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. 2022 Oct 4;14(41):46738–46747. doi: 10.1021/acsami.2c13088

Terahertz Faraday Rotation of SrFe12O19 Hexaferrites Enhanced by Nb Doping

Zimeng Hu †, Gavin B G Stenning ‡, Vladimir Koval §, Jiyue Wu †, Bin Yang ∥,*, Alisa Leavesley ⊥,#, Richard Wylde #, Michael John Reece †, Chenglong Jia ∇,*, Haixue Yan †,*
PMCID: PMC9585520  PMID: 36194853

Abstract

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The magneto-optical and dielectric behavior of M-type hexaferrites as permanent magnets in the THz band is essential for potential applications like microwave absorbers and antennas, while are rarely reported in recent years. In this work, single-phase SrFe12–xNbxO19 hexaferrite ceramics were prepared by the conventional solid-state sintering method. Temperature dependence of dielectric parameters was investigated here to determine the relationship between dielectric response and magnetic phase transition. The saturated magnetization increases by nearly 12%, while the coercive field decreases by 30% in the x = 0.03 composition compared to that of the x = 0.00 sample. Besides, the Nb substitution improves the magneto-optical behavior in the THz band by comparing the Faraday rotation parameter from 0.75 (x = 0.00) to 1.30 (x = 0.03). The changes in the magnetic properties are explained by a composition-driven increase of the net magnetic moment and enhanced ferromagnetic exchange coupling. The substitution of the donor dopant Nb on the Fe site is a feasible way to obtain multifunctional M-type hexaferrites as preferred candidates for permanent magnets, sensors, and other electronic devices.

Keywords: SrFe12O19 hexaferrite, THz, Faraday rotation, ferrimagnetic, dielectric

Introduction

Magnetic materials like hexaferrites1,2 and spinel ferrites3,4 have been investigated for decades due to their advanced electronic and magnetic performances and potential applications. M-type hexaferrites having the general formula MeFe12O19 (Me is a divalent ion like Ca, Sr, Ba, Pb, etc.) are widely studied for sensing and imaging applications as well as for advanced multi-state memory devices, transducers, and RF/MW filters.5,6 Their unique magnetic, dielectric, and multiferroic properties originate from their large magneto-crystalline anisotropy along the c-axis and collective displacement of iron ions in the FeO5 bipyramidal units. The crystal structure of M-type hexaferrites is hexagonal with the space group P63/mmc. The P63/mmc unit cell consists of RSR*S* layers, where S = Fe6O82+ is the spinel block and R = MeFe6O112– is the hexagonal block. The R*S* layers are RS layers rotated around the c-axis by 180°. Fe3+ ions occupy five different sites showing opposite spin rotations: at the 12k, 2b, and 2a octahedral sites, the spins have the up ↑ direction, and at the 4f1 and 4f2 sites, the spins are aligned in the down ↓ direction.7 As a consequence, the M-type hexaferrites show ferrimagnetic behavior at room temperature.

Among the M-type hexaferrites, SrFe12O19 has become one of the most studied hard ferrites due to its high coercive field (Hc = 5.55 kOe),8 high Curie temperature (Tc = 460 °C),9 large saturation magnetization (Ms = 0.056 emu/mg), and large remnant magnetization (Mr = 0.016 emu/mg).2,9 SrFe12O19 can be prepared at a low cost, which makes it an attractive material for commercial use. However, achieving larger saturated magnetization and, at the same time, appealing dielectric behavior remains a big challenge in designing and preparing high-performance hexaferrites derived from SrFe12O19.

The most promising approach to synthesize SrFe12O19-based hexaferrites and tailor their functional properties for desired applications is a partial substitution of Sr2+ ions by isovalent Ba2+, Pb2+, and Ca2+ ions10−13 or trivalent rare earth elements14 like La3+, Nd3+, and Sm3+. Doping at Sr sites by the La3+ ion with smaller radii has been reported to decrease both saturated and remnant magnetization of SrFe12O19.14,15 It was shown that the La3+ substitution makes the valence variation from Fe3+ to Fe2+ and the noncollinear spin arrangement of magnetic moments, which results in this decrement of magnetization.14 In addition, substitution with rare earth elements can significantly increase the grain size of SrFe12O19-based ceramics, further enlarging the magnetic coercive field.14

