Size Effect of Fe3O4 Nanoparticles on Magnetism and Dispersion Stability of Magnetic Nanofluid

It is well known that magnetic nanofluids are widely applied in various fields ranging from heat transfer to miniature cooling, and from damping to sealing, due to the mobility and magnetism under magnetic field. Herein, the PFPE-oil based magnetic nanofluids with superior magnetization and dispersion stability were obtained via regulating reaction temperature. The structures of particles were characterized by X-ray diffraction (XRD) and transmission electron microscopy (TEM). The size effects of particles on the magnetism and coating effect of particles, and on the stability and saturation magnetization of the fluids were characterized by Fourier transform infrared spectroscopy (FTIR), thermogravimetric analysis (TGA), vibrating sample magnetometer (VSM) and density instrument, respectively. The results indicate that the impurity phase FeOOH only appear in the sample prepared at 18°C and the average size of Fe₃O₄ nanoparticles reduces from 120 to 20 nm with raising reaction temperature. The saturation magnetization of Fe₃O₄ particles increases firstly and then reduces with increasing particle size, which is affected by the thickness of magnetic dead layer and impurity phase FeOOH. The Fe₃O₄ particles could be chemically coated by PFPE-acids, and the coated mass is a little affected by particle size. The stability of the nanofluids lowers while the saturation magnetization increases firstly and then decrease with increasing particle size. At reaction temperature of 60°C, Fe₃O₄ particles of 25 nm and the nanofluids with superior stability and saturation magnetization were obtained. Our results indicate that the control of nanoparticles size by regulating reaction temperature can be a useful strategy for preparing magnetic nanofluids with desirable properties for various potential applications.

Introduction

The nanofluids are colloidal suspensions composed of various nanoparticles (Al₂O₃, TiO₂, ZnO, CuO, SiO₂, Fe₃O₄, etc.) (Shahrul et al., 2016; Nayak et al., 2020; Aldabesh et al., 2021; Awan et al., 2021; Iskander, 2021; Khan et al., 2021; Tlili et al., 2021), and these particles have different characteristics, for example, ZnO has the highest thermal conductivity, SiO₂ has lowest thermal conductivity, Fe₃O₄ has magnetism and enhancement of thermal conductivity (Lemes et al., 2017). Magnetic nanofluids have magnetism and mobility under a magnetic field, and thus, which are called “smart materials” and widely applied in many fields, such as heat transfer, miniature cooling, damping, biomedicine and sealing (Yadav et al., 2013; Akbar et al., 2016; Shahsavar et al., 2016; Chen et al., 2018; Chen et al., 2019).

The performance and applications of magnetic nanofluids depend on their stability, which is related to the proper dispersion of nanoparticles (Chen et al., 2016a; Colla et al., 2012; Aishwarya et al., 2013; Mabood and Akinshilo, 2021). Control of the pH value of suspension, or addition of surfactants, aim to change the surface properties of suspended nanoparticles to avoid the formation of the clusters and achieve a stable suspension (Socoliuc and Vékás, 2014). Most of the studies on the magnetism and stability of magnetic nanofluids are carried out in nanofluids with particle size >20 nm, such suspensions are less stable, due to strong dependence of particle size d on the sedimentation velocity V∝d² (Mahbubul, 2019).

However, the high saturation magnetization of magnetic nanofluids is needed in various applications, such as big gap sealing and biomedicine (Sharifi et al., 2012; Yang et al., 2013). The conventional ferrofluids possess low saturation magnetization due to their small average particle size (i.e., ∼10 nm) and the differences of particle morphology and types of magnetic component (López-López et al., 2012). Even though some magnetorheological fluids contain larger average particle size (i.e., ∼ 1 µm) with higher saturation magnetization (Tang, 2011), they exhibit unsatisfied dispersion stability compared to ferrofluids (Chen et al., 2021). Therefore, the two critical parameters, saturation magnetization and stability, must be considered simultaneously for different nanofluids application occasions.

