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Synthesis and magnetic properties of cobalt ferrite nanoparticles formed under hydro and solvothermal conditions
B. V. Vasil'ev1'2, R. Yu. Smyslov1, D. A. Kirilenko3'4, A. N. Bugrov1'2 institute of Macromolecular Compounds RAS, Bolshoy pr. 31, 199004 Saint Petersburg, Russia 2 Saint Petersburg Electrotechnical University "LETI", ul. Professora Popova 5,
197376 Saint Petersburg, Russia 3Ioffe Institute RAS, Politekhnicheskaya ul. 26, 194021 Saint Petersburg, Russia 4ITMO University, Kronverskii avenue 49, 197101 Saint Petersburg, Russia [email protected], [email protected], [email protected], [email protected]
PACS 75.20.-g; 75.75.+a DOI 10.17586/2220-8054-2021-12-4-492-504
Cobalt ferrite nanoparticles were synthesized both in hydro and in solvothermal conditions from Co and Fe salts of different chemical nature (nitrates and chlorides) taken in a 1:2 cation ratio. Varying the chemical prehistory, synthesis temperature, isothermal holding time, and the reaction medium composition made it possible to obtain a set of CoxFe3-xO4 nanoparticles of different average diameters and isomorphic substitution degree x. The resulting nanoparticles' elemental composition, crystal structure, sizes, and magnetic properties were determined using EDX analysis, X-ray diffraction, transmission electron microscopy, and SQUID magnetometry. The temperature dependences of the coercivity, remanent magnetization, squareness on both the average diameter and the stoichiometry of nanoparticles are considered. CoxFe3-xO4 nanocrystals ranged from 11 to 29 nm were single magnetic domains and showed ferrimagnetic behavior at room temperature. The hardest magnetic nanoparticles with maximum squareness values in the high-temperature region were formed with x = 0.79 using solvothermal treatment of cobalt and iron nitrates at 250 °C, 7 MPa for 10 hours.
Keywords: single-domain cobalt ferrite, ferrimagnetic nanocrystals, size-controlled synthesis, stoichiometry, Rietveld refinement, coercive field, saturation magnetization, squareness. Received: 19 October 2020 Revised: 9 August 2021
1. Introduction
Cobalt ferrite is well known as a hard magnetic material with a high coercive force (11.9 kOe) [1], moderate saturation magnetization (85 emu/g) [2], strong magnetocrystalline anisotropy (2.7 x 106 J/m), and high Curie temperature (520 °C) [3], which are combined with its increased mechanical hardness and chemical stability. This opens up opportunities for the potential use of CoFe2O4 in high-frequency applications [4], microwave devices [5], high-density magnetic storage materials [6], ferrofluids [7], as well as functional systems for hyperthermia [8], targeted drug delivery, and MRI diagnostics [9].
