Background

Magnetic nanocomposites consisting of spinel ferrite nanoparticles in a non magnetic SiO2 matrix exhibit interesting properties arising in size effects and magnetic interactions [1–5]. Among them, CoFe2O4-SiO2 magnetic nanocomposites have high potential for applications as magnetic fluids [6], drug delivery [7], and high density information storage [8] due to remarkable properties of bulk cobalt ferrite (high saturation magnetization and coercivity, strong anisotropy, mechanical hardness and chemical stability) [9], combined with the magnetic properties characteristic of nanoparticles, which depend strongly on particle shape and size, particle-matrix interactions and degree of dispersion throughout the matrix. Recently, cobalt ferrite nanoparticles were also known to be a photomagnetic material that shows a remarkable light induced coercivity change [10–12].

Based on the above technological challenge and scientific importance, researches such as ceramic method [13], sol-gel [14], co-precipitation [15], solvent evaporation [16], hydrothermal [17], combustion [18], microemulsion [19] and citrate methods [20] have been made into various synthesis routes of nanocrystalline ferrites. In the earlier report, cobalt ferrite nanoparticles have been synthesized by the polymeric precursor method [21]. While the nanoparticles obtained usually have a strong tendency to aggregate, this makes it very difficult to exploit their unique physical properties [22]. To reduce the unwanted crystallite coarsening and particles aggregation, attempts have been made to synthesize nanocomposites by embedding ferrite nanoparticles in a suitable matrix [23]. Different matrixes such as resins [24], polymer films [25] and silica glasses [26, 27] have been studied. Studies on magnetic nanocomposites of ferrite nanoparticles dispersed in the silica matrix [28, 29] have revealed a behavior different from that of bulk systems.

Among various synthetic routes, sol-gel process has proved to be an efficient method to prepare ultra-fine particles dispersed in different matrices. Through this method, a good control of the sample morphology, texture, structure, and chemical composition can be attained by carefully monitoring the preparation parameters. The size and morphology of the nanoparticles and their properties may be controlled by modifying the composition of the nanocomposites and by thermal treatment conditions [30]. This is the reason why the sol-gel synthesis method has gone an intensive development.

Tetraalkoxysilanes (tetramethoxysilane, TMOS and tetraethoxysilane, TEOS) are common precursors to synthesize silicate. Their hydrolysis in aqueous solutions and further polycondensation reactions cause formation of sol particles of which the cross-linking leads to the self-organization into a porous three-dimensional network in the bulk. In view of the fact that tetraalkoxysilanes are poor-water soluble compounds, methanol or ethanol is generally added to avoid the phase separation [31, 32]. This problem has been countered by the use of polyol silicates possessing improved water solubility [33] I. Gill and A. Ballesteros, Encapsulation of biologicals within silicate, siloxane, and hybrid sol-gel polymers: an efficient and generic approach. J. Am. Chem. Soc. (1998), pp. 8587-8598. TMOS and TEOS, as shown recently in [34], can be also exchanged for tetrakis(2-hydroxyethyl) orthosilicate (THEOS). This completely water-soluble precursor forms nanocomposite monolithic material in aqueous solutions in the absence of added alcohol.

In this paper, effects of calcination temperature on structural and magnetic properties of cobalt ferrite nanocomposites in silica matrix prepared by sol-gel method using tetrakis(2-hydroxyethyl) orthosilicate (THEOS) as silica precursor have been reported aiming at tuning the magnetic properties of CoFe2O4 nanoparticles dispersed in a sol gel silica matrix and greatly expanding the range of applications by adjusting the calcination temperature. Also, FT-IR and thermal analysis (TG-DTG-DTA) of the alcogel precursor have been carried out. Therefore, special attention is given to the correlation between the structural and magnetic properties of CoFe2O4 nanoparticles embedded in THEOS as silica precursor for different calcination temperatures.

