H2O were mixed and heated at 60°C under a nitrogen atmosphere. An 8 M ammonia solution was then added drop wise to the parent solution until the pH became 10. The resultant solution was maintained at 60°C for 2 h, and centrifuged at 10,000 rpm for 10 min. The sediment particles were thoroughly washed with distilled water three times to remove the byproducts. Thereafter, the particles were washed several times with ethanol. The product was finally dried in an oven at 100°C for 3 h.

2.3. Characterization of SPIONs

The crystal structure of the SPIONs was ascertained by x-ray powder diffraction (XRD) using a Bruker D8 advance diffractometer with Cu-Kα radiation (1.5406 Å) operating at 40 kV and 30 mA. The FTIR spectrum of the SPION particles was recorded using a BRUKER 10049391IR spectrometer at RT in the frequency range 500 - 4000 cm−1. The UV-Vis-NIR absorption spectrum was measured between 200 and 2500 nm using a Varian Cary 5000 spectrophotometer. The morphology of the SPIONs was analyzed by FE-SEM using a JEOL-JSM-6390 LV, while its particle size was determined by HRTEM using a JEOL JEM 2100. Moreover, the magnetic properties of the SPIONs were studied by vibrating sample magnetometry (VSM) using a Lakeshore 7410 at RT. The dielectric parameters of the sample, such as dielectric constant (ɛr), dielectric loss (tan δ), and AC conductivity, were studied using HIOKI 3532-50 LCR HiTESTER at various temperatures (350 K-400 K) in the frequency range 100 Hz - 5 MHz.

3. Results and Discussion

3.1. X-ray diffraction (XRD)

The XRD pattern of the as-synthesized SPIONs is shown in Fig. 1. All the diffraction peaks were indexed to the cubic inverse spinel structure of Fe3O4, similar to that of the bulk Fe3O426) with a lattice constant a = b = c = 8.381 Å and space group Fd3m. The observed peaks could be assigned to the (hkl) reflections from the (220), (311), (400), (422), (511), (440), (620), and (622) planes in the order of ascending 2θ values. No impurities were observed across the entire range of the profile. The interplanar distance (d-spacing) of the cubic lattice was estimated by Bragg’s diffraction equation: 2d sinθ = nλ for n = 1. The lattice parameter of the cubic unit cell (a) was estimated by the equation (1):
where d is the d-spacing and h, k, and l are the Miller indices (h k l). The calculated d-spacing and lattice parameters match the standard data reported for magnetite (JCPDS 85-1436). The average crystallite size was calculated from the major diffraction peak of (311) using the Debye-Scherrer formula and was found to be 7 nm. The reduction in the particle size of the sample could be collectively attributed to the purity of the starting compounds, proper control of pH, and the optimum temperature. Furthermore, the size reduction of Fe3O4 nanoparticles would greatly influence their superparamagnetic behavior and blocking temperature. The variation in particle size would also affect the monitoring and tracing of magnetic nanoparticles by MRI and magnetothermal techniques,27) as the molecular probes sensitivity strongly depends on the surface-to-volume ratio of the nanoparticles.

3.2. Fourier transform infrared (FT-IR) analysis

The FTIR transmission spectrum of the SPIONs is shown in Fig. 2. The two main absorption bands at 442 and 538 cm−1 correspond to the Fe-O bonds in the tetrahedral and octahedral sites, respectively, confirming the spinel structure of pure Fe3O4 nanoparticles.28-30) This is also reflected in the planes observed in XRD, thus confirming the spinel cubic nature of the synthesized sample. The broad peaks that appear from 3500 to 3000 cm−1 and the IR absorption peaks between 1800 and 1073 cm−1 are due to the fundamental and overtonic O-H stretching vibrations of the hydroxyl groups of water on the nanoparticles, respectively.31) These results are consistent with the previous reports.32-34) Despite absorbing water on their surface during synthesis, the nanoparticles exhibited sizes significantly less than those of the particles30) obtained using microwave radiation. The particle sizes of the non-hydrated samples of Fe3O4 subjected to microwave irradiation ranged from 17 to 25 nm. Here, the co-precipitation method yielded particles 7 nm in size even with water of crystallization.