Another strategy to improve the functional properties of the M-type hexaferrites is a partial substitution of the Fe ions by dopants: (i) isovalent ions such as Sc3+,16 Ga3+,17 Al3+,18,19 and In3+;20 (ii) Co2+ ions21,22 or Nb3+;23 and (iii) ionic combinations like Cr3+–Zn2+,24 Co4+–Ca2+,21 or Zr4+–Cd2+.7 For example, the coexistence of electrical and magnetic ordering at room temperature was observed in modified SrFe12–xInxO19 magnetoelectric multiferroic ceramics.25,26 The cointroduction of Co4+ and Ca2+ ions on Fe sites in BaFe12O19 can increase the dielectric permittivity if compared to the undoped one due to a higher concentration of Fe3+ ions in the high spin state.21 The reduced grain size, increased saturated magnetization, and large magneto-crystalline anisotropy were obtained in the Nb-substituted BaFe12O19.23 In addition, the introduction of Nb3+ ions can help decrease both the alternating current (AC) conductivity and direct current (DC) conductivity of the M-type hexaferrites, which suggests the potential function of Nb for improving the dielectric behavior.27 Asghar and Anis-ur-Rehman have proposed, based on the Maxwell–Wagner two-layer theory, that the highly resistive grain boundaries are responsible for the reduced conductivity of hexaferrites in the dielectric measurements.24,28 The above-mentioned AC studies, however, were carried out on M-type hexaferrites within a narrow frequency range. To date, there have been only a few reports on the dielectric behavior of M-type hexaferrites at terahertz (THz) frequencies29,30 and much less study on the Faraday rotation,31 knowledge of which is crucial for the construction of optical communication devices. Moreover, a comprehensive study on the dielectric properties of hexaferrites over a wide frequency and temperature range is missing. Also, for future perspectives, it is also necessary to search for new hexaferrites with tunable dielectric, magnetic, and even magnetodielectric properties.

As the Nb5+ ion can electrically compensate for the presence of the Fe2+ ions and simultaneously inhibit the abnormal grain growth in polycrystalline SrFe12O19, a study on the dielectric and magnetic properties of the SrFe12O19 ceramics (with and without Nb doping) was undertaken to explore the relationship between the composition, structure, and functional properties of these hard ferrites. Here, two compositions of SrFe12–xNbxO19 (x = 0.00 and 0.03) were designed. Additionally, for the first time, a modified technique of THz spectroscopy is introduced to study the Faraday rotation effect in hexaferrites. Finally, using this technique, we demonstrate that the Nb-doped SrFe12O19 ceramics possess a large relative permittivity and Faraday rotation at THz frequencies, suggesting that the Nb-modified M-type hexaferrites are useful in optical communication devices, security surveillance systems, and sensing applications.

Materials and Methods

Materials

Hexaferrite ceramics can be prepared by the solid-state sintering method,22 sol–gel method, and green pulsed laser ablation in liquid (PLAL) approaches.32,33 Here, SrFe12–xNbxO19 ceramics, with x = 0.00 and 0.03 (abbreviated as SFO and SFN3O), were prepared by the conventional solid-state method using raw materials of SrCO3 (purity ≥ 99.9%, Aldrich), Nb2O5 (purity ≥ 99.9%, Alfa Aesar), and Fe2O3 (purity ≥ 99.945%, Alfa Aesar). The chemicals were preheated at 200 °C for 24 h and then weighed according to the stoichiometric formula. They were ball milled in ethanol for 12 h at 250 rpm using stainless balls and vessels. The slurry was dried, and the powder product was calcined at 1100 °C for 6 h. To reduce the particle size, the calcined powder was ball milled again. The fine precursor was mixed with 5 wt % PVA and then pressed into pellets with a diameter of 13 mm and thickness of 1–2 mm. The pellets were heated at 800 °C for 2 h in air to remove the binder. Sintering was carried out at 1200 °C for 6 h in air. The sintered pellets were polished and then annealed in air for 12 h at 1000 °C.