It is well known that the size of magnetic nanoparticles has a great impact on the electronic, optical and magnetic properties compared with their bulk counterparts. Particularly, saturation magnetization can be well-tuned by modifying their size using different synthesis approaches. The Fe₃O₄ particles with size between 67 and 143 nm were obtained via regulating the ion concentration through an one-pot method, and the saturation magnetization of particles increases from 63.0 emu/g to 68.9 emu/g (Dong et al., 2016). The Fe₃O₄ particles with average size in range of 21–123 nm were obtained by regulating reaction time via hydrothermal process and the saturation magnetization also increases from 77.9 emu/g to 92.5 emu/g (Ozel et al., 2015). Li J. H. prepared the Fe₃O₄ nanocrystals by thermal decomposition, the range of particle size is from 4 to 12 nm and the saturation magnetization of Fe₃O₄ increase from 25 emu/(g Fe) to 102 emu/(g Fe) (Jun et al., 2005). Particle size has a strong effect on the magnetic properties of nanoparticles, and which turned out to be caused by the magnetic dead layer. In addition, Brownian motion provides a physical foundation for stability in magnetic nanofluids applications, also determined by the magnetic particle size (Fannin and Charles, 2001). The magnetic nanoparticles of small size are beneficial to the stability of magnetic nanofluids. Therefore, it is important to tune the magnetic property and size of nanoparticles in terms of saturation magnetization and stability of magnetic nanofluids.

The aims of this paper are to prepare Fe₃O₄ nanoparticles with different sizes and optimize the saturation magnetization of magnetic nanofluids with high dispersion stability, thus to facilitate their applications in thermal conductivity, big gap sealing and other occasions.

Experimental

Preparation of Fe₃O₄ Nanoparticles and PFPE-Oil Based Magnetic Nanofluids

Briefly, ferrous sulfate (FeSO₄·7H₂O), sodium hydroxide (NaOH), sodium nitrate (NaNO₃), hydrochloric acid (HCl), ethyl alcohol (C₂H₅OH), PFPE-acids (C₃F₇O-(C₃F₆O)_n-C₃F₄O₂H, of which n is about 10) and PFPE-oils [F-(C₃F₆O)_n-C₂F₅, of which n is about 27] were all purchased from a local chemical supplier. All chemicals were of analytical grade and were used without any further purification.

First, the NaOH (0.5 M, 20 g), NaNO₃ (0.1 M, 8.5 g), and FeSO₄·7H₂O (0.1 M, 27.8 g) were dissolved in 1,000 ml ultrapure water by stirring at room temperature, respectively. The solutions containing sodium ions were mixed and added to the solution containing iron ions, and then a stirring process was applied for 5 min when the stirring speed was 100 r/min. After that, the oxidation precipitation reaction was carried out at various temperatures (i.e., 18°C, 35°C, 45°C, 60°C, 80°C) for 24 h, respectively. And then, the pH of reaction solutions was adjusted to be ∼7 by dropping in HCl, and then PFPE-acids (6 g) were added and mechanical stirring was carried out to coat the Fe₃O₄ nanoparticles. These coated nanoparticles were washed with deionized water (DIW) and C₂H₅OH until the pH of the solution was neutralized. Once the solution was neutralized, these nanoparticles were dried and subjected to characterizations.

Finally, these Fe₃O₄ nanoparticles were dispersed in PFPE-oil for preparing a series of magnetic nanofluids possessing different average particle sizes. The solid concentration in the magnetic nanofluids remains 10 wt.%. Figure 1 presents a schematic illustration of the preparation process of magnetic nanofluids.

FIGURE 1

FIGURE 1. Schematic illustration of the preparation process for Fe₃O₄ nanoparticles dispersed in PFPE oil-based magnetic nanofluids.

Characterization Methods

X-ray diffraction (XRD) analysis was performed on a DX-2700X X-ray diffractometer equipped with Cu Kα (λ = 0.154 nm) radiation. Scans were made from 10° to 80° at the rate of 0.085 deg./s. High-resolution transmission electron microscopy (TEM: JEM-2000EX) was employed to study the microstructure and size dispersion of synthesized Fe₃O₄ nanoparticles. A vibrating sample magnetometer (VSM, Lake Shore 7410) was used for the magnetic characterization of nanoparticles and ferrofluids at an external magnetic field ranging from −2.5×10⁴ Oe to +2.5×10⁴ Oe at 25°C. Fourier Transform Infrared Spectrometer (FTIR, Nicolet iS10) spectra were recorded over the wavenumber range of 400–4,000 cm⁻¹ to investigate the interactions between surfactants and magnetic nanoparticles. Thermogravimetric analysis (TGA) of coated nanoparticles was performed using a TGA, TG209F1 analyzer, from RT to 600°C with a heating rate of 10°C/min in an argon atmosphere. A densimeter (ST-300GM) was used to measure the density of a magnetic nanofluids. All the magnetic nanofluids samples were centrifuged for two hours at 5,000 rpm to measure the magnetic nanofluids saturation magnetization and the stability.