3.3. Optical properties of SPIONs

The optical absorption properties of the synthesized SPIONs were measured in the wavelength region 200 - 1400 nm, and are illustrated in Fig. 3. The bandgap of the nanoparticles has been calculated using the Tauc equation. (2):
αhν=A (hν-Eg)n,
where α is the absorption coefficient, A is a constant, h is Planck’s constant, ν is the photon frequency, Eg is the bandgap energy, and the exponent n = 1/2 for an allowed direct transition and 2 for an allowed indirect transition. The optical band gap of the SPIONs can be extracted from the intercept of the extrapolated linear fit of the plot of (αhν)2 versus incident photon energy (hν) near the absorption edge, as shown in Fig. 3. The bandgap energy (Eg) of the SPIONs was found to be 2 eV for indirect transition, higher than the bulk Eg of magnetite. Manohar et al.34) reported that the Eg of Fe3O4 is 0.12 eV. The deviation in refractive index was attributed to the influence of quantum confinement on the band gap of iron oxide nanoparticles.35) Sahana et al.36) also demonstrated the correlation between bandgap energy and nanocrystallite size and discussed it in terms of the confinement effect. Therefore, the bandgaps of SPIONs are tunable with the proper control of particle size and morphology, which could be utilized in microwave-based device applications. Accordingly, the Eg of the synthesized Fe3O4 particles has been found to be 2 eV for the particles 12.7 nm in size. This considerable increase in Eg for the same particle size compared with that reported by Manohar et al.34) is quite favorable for a higher absorbance of UV radiation. Consequently, the blocking capacity of the powder in the UV regime is greater. This property will be useful for the application of the synthesized samples as sunscreen agents. Gold coating on Fe3O4 (Au (shell)/Fe3O4 (core)) 10 nm in size has 50% UV blocking effects,23) whereas the present study involving particles of size 8 nm revealed 65% UV absorption. Table 1 presents the shift in λmax and Eg due to the size effect.

3.4. Field emission scanning electron microscopy (FE-SEM) and energy dispersive x-ray (EDX) analysis

The FE-SEM image of the SPIONs is shown in Fig. 4(a). It was found that the nanoparticles had an almost spherical morphology with a narrow particle size distribution. The EDX spectrum, presented in Fig. 4(b), reveals the presence of stoichiometric proportions of elemental Fe and O, confirming the formation of Fe3O4. Furthermore, the observed Cl and S peaks were attributed to the impurities from the starting compounds. These impurities could be removed after repeated washing with water and alcohol. Powders with trace amounts of Cl and S have no impact on the size of the SPIONs and their morphological properties. This has been confirmed from the XRD pattern and FE-SEM images (not shown here) of the Fe3O4 powders obtained after leaching the samples with water and subsequently alcohol.

3.5. High Resolution Transmission electron microscope (HRTEM) studies

The HRTEM images of the obtained SPIONs are shown in Figs. 5(a-b). The analysis revealed that the sample consists of uniform spherical particles with an average size of 12.7 nm and lattice fringes. Only few particles agglomerated, because of the existence of Vander Waals interactions among them.37) Fig. 5(c) indicates a very narrow particle size distribution of the SPIONs at 12.7 nm. The selected area electron diffraction (SAED) pattern is shown in Fig. 5(d), as predicted by XRD. Deepak et al.38) produced SPIONs with a size of around 7 nm and spherical morphology by the thermal decomposition process using iron (III) acetylacetonate. Compeán-Jasso et al.39) prepared superparamagnetic magnetite nanoparticles with diameters of approximately 15 nm by a forced hydrolysis method. Maleki et al.40) synthesized SPIONs that are surface-coated with gold and achieved a size of 8 - 13 nm with a narrow size distribution. The particle sizes of the SPIONs obtained from other methods have also been compared with our work, as shown in Table 1.41-45)

3.6. Magnetic properties of SPIONs

Magnetization measurements were conducted at RT to obtain parameters such as saturation magnetization (Ms), remanence (Mr), and coercivity (Hc) from the analysis of the M-H magnetization curves. The VSM results of the SPIONs are presented in Fig. 6 and Table 2. It shows that the samples possess superparamagnetic properties at RT, with negligible coercivity (Hc) and remanence (Mr) even in the absence of an external magnetic field. The saturation magnetization (Ms) of the SPIONs is about 29.75 emu/g, while that of the bulk Fe3O4 is 92 emu/g.46) When the size of magnetic nanoparticles is reduced below a critical value (12.7 nm for SPIONs), the KBT term becomes greater than the energy barrier, causing magnetic anisotropy. Consequently, thermal energy can reorient the domains, which causes the hysteresis to diminish and results in a zero coercive field, leading to superparamagnetism.47) As the black particles in Fig. 6 were attracted toward the magnet, the SPIONs can easily be separated from the emulsion under an external magnetic field.