Experimental

All the chemicals were of analytical grade and used without any further purification. Nanocomposites of cobalt ferrite dispersed in a silica matrix were prepared by sol-gel process using tetrakis(2-hydroxyethyl) orthosilicate (THEOS) as a water-soluble silica precursor of silica and metallic nitrates as precursors of the ferrite. The THEOS:H2O and Fe:Co molar ratios were controlled at 1:5 and 2:1, respectively. The weight ratio of nanocomposites was 30 wt.% CoFe2O4 in the silica matrix. The sol was prepared by dissolving Fe(NO3)3.9H2O and Co(NO3)2.6H2O in deionized water, followed by the addition of the aqueous solution of THEOS. After vigorous stirring for 1 h, the sol was allowed to gel at room temperature for some days in a partially closed glass vessel. The obtained alcogel was put into an oven for further drying at 110°C for 24 h to obtain the xerogel. The xerogel was calcined at different temperatures varying from 400 to 1000°C for 2 h with a heating rate of 10°C/min in ambient atmosphere.

X-ray diffraction (XRD) patterns were collected using a Philips PNA-analytical diffractometer with CuKα radiation. FT-IR spectra (500-4000 cm-1) were recorded on a Perkin Elmer Spectrum One spectrophotometer with KBr pellets. Thermal analyses (TG-DTG-DTA) including the thermogravimetery (TG), derivative thermogravimetery (DTG) and differential thermal analysis (DTA) were carried out using a Perkin Elmer simultaneous thermal analyzer (STA Pyris Diamond Model) with the heating rate of 5°C/min in flowing air. The TEM images and selected area electron diffraction (SAED) pattern were recorded on a Philips CM 200 FEG transmission electron microscope. Magnetic measurements were carried out at room temperature using a vibrating sample magnetometer (VSM).

Results and Discussion

X-ray diffraction (XRD) analysis

The XRD patterns of the samples calcined at different temperatures varying from 400 to 1000°C were shown in Figure 1 to investigate the influence of the calcination temperature on the structure. The weak diffraction peaks assigned to CoFe2O4 appeared at 400°C suggesting that the particles of CoFe2O4 had been nucleated in the silica matrix. X-ray diffraction patterns showed poor crystallinity up to calcination temperature of 600°C.

Figure 1
figure 1

XRD patterns of the nanocomposite samples calcined at different temperatures varying from 400 to 1000°C.

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Our results showed that with increasing calcination temperature, the intensity of peaks increases and the diffraction peaks become sharper and narrower. This indicates the enhancement of the crystallinity which originated from the increment of the crystalline volume ratio due to the size enlargement of the nuclei [35, 36]. The full-width at half maximum (FWHM) of the diffraction peaks decreases with increasing calcination temperature discloses that the average crystallite size is becoming bigger correspondingly. The very broad peak at 2θ of around 23° in XRD patterns of all samples was attributed to the characteristic diffraction peak of the amorphous SiO2 matrix.

All of the diffraction peaks confirmed the formation of the pure single-phase cobalt ferrite with the face-centered cubic spinel phase and Fd3 m (2 2 7) space group. No diffraction peaks of impurities were observed in the patterns. It showed that in comparison with the previous report using TEOS as a silica precursor [37], Co-ferrites with more crystallinity have been successfully synthesized at lower calcination temperatures under current mild experimental conditions.

The increase of the calcination temperature results in sharper peaks with the increased intensity and higher crystallization without changes in the obtained phases.

The influence of the calcination temperature on the crystallite sizes of the nanocomposite samples were shown in Tables 1.

Table 1 Crystallite size and magnetic properties of the nanocomposite samples calcined at different temperatures varying from 400 to 1000°C.
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The crystallite size of all samples prepared at different calcination temperatures estimated from XRD peak broadening using Scherrer's formula [38]

(1)

where t is the crystallite size, λ the wavelength of X-ray radiation (CuKα), θ the Bragg angle and β is the full width at half maximum (FWHM) of the most intense diffraction peak (311). The crystallinity and crystallite size increase at higher calcination temperatures, indicating that the silica network plays an important role in restricting the growth and aggregation of Co-ferrite nanoparticles.