CoFe2O4 belongs to the single-phase structure of a cubic reverse spinel with the Fd-3m space group, where one half of Fe3+ ions occupies tetrahedral vacancies (A-position), and the other populates octahedral interstices (B-position) along with Co2+ [10,11]. In the case of cobalt ferrite nanoparticles, there is also a mixed spinel structure with the (Co2+ Fe1-z)A[Fe^ Co1+z]BO4 formula, where z is the inversion degree of the corresponding metal ions [3,12]. A change in x values of CoxFe3-xO4 particles strongly affects their magnetic properties since properties largely depend on the superexchange interaction between the tetrahedral and octahedral sublattices [3,10,13,14]. So, for dispersions of cobalt ferrite nanoparticles obtained by the pH-controlled coprecipitation method, the coercive force (Hc) did not change monotonically depending on the stoichiometry. At first, Hc decreased up to the substitution degree of 0.2, then increased in the range x = 0.2 - 0.6, after which it again decreased at a higher concentration of Co2+ (x = 0.8). The saturation magnetization (Ms), on the contrary, increased to x = 0.2 and, having reached its maximum value of 61.78 emu/g, decreased with a further increase in the concentration of divalent cobalt in the spinel structure [3]. The coprecipitation method presented in another work [13] made it possible to obtain cobalt ferrite nanoparticles for which an increase in x from 0 to 1 promoted growth in Hc from 7.75 to 340.5 Oe and a decrease in Ms from 59.1 to 32.7 emu/g at room temperature. For CoxFe3-xO4 particles synthesized by thermal decomposition of precursors, starting with an substitution degree of 0.1 and ending with 0.7, the authors of [14] recorded an increase in the coercivity from 120 to 610 Oe, after which it began to decrease down to 325 Oe at x = 1.5. In turn, the Ms of these nanoparticles decreased as their composition approached stoichiometric since Co2+ has a lower magnetic moment than Fe3+. In [10], during the formation of cobalt ferrite nanocrystals under hydrothermal conditions, a
similar tendency was observed in the variation of Ms and Hc, but the maximum value for the latter was reached at x = 0.75 and was 810 Oe. Thus, the substitution degree of Fe3+ by Co2+ in octahedral positions and the conditions of formation of cobalt ferrite nanoparticles affect their final magnetic characteristics.
In addition, to precise control of the composition and structure of CoFe2O4, practical applications require the ability to regulate particle size at the nanoscale. It is known that fine tuning the size of cobalt ferrite nanocrystals in the single magnetic domain region can achieve extremely high values of the coercive force at room temperature [1,15]. With an increase in the particle diameter, both the saturation magnetization and the coercive force rapidly accrue, but upon transition to the multidomain state, Ms reaches a plateau with a characteristic value of bulk CoFe2O4, and Hc passes through a maximum. Depending on the synthesis conditions, the critical size (Dcr ) of CoFe2O4 nanoparticles corresponding to the boundary of the single-domain region varies from 5 to 40 nm [14,16-22]. For cobalt ferrite nanoparticles synthesized by the forced hydrolysis in polyol, Dcr was about 5 nm with a maximum coercivity of 14.5 kOe (5 K) and a saturation magnetization of 85 emu/g (5 K) [16]. The micellar microemulsion method [17] made it possible to obtain the maximum value of Hc (16 kOe) and provided a plateau for Ms (70 emu/g) at a particle size of 10 nm. In the case of approaches associated with thermal decomposition of precursors [14] and high temperature non-hydrolysis process combined with seed-mediated growth [18], the critical size was 12 nm with magnetic characteristics of 22.8 kOe, 69 emu/g (2 K), and 18 kOe, 82 emu/g (5 K), respectively. Larger Dcr were recorded for CoFe2O4 nanoparticles obtained by coprecipitation of cobalt and iron salts in the presence of oleic acid (28 nm) [19], hydrothermal synthesis with annealing (40 nm) [20], and the polymeric method via a thermal decomposition process (40 nm) [21]. A special place among the above methods is occupied by hydro(solvo)thermal synthesis due to relatively mild temperature conditions, the possibility of effective control of the composition, size, and morphology of the resulting nanoparticles, as well as due to the high purity and homogeneity degree of the resulting products [23-26].
Therefore, the main task of this work was to determine the effect of the nature of precursors, the composition of the reaction medium, the temperature and time of isothermal holding on the size, structure, and magnetic properties of cobalt ferrite nanoparticles formed under hydro(solvo)thermal conditions.
2. Experimental part
2.1. Synthesis of cobalt ferrite nanoparticles under hydrothermal conditions
CoxFe3-xO4 nanoparticles were obtained by coprecipitation of cobalt and iron hydroxides from aqueous solutions of their chlorides or nitrates, followed by dehydration under hydrothermal conditions. Based on the analysis of published data, the following procedure for synthesizing cobalt ferrite nanoparticles was developed.