3.7. Dielectric studies of SPIONs

The dielectric measurements of the SPIONs were performed in the frequency range 100 Hz to 5 MHz at various temperatures, 313 - 353 K. A SPIONs sample was mounted between two electrodes. The capacitance of the parallel plate capacitor formed by the electrodes with the sample as a dielectric medium was measured.
Both the samples were sputtered with silver paste. The variation in capacitance was recorded in the frequency range 100 Hz to 5 MHz at different temperatures. The plot of the dielectric constant (ɛr) versus temperature is shown in Fig. 7(a). The ɛr decreases with increasing applied frequency of SPION pellets, with a value of about 16.3 at 5 MHz. Both dielectric constant and dielectric loss (ɛ″) were measured using the following equation (3 & 4):
where ‘c’ is the capacitance, ‘d’ is the thickness of the sample, ‘A’ is the cross-sectional area, and ɛ0 is the free space permittivity (8.854 × 10−12 F/m). In Table 3, the dispersion of ɛr with applied frequency at various temperatures is shown in Fig. 7(a). The high value of ɛr at low frequency may be ascribed to the presence of electronic, ionic, orientation, and space charge polarizations.48) The low values at higher frequencies may be ascribed to the gradual decrease of these polarizations.
Across all the temperatures, the value of ɛr gradually decreases when the samples are probed beyond the 42 Hz -5 MHz range. This may be due to the fact that the influence of the temperature-dependent space charge polarization on ɛr is only significant at frequencies below 1000 Hz. Therefore, above this range, the ɛr values of the SPIONs are almost constant. The typical values of ɛr at 5 MHz for various temperatures are listed in Table 3.
Similarly, the dielectric loss (ɛ″) of the SPIONs as a function of frequency at different temperatures is shown in Fig. 7(b). Observably, ɛ″ decreases as the frequency increases and is almost constant at higher frequencies. The trend observed could be ascribed to dipole polarization. The typical values of ɛ″ for 5 MHz at 313 K is found to be 1.05. Furthermore, the increase in dielectric loss with temperature may be attributed to increasing lattice vibrations and generation of phonons which interact with the charge carriers leading to electron phonon scattering.49,50) The dielectric relative loss factor (rlf) is also calculated from (tanδ/ɛr) to measure the purity of the sample. Low rlf values correspond to high purity.
The variation in AC conductivity (σac) with frequency at (RT) is illustrated in Fig. 8(a-b) It is obvious from the log σ versus log ω plots that the total AC conductivity is a sum of two terms: σac(ω, T) = σdc(T) + σac(ω), where the first term is temperature dependent and independent of frequency. This can be regarded as the DC conductivity, which obeys the Arrhenius relation. The DC conductivity value is calculated to be 2.29 × 10−10(S/cm) at RT. Fig. 9 demonstrates the temperature dependence of the AC conductivity, σac(ω), for the SPIONs. At lower temperatures, conductivity varies with frequency. However, at higher temperatures, the conductivity curves at different frequencies merge, resulting in what is known as intrinsic conductivity.51) The influence of temperature on AC conductivity has been explained by considering the mobility of charge carriers that is responsible for hopping. As temperature increases, the mobility of hopping electrons between Fe2+↔Fe3+ ions improves, thereby increasing conductivity. This frequency dependent conductivity, σac (ω), which increases with frequency according to Huseynov et al.,52) is a common feature to all semiconductor materials.
The AC conductivity was determined using the equation (5):
where ω is the angular frequency, ɛr is the relative dielectric constant, ɛ0 is the permittivity of free space, and tanδ is the tangent loss. The AC conductivity versus temperature plots in Fig. 9 show a direct correlation. The AC activation energy, determined from the slope of the linear plot in each region, varies in the ranges 0.325 - 0.523 eV and 0.482 - 0.775 eV for the high (E1) and low (E2) temperature regions, respectively. The decreasing trend of activation energy is due to increasing conductivity. The linear increase in σac reveals the polaron hopping conduction mechanism in the SPIONs.53) At 5 MHz, the σac value is about 1.08 × 10−3 S/cm.
The complex impedance measurements (Z′ and Z″) at various temperatures between 313 and 353 K were recorded. Cole-Cole plots were drawn (Fig. 10) at RT. Although semicircles are derived from the data points, the relaxations are of the non-Debye type, since the centers of semicircles lie below the real axis of impedance. However, at higher temperatures, the SPIONs exhibit complete semicircular arcs. The centers of these arcs are above the real axis, and hence confirm that the sample is of high homogeneity and obeys ideal Debye relaxation.54)