Methods

The crystal structure of the sintered ceramics was investigated by X-ray powder diffraction (XRD, PANalytical, Cubix) on crushed powders using Ni-filtered Cu Kα radiation (λ = 1.5418 Å) over the 2θ range of 5–120° with a step of 0.0315°. Structural analysis was performed using Rietveld refinement using the EXPGUI and GSAS software packages.34,35 The surface morphology of the polished and thermally etched samples was observed by scanning electron microscopy (SEM). Surface element analysis was performed with an X-ray photoelectron spectrometer (XPS, Nexsa). Thermal analysis was carried out by differential scanning calorimetry (DSC, rheometric scientific, a model STA 1500 H) in N2 from 25 to 800 °C with a heating/cooling rate of 10 °C/min. For dielectric measurements, the as-sintered samples were ground to less than 0.5 mm thickness and then coated with silver paint (Gwent Electronic Materials Ltd., C2011004D5, Pontypool, U.K.). The temperature dependence of the relative dielectric permittivity (ε′) and loss tangent (tan δ) were measured in the temperature range 25–600 °C at three different frequencies (100 kHz, 500 kHz, and 1 MHz) via a computer-controlled system with an LCR meter (Agilent, 4284A) attached to a furnace. The field-dependent magnetization (M–H) loops of the samples at room temperature and the zero-field cooling (ZFC) and field cooling (FC) magnetizations were measured over the temperature range 1.8–400 K at 1000 Oe using a superconducting quantum interference device (SQUID, Quantum Design). The dielectric properties and Faraday rotation in the THz region were measured by modified terahertz time-domain spectroscopy (THz-TDS, TeTechs Ltd., Canada) in transmission mode. Electromagnetic radiation ranging from 0.2 to 0.8 THz was used to illuminate tiny wafers with a thickness of 1 mm and a diameter of 12 mm. The collected THz time-domain spectra were Fourier transformed to obtain both amplitude and phase information in the frequency domain. All information in the frequency domain was used to extract the permittivity and loss tangent data of the samples.31,36 The permittivity and loss tangent in the THz band were converted from the refractive index of virgin samples. After magnetizing at a magnetic field of 3500 Oe, the samples were tested in the THz band with right-handed and left-handed gratings to study the Faraday rotation effect.

Results and Discussion

A schematic of the crystal structure of SrFe12O19 hexaferrite is illustrated in Figure 1a. Figure 1b shows the room-temperature XRD patterns of the SrFe12–xNbxO19 (x = 0.00 and 0.03) ceramics. Both SFO and SFN3O are single-phase materials with a hexagonal structure (space group: P63/mmc). The Miller indices are labeled based on the reference SrFe12O19 standard (ICSD no. 69022) and are in good agreement with Kimura’s work on the structural analysis of SrFe12O19.18 The Nb5+ ions can enter both the octahedral and tetrahedral sites based on previous work.23,37 Here, Nb5+ ions prefer occupying the spin-down 4f1 and 4f2 sites. The well-fitted XRD patterns within the selected range of 20–120° for SFO and SFN3O are shown in Figure S1a,b, respectively. The χ2 factor for good fitting does not exceed 2.7. The refinement and crystal parameters are listed in Table S1. In diffractograms, no secondary phase is observed within the detection limit of the X-ray diffractometer. Thus, the substitutional niobium ions are supposed to incorporate into the lattice. Because of the smaller ionic radius of Nb5+ (0.640 Å) compared to that of Fe3+ (0.645 Å),38 the volume of the unit cell decreases on doping from 692.887(2) to 692.262(3) (Å3), and thus the shifting of diffraction peaks toward higher angles is observed for SFN3O in Figure 1b (inset), indicated by blue short-dotted lines. The etched microstructures of the SFO and SFN3O ceramics are shown in Figure 1c,d. As can be seen, the grains are closely packed in both samples. This observation is consistent with the high relative density of the ceramics (>95%) measured using the Archimedes’ method. It should be noticed that the grain size decreases with Nb doping from 1.85 μm (SFO) to 1.43 μm (SFN3O), which is in accordance with SEM observations of other Nb-doped dielectric ceramics.39 It should be noted that decreasing grain size results in a smaller unit cell volume due to larger surface tension forces, as reported in other magnets.40,41

Figure 1.

Figure 1

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(a) Schematic of the crystal structure of pure SrFe12O19 hexaferrite. (b) XRD patterns of SrFe12–xNbxO19 (x = 0.00 and 0.03) ceramics within the selected 30–60° range; indexing was performed based on the reference standard SrFe12O19 (ICSD no. 69022). Inset: enlarged view of XRD patterns within 30–40°. (c, d) SEM images of the thermally etched ceramics with x = 0.00 and 0.03 ceramics, respectively.