Results and Disscussion

The Structures of Nanoparticles

Figure 2 shows the XRD patterns of the Fe₃O₄ nanoparticles prepared at various reaction temperatures. The diffraction peaks of Fe₃O₄ nanoparticles correspond to the planes, such as (111), (220), (311), (400), (422), (511), (440), and (533) that can be unambiguously observed [PDF#88-0315] (Vasilescu et al., 2018; Kamali et al., 2016). With the increasing temperature, the peaks intensity and full-wave half maximum (FWHM) were observed, indicating that Fe₃O₄ nanoparticles contain a significant volume fraction of single-phase crystalline structure. On the other hand, the Fe₃O₄ nanoparticles prepared at room temperature (RT), the dual-phase structure consisting of the Fe₃O₄ spinel phase seemed dominant (Yang et al., 2012) and an impurity phase as well. From the extended XRD profiles in Figure 2B, the diffraction peaks at 2θ values of 21.24, 33.24, and 36.66 correspond to the reflections of the (110), (130), and (111) planes of α-FeOOH (PDF#81-0464), and which can be identified from these three peak planes marked with black diamond symbols. These results suggest that in the synthesis process of Fe₃O₄, the intermediate product α-FeOOH formed when the synthesis process was carried out at RT. At higher oxidation reaction temperatures, the intermediate product α-FeOOH are vanished, indicating that α-FeOOH is wholly converted to Fe₃O₄ material (Altman et al., 2004; Jia and Gao, 2007; Li et al., 2011).

FIGURE 2

FIGURE 2. (A) XRD profiles of the samples prepared at different reaction temperatures, (B) the extended XRD profiles from 20 to 40°.

Figures 3A–E shows the TEM images and size distributions of the Fe₃O₄ nanoparticle synthesized at different temperatures. It can be seen that all the nanoparticles are nearly quadrilateral in shape. The average size and the distribution span of the nanoparticles decrease with the increase of temperature.

FIGURE 3

FIGURE 3. TEM images and size distributions of Fe₃O₄ nanoparticles prepared at different temperatures: (A) 18°C (RT), (B) 35°C, (C) 45°C, (D) 60°C, and (E) 80°C, and the insets represent of particle sizes.

In general, the increase of reaction temperature is conductive to the growth of particles. Here, the estimated average nanoparticles size synthesized at oxidation reaction temperature varied from room temperature (RT) to 80°C is 118.7, 69.9, 49.3, 24.6, and 20.1 nm, particle size decreases with increasing temperature. The similar effect of temperature on particle size has appeared and has been well revealed by Wang W. (Wang et al., 2008). and K. Nishio (Nishio et al., 2007). These studies revealed that the particle size could be effectively controlled at the nucleation stage. When the total volume of all nanoparticles is constant, the volume of one particle is inversely proportional to the final number of nanoparticles. The final number of nanoparticles could be expressed by the equation (Eq. 1) (Sugimoto et al., 1998)

$n_{+}^{\infty }=Q_0{V}_m/v_{+}(1)$

Where, $n_{+}^{\infty }$ is the number of nanoparticles, $Q_0$ the rate of monomer provided, $V_m$ the molar volume of solids and $v_{+}$ indicates the volume growth rate of a single particle. When the increased effect caused by temperature on $Q_0$ is greater than the effect on $v_{+}$, $n_{+}^{\infty }$ increases and the final size of nanoparticles decreases. And therefore, the increase of the oxidation reaction temperature causes the decrease of particle size.

The Magnetism of Nanoparticles

In order to analyze the magnetic properties of Fe₃O₄ nanoparticles synthesized at different temperatures, magnetic field-magnetization (H-M_s) characteristics are measured, as shown in Figure 4A. It should be noted that the saturation magnetizations are 81.7, 89.8, 94.9, 82.8, and 71.0 emu/g for the samples synthesized at 18, 35, 45, 60, 80°C, respectively. Besides, the inset in Figure 4A shows that the coercivities of nanoparticles are small and fall in the interval of 75 through 125 Oe. On the other hand, the Fe₃O₄ particle size decreases with increasing reaction temperature, and thus, the saturation magnetization of nanoparticles decreases is shown in Figure 4B.

FIGURE 4

FIGURE 4. Magnetic properties of Fe₃O₄ nanoparticles prepared at different temperatures: (A) hysteresis loops, (B) preparation temperature dependence of magnetization M_s, (C) schematic illustration of the moment alignment of a magnetic nanoparticle.