Prepared solutions of Co(NO3 V6H2O (analytically pure, GOST 4328-77, Vecton, Russia) andFe(NO3);r 9H2O (chemically pure, CAS 10294-41-4, Vekton, Russia) or CoCh 6H2O (analytically pure, GOST 4328-77, Vecton, Russia) and FeCl39H2O (chemically pure, CAS 10294-41-4, Vekton, Russia) were mixed for 2 hours. Then an aqueous solution of ammonia (NH4OH) was added dropwise in an amount of 10 ml. The precipitate had formed at pH=10, it was repeatedly washed with distilled water until a negative reaction for chloride or nitrate ions and dried at 65 °C to constant weight. After cooling to room temperature, the resulting powder was crushed and transferred in an amount of 0.5 g to an autoclave with a teflon cell. 14.5 ml of distilled water was added to a weighed portion of a mixture of cobalt and iron hydroxides, and hydrothermal treatment was carried out. The holding time of the reaction mixture in the autoclave was 10 hours at a temperature of 200 °C and pressure of 7 MPa. Further, for nanoparticles of cobalt ferrite obtained from chlorides and nitrates under hydrothermal conditions, the abbreviations HC200 and HN200 will be used, respectively.
2.2. Synthesis of cobalt ferrite nanoparticles under solvothermal conditions
Co(NO3)2-6H2O and Fe(NO3)3-9H2O were each dissolved separately in 15 ml of ethylene glycol (C2H6O2) and, after complete dissolution, were mixed. Then, 3.8 ml of ammonia in the form of a 25% aqueous solution as a precipitant (pH=10) were added and mechanically stirred for 1 hour. The resulting mixture was placed in an autoclave and kept for 5 hours at 250 °C or 10 hours at 100 - 250 °C, where the step was taken equal to 50 °C. The pressure in the reaction vessel during the synthesis was 7 MPa. After cooling to room temperature, the resulting black powder was centrifuged for 10 minutes at 8000 rpm. The precipitate of nanoparticles washed with alcohol was dried in air at 45 °C. Subsequently, for brevity, these samples will be designated as SN100, SN150, SN200, SN2505, and SN25010, where the number in the title block indicates the temperature, and the superscript indicates the synthesis time.
Using CoCl2 6H2O and FeCl3 9H2O to form cobalt ferrite nanoparticles under solvothermal conditions, the synthesis procedure was identical to that described above, and the name of the sample was taken as SC250.
B. V Vasil'ev, R. Yu. Smyslov, D.A. Kirilenko, A.N. Bugrov Table 1. Parameters of the CoFe2O4 phase with a cubic cell a = 7 = fi = 90°
Sample Unit cell parameters Crystalline domain
a = b = c, A D, nm
HC200 8.3809 ± 0.0008 13.9 ± 0.5
HN200 8.3832 ± 0.0009 11.9 ± 0.5
SC250 8.3965 ± 0.0005 28.7 ± 0.5
SN25010 8.3992 ± 0.0008 24.8 ± 0.5
SN2505 8.3974 ± 0.0008 15.5 ± 0.5
SN200 8.4015 ± 0.0006 16.7 ± 0.5
SN150 8.4176 ± 0.0012 12.2 ± 0.5
SN100 - -
2.3. Instruments and characterization
The size and shape of the cobalt ferrite nanoparticles obtained in this study were determined using a Jeol JEM-2100F transmission electron microscope at an accelerating voltage of 200 kV. Aqueous dispersions of CoFe2O4 nanopowders were deposited onto copper grids covered with graphene paper to obtain bright-field images.
X-ray diffraction (XRD) patterns of CoFe2O4 nanoparticles were obtained using a Rigaku SmartLab diffractome-ter with CoKa radiation. The survey was carried out in the 26 range of angles from 5 to 90° with a scanning speed of 0.5°/min. The structure analysis of the obtained XRD patterns was carried out in the MAUD program [27] using the Rietveld method.