FT-IR analysis

Figure 2 shows the FT-IR spectra of the alcogel precursor and CoFe2O4/SiO2 samples calcined at different temperatures varying from 400 to 1000°C. The broad band at 1630 cm-1 in the IR spectrum of the alcogel ascribed to the H-O-H bending vibration of the free or absorbed water. As shown in Figure 2(a), the band at 1384 cm-1 is associated with the antisymmetric NO3- stretching vibration arising from the residual nitrate groups in the alcogel. Using THEOS as precursor, the silica network is formed and characterized by the strong absorptions at 1076, 825 and 471 cm-1 corresponding to the Si-O-Si antisymmetric stretching and bending mode [39] which shows a shift to lower wavelength in comparison with the previous report using TEOS as silica precursor [40].

Figure 2
figure 2

FT-IR spectra of (a) alcogel and nanocomposite samples calcined at (b) 400°C, (c) 500°C, (d) 600°C, (e) 900°C, (f) 1000°C.

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In IR spectra of samples calcined at different temperatures varying from 400 to 1000°C, the intensities of the broad bands associated with the absorbed water are drastically weakened. Also, the disappearance of the absorption at 1384 cm-1 could be ascribed to the complete decomposition of the nitrate species after calcination, as confirmed by the thermal analysis. The band at 605 cm-1 assigned to the Si-O-Fe vibration increases in intensity with increasing the calcination temperature, which can be ascribed to the enhanced interactions between CoFe2O4 particles and the silica matrix [41]. The characteristic absorptions for the silica network slightly increased in intensity with increasing calcination temperature. With increasing the calcination temperature the intensity of ≡Si-O-Si≡ absorption band of the SiO4 tetrahedron of the silica network at 1079 cm-1 increases.

Thermal analysis

The simultaneous thermal analyses (TG-DTG-DTA) of the alcogel were shown in Figure 3. The thermogravimetery (TG) and derivative thermogravimetery (DTG) curves show two stages of the weight loss. First stage of the weight loss at about 100°C was attributed to the loss of water and some gases adsorbed on the surface, which corresponds to an endothermic peak in the differential thermal analysis (DTA) curve. The second one at about 200°C was ascribed to the burning of residual organic groups accompanied by an exothermic peak in the DTA curve which occurs at lower temperature in contrast to the previous report using TEOS as a silica precursor [42]. We can observe a broad endothermic event between 800-1000°C associated with the densification of the nanocomposites. Above 300°C the weight loss is almost negligible showing that the majority of the mass loss occurs under 300°C which allows for optimization of the calcination temperature. These results were in agreement with the FT-IR spectroscopy and XRD ones.

Figure 3
figure 3

Thermal analyses of the alcogel (a) TG-DTA and (b) TG-DTG.

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Transmission electron microscopy (TEM) analysis

TEM images and selected area electron diffraction (SAED) pattern of the nanocomposites calcined at 600 and 800°C were shown in Figure 4. TEM observations indicate that almost spherical Co-ferrite nanoparticles were embedded in the silica network. The average particle sizes of the nanocomposites calcined at 600 and 800°C were about 10 nm and 27 nm, respectively, in accordance with the results obtained from XRD analyses according to the Scherrer's formula. The diffraction dots and diffuse rings of different lattice planes in the SAED pattern (Figure 4c) were in good agreement with the present spinel system.

Figure 4
figure 4

TEM micrographs of nanocomposites calcined at 600°C (a), 800°C (b) and SAED pattern (c).

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Magnetic measurements

To investigate the influence of the calcination temperature on magnetic properties of nanocomposite samples, hysteresis loops of samples calcined at different temperatures varying from 400 to 1000°C were analyzed by VSM, as shown in Figure 5. Also, the corresponding magnetic parameters were listed in Tables 1.

Figure 5
figure 5

Hysteresis loops of nanocomposite samples calcined at different temperatures varying from 400 to 1000°C.