The variation in magnetic parameters, such as saturation magnetization and coherence to average nanoparticles size are summarized in Table 1. From these results, it could be concluded that the nanoparticles synthesized at RT are of superparamagnetic-like materials, which has low saturation magnetization and due to the presence of impurity phase α-FeOOH with low magnetization. In contrast, the Fe₃O₄ particle size decreases with increasing reaction temperature, and thus, the saturation magnetization of nanoparticles decreases (Aslibeiki et al., 2012). Figure 4C illustrated the alignment of magnetic moments in nano-sized magnetic materials. The outer moments go around the surface layer instead of aligning with the externally applied field, not the same as in the core. Some moments offset in magnitude and decrease the total magnetization (Mathew and Juang, 2007). Because of this, generally, the outer surface is named as a magnetic dead layer. It has been reported that the magnetic dead layer arises from the destruction of the Fe-O-Fe chain physically (Poddar et al., 2005). The relationship between the saturation magnetization and particle size could be well defined by equation (Eq. 2) (Tang et al., 1991)

$M_{sn}=M_{sb}\left(1-6t/D\right)(2)$

Where, M_sb and M_sn are the saturation magnetization of bulk and nanomaterials, respectively, t is the thickness of the magnetic dead layer and D is the particle size. It is well known that increasing particle size is a useful method to increase the saturation magnetization of nanoparticles. From the preceding analysis, it can be understood that the nanoparticle prepared at 45°C has the maximum saturation magnetization of 94.9 emu/g compare with that of bulk Fe₃O₄ due to the absence of the secondary phase and relatively large particle size. All the nomenclatures used in the paper are shown in Table 2.

TABLE 1

TABLE 1. Particle sizes and magnetic parameters of Fe₃O₄ nanoparticles prepared at different temperatures.

TABLE 2

TABLE 2. All the nomenclatures used in the paper.

The Coated Effect of PFPE-Acid on the Nanoparticles

The FTIR curves of PFPE-acid and Fe₃O₄ nanoparticles coated with PFPE-acid were studied to gain insight into the coated effect of particles. Figure 5A shows that the peak located at 563.1 cm⁻¹ can be attributed to the Fe-O bond vibrations in Fe₃O₄ (Li et al., 2007). Also, the peaks centered at 1,238.1, 1,134.0, 1,307.5, and 983.5 cm⁻¹ confirm the existence of C-F, CF₂, CF₃, and C-O-C bonds, respectively (Ma et al., 2003). The stretching vibrations of C=O from COOH in the PFPE-acid shift from 1777.3 cm⁻¹ to 1,685.5 cm⁻¹ in coated Fe₃O₄ nanoparticles using PFPE-acid, which may be due to the red-shift effect of the covalent bonding with the bare charge on nanoparticles (Chen et al., 2016b). From these results, it can be concluded that the PFPE-acid is chemically adsorbed on the surface of Fe₃O₄ nanoparticles with various particle sizes in the range of 20–120 nm.

FIGURE 5

FIGURE 5. (A) FTIR curves of PFPE-acids and coated Fe₃O₄ nanoparticles with different particle sizes, (B) TGA curves of Fe₃O₄ nanoparticles coated with PFPE-acids.

Furthermore, TGA measurements are taken to further confirm the coating mass. Figure 5B shows the weight loss of nanoparticles with respect to temperature. Significant mass is decreased between 200 and 400°C, which may be caused by the decomposition of coated PFPE-acid. In contrast, above the 400°C, no mass loss is detected. As shown in the inset, the loss in mass is calculated, ranging between 32 wt% and 37 wt%, which suggests that the effect of nanoparticle size on the coated mass is insignificant. When chemically coated enough PFPE-acids, some excessive PFPE-acids will further be coated physically. Too much PFPE-acids coated on the nanoparticles will reduce the saturation magnetization and stability of the nanofluids, while less PFPE-acids will reduce the stability of the fluids. (Chen et al., 2018).