Energy dispersive X-ray (EDX) analysis was carried out to investigate the elemental composition of the obtained cobalt ferrite nanoparticles. EDX analysis was carried out on a TESCAN VEGA 3 SBH scanning electron microscope (TESCAN BRNO, Czech Republic) with an Advanced Aztec Energy energy-dispersive attachment for elemental mi-croanalysis based on an X-act semiconductor energy dispersive detector (Oxford Instruments NanoAnalysis, Great Britain).
The study of the magnetic properties of the synthesized cobalt ferrite nanoparticles was carried out on a superconducting quantum interferometer (SQUID) MPMS SQUID VSM (Quantum Design) with a magnetic field up to 7 T.
3. Results and discussion
Qualitative X-ray phase analysis of nanoparticles obtained from salts (nitrates, chlorides) of cobalt and iron under hydro- and solvothermal conditions was carried out using the PDWin 4.0 software package (Burevestnik, Russia). Its results showed that HC200, HN200, SN150, SN200, SN2505, SN25010 and SC250 samples correspond to the crystal structure of CoFe2O4 (PDF card No. 3-864). No supplementary impurity phases were found during the analysis, except for the SN100 and SN150 nanoparticles. In their XRD patterns, in addition to the amorphous halo and peaks of partially crystallized cobalt ferrite in the 26 region of 8°, a reflection corresponding to the double layered hydroxide (Co-Fe LDH) [28] was observed. This phase, passed into CoFe2O4 when the synthesis temperature increased to 200 °C and higher (Fig. 1a,b,c). Analysis of powder XRD data (Fig. 1) using the Rietveld method made it possible to track the simultaneous changes in crystallite sizes and unit cell parameters (Table 1). For nanoparticles formed from cobalt and iron nitrates under solvothermal conditions, the crystallite size grew with an increase in the synthesis temperature, while the volume of a cubic unit cell, on the contrary, decreased. A longer isothermal holding of the reaction mixture also promoted an increase in the size of the CoxFe3-xO4 crystallites, but at the same time, had little effect on the unit cell parameters. The use of CoCl2 6H2O and FeCl3 9H2O as precursors for the synthesis of nanoparticles led to the compaction of the cubic unit cell and the formation of larger coherent scattering regions in comparison with the samples obtained from the corresponding nitrates (Table 1).
The same tendencies persist for cobalt ferrite nanoparticles obtained by hydrothermal synthesis (Fig. 1e,f). However, it should be noted that the average size of crystallites formed in an aqueous medium at elevated pressure and temperature is noticeably lower than that of their analogs obtained in ethylene glycol (Fig. 1c,e). The same can be said about the volume of the unit cell (Table 1).
The value of microstresses for the synthesized CoxFe3-xO4 nanoparticles, regardless of their chemical prehistory and preparation method, was 0.0025 ± 0.0001 (0.25 ± 0.01%).
FIG. 1. XRD patterns of SN100 (a), SN150 (b), SN 200 (c), SN2505 (d), HN200 (e), HC200 (f) nanoparticles
The morphology of CoxFe3-xO4 nanoparticles synthesized by the hydro- and solvothermal method from various precursors is shown in TEM micrographs (Fig. 2a). Cobalt ferrite nanoparticles are mostly quasi-spherical, although a small number of large crystals in the form of plates and octahedra are observed. In Fig. 2b, the diameter data of quasi-spherical nanoparticles as histograms are statistically treated using a lognormal distribution. Data processing was performed in the program OriginPro 2021b (built 9.8.5.201). The lognormal distribution usually describes the size of the synthesized nanoparticles well. In our case, it is better than the normal one. Besides, the obtained data are shown as Half Violin with data points in the left size (Fig. 2c). The size distribution of nanoparticles turned out to be relatively wide and asymmetric for all the selected synthesis conditions (Fig. 2b,c). It should be noted that the maxima in the size histograms corresponding to the average diameter of nanoparticles, within the limits of the method errors, are comparable to the crystallite sizes determined from the XRD data (Fig. 2b,c, Table 1). Thus, this confirms the earlier conclusion that the formation of smaller CoxFe3-xO4 nanoparticles is facilitated by the hydrolysis of nitrates of the corresponding metals, followed by the dehydration of oxyhydroxides under hydrothermal conditions.