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It can be observed that the values of Ms and Mr were increased by increasing the temperature from 400 to 1000°C which arising from spin non-colinearity at the surface of the crystals. The changes in the magnetic properties of the samples can be attributed to the modification of the crystallinity and crystallite sizes dependent on the calcination temperature. The energy of a magnetic particle in the external field is proportional to its particle sizes via the number of molecules in a single magnetic domain. Therefore, the decrease of the Ms values with the decrease of particle sizes can be attributed to surface effects that are the result of finite-size scaling of nanocrystallites [43].

The variation of the saturation magnetization Ms and remanent magnetization Mr as a function of temperature were shown in Figure 6. To calculate the saturation magnetization (Ms) the magnetization values (M) were plotted vs. 1/H. The Ms was calculated from the extrapolation of the magnetic curve at the magnitude of M when 1/H≈0 (Tables 1).

Figure 6
figure 6

Variation of M s and M r of nanocomposite samples as a function of the calcination temperature.

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It can be observed that the Ms and Mr values for samples calcined at different temperatures were increased by increasing the temperature (Figure 5). This type of behavior is entirely consistent with a model of particle growth in the system in such a way that differences in the magnetic parameters are associated with changes in the particle size [43]. The variation of coercivity Hc was not in accordance with that of Ms and Mr, indicating that Hc is not determined only by the size of nanoparticles. Hc values were significantly less than previous reports using TEOS as a silica precursor [37, 40]. Therefore changes in magnetic properties such as superparamagnetism and ferromagnetism of samples can be recognized by the modification of the crystallinity and crystallite sizes dependent on the calcination temperature [44]. The lower Ms values related to the particles with the smaller size could be attributed to the surface distortion due to the interaction of transition metal ions in the spinel lattice with the oxygen atoms, which can reduce [45] the net magnetic moment in the particle. This effect is particularly prominent for the ultrafine particles due to their large surface to volume ratio. Finite size effects have been reported as being responsible for the reduction of the saturation magnetization of nanoparticles [46].

It is found that the M-H curves of samples calcined at 400-600°C take on incomplete reversibility, and corresponding Mr values is about 0.01 emu/g, which means that samples are superparamagnetic. When the calcination temperature is up to or above 800°C, typical saturated hysteresis loops can be observed. For samples calcined at 400-600°C, the size of most nanoparticles is smaller than the critical size to remain ferromagnetic; hence they will show superparamagnetic behavior. However, if the calcination temperature is increased until the size of most nanocrystallites exceeds the critical size, there will be noncoherent magnetization change in the nanoparticles themselves, and sample shows ferromagnetic properties. Therefore, we can change the calcination temperature of nanocomposites to achieve ideal magnetic properties and behavior. Calcination temperatures at 400-600°C can be applied if samples used in areas such as ferrofluid technology which CoFe2O4 should be of superparamagnetic.

Conclusions

In summary, the influence of the calcination temperature on the magnetic properties and crystallinity of cobalt ferrite nanocomposites successfully synthesized by sol-gel method using tetrakis(2-hydroxyethyl) orthosilicate (THEOS) have been investigated with the aim of tuning the magnetic properties and greatly expanding the range of applications. The tetrakis(2-hydroxyethyl) orthosilicate as silica matrix network provides an ideal nucleation environment to disperse CoFe2O4 nanoparticles and thus to confine them to aggregate and coarsen. By using THEOS as precursor over the currently used TEOS and TMOS, the organic solvents are not needed owing to the complete solubility of THEOS in water. Particle sizes of the samples increased with the calcination temperature. Our results showed that the magnetic properties of the nanocomposite samples were strongly affected by the calcination temperature as a consequence of the gradual increase in the crystallinity and particle size. The saturation magnetization for all the samples was lower than that of the CoFe2O4 bulk phase owing to the particle sizes obtained. Therefore, size-adjustable and magnetic controllable cobalt ferrite nanoparticles were obtained by embedding CoFe2O4 particles in the amorphous silica network and controlling suitable calcination temperature. The magnetic properties of the synthesized nanocomposites indicate that these materials have good potential for important technological applications, e.g. in ferrofluid technology, bioprocessing and magneto-optical devices.