The Stability and Magnetism of the Fluids

Following investigations of saturation magnetization and weight loss effect of PFPE-acids and coated Fe₃O₄ nanoparticles, we further investigate the stability of Fe₃O₄ nanoparticles dispersed PFPE-oil based magnetic nanofluids. For this, Fe₃O₄ magnetic nanoparticles coated with PFPE-acid were dispersed in PFPE-oil to form magnetic nanofluids. The stability of the magnetic nanofluids is measured in terms of saturation magnetizations and densities before and after the centrifugation process. For this, all the samples were centrifuged for two hours at 5,000 rpm, and the centrifugal parameters are enough for the sedimentation of agglomerated particle and hence sufficiently characterizing the stability of the magnetic nanofluids. Temperature has obvious effect on particle size, and thus which will further influence the saturation magnetization and density of the magnetic nanofluids, fluid samples were taken from the upper part in centrifuge tubes. Before and after being centrifuged, the magnetic nanofluids were always black and without visible stratification. Figure 5 shows that the magnetizations are 0.56, 1.95, 4.55, 5.96, 5.91 emu/g for the magnetic nanofluids samples before centrifuging with average nanoparticles size of 118.7, 69.9, 49.3, 24.6, and 20.1 nm at 18, 35, 45, 60, and 80°C, respectively. In addition, considering the concentration of 10 wt% of the magnetic nanoparticles in the magnetic nanofluids, the theoretical magnetizations for the samples are 8.17, 8.98, 9.49, 8.28, and 7.10 emu/g, respectively. The decrease in the magnetization for the samples before centrifuging can be ascribed to precipitation of the large particle sizes of the magnetic nanoparticles (Table 1). After adding the Fe₃O₄ nanoparticles into the PFPE-oil, some nanoparticles with large size and uneven coating with PFPE-acid precipitate directly and cause the reduction in magnetization. Also, with increasing the average sizes of magnetic nanoparticles, magnetization increases and tends to be stable at temperatures above 60°C. The reduction in the particle size is responsible for this tendency. The magnetization curve shows the same pattern after the centrifugation process, but the magnetization is observed to decrease further. From these results, it can be understood that further sedimentation during centrifuging occurs because of particle aggregation.

Figure 6 also shows that the densities of the surface fluids before and after centrifugation vary close to magnetization. The sedimentation of nanoparticles in the magnetic nanofluids can be restrained by hydraulic resistance, and the sedimentation velocity could be obtained by the Stokes equation (Eq. 3) (Amirat and Hamdache, 2009)

$v=\frac{\left({\rho }_{N_p}-{\rho }_{N_c}\right)g{d}_p^2}{18{\eta }_c}(3)$

Where, ${\rho }_{N_c}$ is the density of a base liquid, ${\rho }_{N_p}$the density of particle Fe₃O₄, ${\eta }_c$ the dynamic viscosity, d_p the average particle size, and g the acceleration due to gravity. This equation indicates the sedimentation velocity decreased with an increase in viscosity of base liquid and a decrease in the density deviation between the base liquid and the magnetic particle. In addition, the sedimentation velocity increases significantly with the increase of particle size d_p. The increase in particle size is advantageous to increase the saturation magnetization of the fluids while it is disadvantageous to the magnetic nanofluids' stability. Obviously, the optimum preparation temperature should be 60°C, considering the positive contribution of particle size to magnetization and the negative contribution to the magnetic nanofluids' stability.

FIGURE 6

FIGURE 6. Average sizes of the Fe₃O₄ nanoparticles dependence of the magnetization, density and the stability of the magnetic nanofluids. The subscripts AC and BC represent the samples before and after centrifuging, respectively.

Conclusion

In this study, Fe₃O₄ nanoparticles dispersed into the magnetic nanofluids were prepared. Fe₃O₄ nanoparticles were synthesized by regulating the reaction temperature, and their structural and morphological characteristics were analyzed. It is observed that the saturation magnetization of the nanoparticles first decreased and then increased with rising reaction temperature due to the appearance of impurity and the increase of nanoparticle size. Furthermore, the stability of the prepared magnetic nanofluids decreases when its saturation magnetization increases with the increasing size of the nanoparticles. The magnetic nanofluids with superior stability and magnetization could be obtained with Fe₃O₄ nanoparticles of 25 nm and when the reaction temperature is 60°C.

Data Availability Statement

The original contributions presented in the study are included in the article/Supplementary Material, further inquiries can be directed to the corresponding author.

Author Contributions

Conceptualization, FC; investigation, NI; supervision, XL, and ZL, and HF; project administration, SY. All authors have read and agreed to the published version of the manuscript.

Funding

This research was financially supported by National Natural Science Foundation of China (No. 52079118) and Key Research and Development Plan of Sichuan province (No. 2020YFH0135).

Conflict of Interest

The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.

Publisher’s Note

All claims expressed in this article are solely those of the authors and do not necessarily represent those of their affiliated organizations, or those of the publisher, the editors and the reviewers. Any product that may be evaluated in this article, or claim that may be made by its manufacturer, is not guaranteed or endorsed by the publisher.

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