Elemental analysis showed that the content of cobalt in the products of solvothermal synthesis carried out at 100 °C did not exceed 0.5% and, therefore, no CoxFe3-xO4 phases were formed (Table 2). This was also confirmed by the XRD data (Fig. 1a). In the case of an increase in the synthesis temperature to 150 °C, a mixed spinel with a stoichiometric coefficient x = 0.535 was formed. Higher temperatures of isothermal holding of cobalt and iron salts under both hydro and solvothermal conditions increased the degree of substituting Fe3+ ions in octahedral positions by Co2+ but the stoichiometric composition was still not achieved (Table 2).
Table 2. Elemental analysis of nanoparticles
Sample Ratio at.% Stoichiometric ratio1
k = [Co]/[Fe] Co Fe O x 1 — x
HC200 0.401 12.18 30.4 57.42 0.858 0.142
HN200 0.396 8.97 22.66 68.37 0.851 0.149
SC250 0.384 10.3 26.8 62.9 0.833 0.167
SN25010 0.357 8.31 23.26 68.43 0.790 0.210
SN2505 0.307 9.79 31.92 58.29 0.704 0.296
SN200 0.353 9.25 26.23 64.52 0.782 0.218
SN150 0.217 4.24 19.54 76.22 0.535 0.465
SN100 0.026 0.5 19.24 80.26 0.076 0.924
xThe formula for calculating the stoichiometric coefficient:
x 3k [Col
k = --^ x = —■— ; k = —— ; CoœFe3_xO4 ^ (CoFe2O4)x(Fe3O4)i_
3 — x 1 + k |FeJ
x
Studies of the synthesized cobalt ferrite nanoparticles using SQUID magnetometry showed that their magnetization curves have hysteresis loops regardless of the type of precursor used, as well as the chosen conditions of hydrolysis and dehydration (Fig. 3, Table 3). The only exception was SN2505 for which almost superparamagnetic behavior (low coercive force and zero remanent magnetization) was observed at room temperature (Table 3). This may be due to the short synthesis time during which the magnetic domains do not yet have time to form and the magnetic properties of nanoparticles are practically absent [29] (Fig. 3b). It should also be noted that "constricted" hysteresis loops were recorded for cobalt ferrite nanoparticles obtained under hydrothermal conditions or in an organic solvent at temperatures of 150 and 200 °C (Fig. 3a,c), which are typical for a mixture of soft and hard magnetic materials [1,30]. In this cases, such a "necking" in the central part of the M-H loop can be explained by a small amount of superparamagnetic single-domain particles in ferrimagnetic CoxFe3-xO4 nanocrystals.