4. Conclusions

SPIONs have been synthesized using a co-precipitation technique, whereby the quantum confinement effect due to particle size leads to a band gap energy of 2 eV, which is significantly higher than those found in previous reports (0.12 eV). This greatly improves the UV blocking properties of the Fe3O4 nanoparticles. The XRD patterns of the samples confirmed their cubic spinel structure, with the space group Fd3m. The FTIR spectrum indicated the presence of absorbed water in the nanoparticulate matrix through peaks that were related to the stretching of the Fe-O bonds. Water might have been trapped inside the matrix even after drying, suggesting that the vibrational structure of the molecule is hydrated. FE-SEM and EDX measurements of the SPIONs revealed that the morphology of the obtained powders is spherical in nature. Trace quantities of Cl and S have no impact on the size and shape of the as-grown nanoparticles. The average size of the particles is 12.7 nm, with a narrow particle distribution. HRTEM analysis revealed that only a few Fe3O4 nanoparticles agglomerated. This condition and the obtained SAED pattern agree with the XRD results. VSM yielded Ms, Hc, and Mr values of 29.75 emu/g, 8.201 Oe, and 0.006 emu/g at RT, respectively. Complex impedance measurements revealed that the values of ɛr and ɛ″ of the SPIONs at 5 MHz were 16.3 and 1.05, respectively. The congruence of the resulting Nyquist plot with the Cole-Cole plot implies that the samples exhibit good homogeneity and follow Debye relaxation.


The authors are thankful to Dr. A. Mohan., Department of Physics, School of Advanced Sciences, VIT University, Vellore-632 014, Tamil Nadu, India, for the fruitful discussions.

Fig. 1
X-ray diffraction pattern of SPIONs.
Fig. 2
Fourier transformation infrared spectrum of SPIONs.
Fig. 3
UV-vis absorption spectra of SPIONs.
Fig. 4
(a) FE-SEM image and (b) EDX spectrum of SPIONs.
Fig. 5
(a-b) HRTEM and lattice fringes, (c) particle size distribution, and (d) SAED pattern.
Fig. 6
VSM of the SPIONs tested by placing a magnet near the bottle.
Fig. 7
Temperature dependence of (a) dielectric constant (ɛr) and (b) dielectric loss (ɛ″).
Fig. 8
(a) log σ versus Temperature and (b) frequency plots of SPIONs.
Fig. 9
lnσac versus 103/T plots of SPION.
Fig. 10
Z′ versus Z″ plots (Nyquist plots) of SPIONs.
Table 1
Comparative Chart of Particle Sizes and Eg Relative to the Present Work
S.No Literature Synthesis methods Particle size obtained from TEM (nm) Eg (eV)
1 Aroonsri Priprem et al.43) Co-precipitation 15 Not specified
2 Deepak et al.38) One pot thermal decomposition 12 Not specified
3 Vineet Kumar et al.45) Chemical co-precipitation 19 Not specified
4 Lin Zhuang et al.46) Solvothermal method 60 Not specified
5 Manohar et al.34) Colloidal nanocrystal 12 0.12
6 Present work Co-precipitation 12.7 2
Table 2
Magnetic Parameters Obtained from the VSM Analysis of SPIONs
Sample code Average crystallite size XRD (nm) Saturation Magnetization Ms (emu/g) Coercivity Hc (Oe) Remnant magnetization Mr (emu/g) Remanence ratio (Mr/Ms)
SPIONs 6.81 29.75 8.201 0.0063 0
Table 3
Data on the Dielectric Properties of SPIONs
Sample ɛr (100 Hz - 5 MHz) ɛ″ (100 Hz - 5 MHz) tanδ/ɛr σac(S/cm) Activation energy in (eV)

E1 E2
SPIONs 90.3 - 16.3 105.73 - 1.05 0.057 1.08E-03 0.325 - 0.523 0.482 - 0.775


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