The coercive force (Hc), saturation magnetization (Ms), remanent magnetization (Mr) were determined from the M-H curves at 400, 300, and 5 K for the resulting nanoparticles (Fig. 3, Table 3). The values of Hc and Ms as a function of the average nanoparticle diameter (D) are shown in Fig. 4a,b for a series of crystallites obtained under solvothermal conditions (S) from cobalt and iron nitrates at different temperatures. It was found that the coercive force grew with an increase in the size of the formed CoxFe3-xO4 crystallites. It is known from the literature that, for spherical cobalt ferrite nanoparticles, Hc grows with an increase in their diameter to a specific critical single-domain size, after which the coercivity begins to decrease against the background of further enlargement of crystallites [31]. The maximum Hc is associated with the transition from a magnetic single-domain regime to a multidomain one: from the coherent
Fig. 2. TEM micrographs (a), histograms of size distribution (b) and Half Violin with data points (c) for SN25010 (1), SC250 (2), HN200 (3) and HC200 (4) nanoparticles
Fig. 3. The low-temperature magnetic hysteresis (M-H) loops for CoxFe3-xO4 nanoparticles synthesized under solvo-(a,b) and hydrothermal conditions (c)
16 18 20 22 24
D, nm a
100
I-1-1-1-1-1-1-1-1
16 18 20 22 24
D, nm
b
Fig. 4. Particle size dependences of (a) coercivity, (b) saturation magnetization for SN150, SN200, and SN250 samples of CoxFe3-xO4 nanoparticles measured at 5, 300, 400 K
to incoherent rotation of spins (twisting rotation and motion of domain walls) [21]. Since we record an increase in the coercivity in the size range from 10 to 24 nm and do not reach the maximum, we assume that all nanoparticles obtained in the S series are single-domain. The saturation magnetization plotted as a function of size at 400, 300, and 5 K shows its initial increase with growing D, but above a specific size, it tends to be a kind of plateau with values comparable to those of bulk CoFe2O4 (Fig. 4b) [16]. The increase in Ms with diameter for single-domain particles can be understood by considering the core-shell model [16,31,32]. An oriented magnetic domain is considered as a core, and disordered spins on the surface due to imperfect coordination of surface atoms create a shell, the so-called surface "dead magnetic layer" [21]. As the particle size increases, the ratio of the shell thickness to the volume of the domain (core) decreases, which leads to an increase in Ms. When particles approach the multidomain state, the growth of the magnetization values stops.
Low remanent magnetization and almost zero squareness at room temperature for SN150 and SN200 nanoparticles may mean their superparamagnetic behavior is replaced by ferrimagnetic behavior with an increase in the synthesis temperature to 250 °C. According to the Stoner-Wohlfarth model, the fixed Mr/Ms values for synthesized singledomain particles are within the range of values characteristic of non-interacting three-dimensional random particles
Fig. 5. Dependence of the magnetization hysteresis loop squareness on the stoichiometry of the elemental composition and nanoparticle size at 5 (a) and 300 K (b)
with uniaxial anisotropy [26]. Only samples SN250 and SC250 are knocked out of the available row. The Mr and Mr/Ms values measured at 5 K turned out to be larger than the values estimated at 300 and 400 K. For this, a possible reason may be associated with the increased ratio of magnetic anisotropy to thermal energy at low temperatures [21].
Figure 5 shows surfaces of the squareness (Q) dependence of the hysteresis loops for the magnetization of synthesized cobalt ferrite nanoparticles (Table 3) on their stoichiometry and size:
Q = M = f (X'D>'
where Mr is the remanent magnetization, Ms is the saturation magnetization, x is the stoichiometric coefficient of the composition of CoxFe(3-x)O4 nanoparticles (Table 2), D is the size of CoxFe(3-x)O4 nanoparticles obtained from TEM data.
Part of Fig. 5, corresponding to the coordinate plane (x, D), shows the projection of the two-dimensional surface of the quantity Q in the form of a color map. It was determined that the maximum squareness of 0.82 at 5 K of the hysteresis loop is at a composition stoichiometry x of about 0.77 - 0.80 and a particle diameter in the range of 16 -25 nm. At 300 K, the maximum Q value of about 0.33 is observed at the same x and a nanoparticle size of 25 nm.
The analysis of the magnetic properties of CoxFe3-xO4 nanoparticles obtained under hydro or solvothermal conditions, depending on the nature of the anion of the salt used, concludes that there is no noticeable difference between them at low temperatures. At 300 K and higher, for nanoparticles obtained from Co and Fe nitrates, the values of Hc, Mr are higher than those for their analogs SC250 and HC200.
The magnetic parameters strongly depend on the distribution of cations (Co2+, Fe2+, Fe3+) between the tetra-hedral and octahedral positions. Fe3+ and Co2+ ions can occupy tetrahedral vacancies (A-positions) or octahedral
Fig. 6. Dependence of the coercive force on the stoichiometry of the elemental composition and size of cobalt ferrite nanoparticles at 5 (a) and 300 K (b)
Table 3. Magnetic characteristics of CoxFe3-thermal prehistory
O4 nanoparticles depending on their chemical and
Temperature
Sample 5 K 300 K 400 K
Q1} Mr, Ms, Hc, Q Mr, Ms, Hc , Q Mr, Ms , Hc ,
emu/g emu/g Oe emu/g emu/g Oe emu/g emu/g Oe
HC200 0.75 60.2 80.8 13935 0.16 11 68.2 385 0.04 2.2 58.6 46
HN200 0.77 66.7 87.2 13657 0.19 13.8 72.7 499 0.06 3.6 61.4 86
SC250 0.73 69.5 95 13210 0.21 16.8 79.9 504 0.04 3.1 70.4 56
SN25010 0.82 67.1 82.3 12783 0.33 23.9 71.6 1007 0.21 12.9 62.7 421
SN2505 - 0.07 0.09 15635 - 0.01 0.08 276 - - 0.06 -
SN200 0.81 75.7 93.7 7583 0.05 4 74.1 47 0.07 4.5 62.8 33
SN150 0.69 49.1 70.8 4856 0.08 4.1 51.8 35 0.08 3.3 42.3 36
squareness of magnetization hysteresis loops for CoxFe3_xO4 nanoparticles: Q = Mr
Ms
interstices (B-positions) in a cation-substituted spinel (Co2+ Fe^)A[Fe3+z Co2+z]BO4, where z is the extrinsic site inversion [3,33]. The change of the magnetization in the ferrimagnetic spinel can be explained by the antiparallel interaction between the moments of the cations in the A and B positions. The magnetic moment of the Co2+ ion (3 ^B) is less than that of the Fe2+ (4 ^B) and Fe3+ (5 ^B) ions. At low degrees of inversion, Co2+ ions prefer to substitute for Fe3+ ions in the A-sites, which decreases the magnetic moment of the tetragonal regions and increases the total magnetic moment. The exchange interaction A-O-B remains stronger than A-O-A and B-O-B. However, the exchange interactions A-O-B weaken with an increase in the degree of substitution of Fe3+ ions on Co2+ in the A-sites. Because of the latter, the magnetic moments of the tetrahedral and octahedral positions align antiparallel to each other.
The increase in the coercive force seen in Fig. 6a is associated at 5 K with an increase in the stoichiometric ratio. The Hc extremum of 13 - 15 kOe is observed at x in the range of 0.82 - 0.85, while the particle diameter varies over a wide range of 12 - 28 nm. However, at 300 K, an Hc maximum is equal to ca. 1 kOe, observed at 0.79 for nanoparticles with a diameter of 25 nm (Fig. 6b), which agrees with the literature data [10,14].
4. Conclusions
The synthesis of cobalt ferrite, an essential step towards creating new efficient ferrimagnetic nanoparticles, requires control over many physicochemical parameters. When synthesizing cobalt ferrite nanoparticles by the solvo(hydro)thermal method, varying the temperature, nature of the solvent, and counterions for cobalt(II) and iron(III) makes it possible to create CoxFe3-xO4 nanoparticles with different stoichiometric ratios. Analysis of the data obtained allowed us to conclude that changes in the conditions for the synthesis of particles from Fe3+ and Co2+ lead to significant changes in the nanoparticles' properties. These properties include the contribution of the superparamagnetic fraction, the degree of spinel inversion, the average size of nanoparticles, coercivity, and saturation magnetization. The results obtained can be used to develop scientific recommendations for developing state-of-the-art materials for medical applications and in engineering. Further research is needed to understand the relationship between the solvo(hydro)thermal synthesis conditions, the structure of the nanoparticles formed, and their functional (magnetic) properties.
Acknowledgement
X-ray diffraction experiments were performed on the Engineering Center equipment of the St. Petersburg State Technological Institute (Technical University). TEM studies were carried out in the Federal Joint Research Center "Material science and characterization in advanced technology" funded by the Ministry of Education and Science of the Russian Federation.
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