The dielectric and magnetic properties of hexaferrites strongly depend on the content of Fe ions and oxygen vacancies.29 Therefore, information on the oxidation state of Fe, which is closely related to oxygen vacancies and changes due to processing at high temperatures, is of great importance. To explore the effect of the Nb substitution on the valence of Fe in the prepared hexaferrites, X-ray photoelectron spectroscopy was employed. The fitted O 1s XPS spectra of SFO and SFN3O are shown in Figure 2a,b. The spectra were fitted by the Avantage software using the Gaussian–Lorentzian product (GLP).42 The results of fittings are summarized in Table S2. Apparently, the experimental O 1s spectrum is formed by three spectral peaks–the red curve peak corresponds to the lattice oxygen (Olatt), the blue peak represents oxygen in a deficient environment (Ovac), and the green curve peak can be ascribed to chemisorbed or dissociated oxygen (Oabs) from the air.43,44 The ratio of integrated areas of Ovac:Olatt can be used to compare the change in the relative oxygen vacancy concentration between compositions.45 The binding energies of the Olatt, Ovac, and Oabs peaks in SFO are 529.40, 530.82, and 532.78 eV, respectively. In SFN3O, the respective peaks are shifted to 529.56, 530.86, and 532.99 eV. The reduced ratio Ovac:Olatt varies from 0.354(3) (SFO) to 0.222(1) (SFN3O), as calculated from the integral area of the corresponding peaks. Therefore, one can conclude that the concentration of oxygen vacancies decreases with Nb doping.46 The reduced oxygen vacancies are expected to improve the dielectric properties of the Nb-doped hexaferrites.29

Figure 2.

Figure 2

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(a, b) Fitted O 1s XPS spectra and (c, d) fitted Fe 2p XPS spectra for the SFO and SFN3O hexaferrites, respectively.

To further investigate the origin of oxygen vacancies, the valence of Fe ions was analyzed by fitting the Fe 2p spectra, as shown in Figure 2c,d. The fitted results are listed in Table S3. The Fe 2p spectrum is formed by a typical doublet of Fe 2p3/2 and Fe 2p1/2 with satellite peaks corresponding to different valences of Fe.29,47,48 Deconvolution of the characteristic Fe 2p3/2 photon emission peak in SFO yields a doublet with the Fe3+ 2p3/2 (∼710.88 eV) and Fe2+ 2p3/2 (∼709.18 eV) peaks, and in SFN3O, the doublet is composed of the Fe3+ 2p3/2 (∼711.08 eV) and Fe2+ 2p3/2 (∼709.38 eV) peaks (depicted by the purple and blue curves in Figure 2c,d). From the fitted spectra, a fraction of the Fe ions in the two chemical states was determined by the integrated area ratio. It was found that the area ratio of Fe2+ 2p3/2: Fe3+ 2p3/2 decreases from 1.076(8) in SFO to 0.592(3) in SFN3O, which indicates that the reduction of Fe3+ is suppressed by the Nb5+ doping. The increased oxidation degree of Fe ions reflected by XPS data is consistent with decreased oxygen deficiency discussed before, which also agrees well with the previous work.49 In addition, the decreased oxygen deficiencies agree well with the smaller unit cell volume for SFO.

A phase evolution analysis of the SFO and SFN3O hexaferrites was performed using the DSC thermograms, as recorded on heating and cooling (Figure S2). Three thermal events denoted as a, b, and c are observed on the DSC curves for both samples. The first event a occurring at around 100 °C (on heating) indicates volatilization of the absorbed water.50 The other two events b and c can be linked with magnetic phase transitions. For SFO, the thermal feature b is around 290 °C and c is around 465 °C; the latter agrees well with the reported ferromagnetic to paramagnetic phase transition temperature (Curie temperature, Tc) of pure SrFe12O19 hexaferrite, 470 °C.9,51 The underlying mechanism of the b event needs further investigation. Similar thermal events were observed for SFN3O; event b occurred at about 260 °C, and c occurred at around 490 °C.

To further study the phase transition behavior, the temperature dependencies of the relative dielectric permittivity (ε′) and loss tangent (tan δ) of the SFO and SFN3O ceramics were measured in the temperature range of 25–600 °C at three different frequencies, namely 100 kHz, 500 kHz, and 1 MHz (Figure 3a,d). At the Curie temperature, the arrangement of spins in ferrites changes from the long-range ordered ferromagnetic state to a paramagnetic state with random orientations. The magnetic transitions are usually accompanied not only by changes in the magnetic properties but also by variations in other physical properties, such as dielectric permittivity, specific heat, and so on.52 For SFO, two broad dielectric anomalies with a strong frequency dependence are observed in ε′(T) in regions I and II (Figure 3a). It should be noted that the dielectric permittivity reflects the ability of electric dipoles to oscillate in an applied AC field.53 Hence, the large decrease of the permittivity with increasing frequency from 100 kHz to 1 MHz can be explained by a lower contribution of interfacial polarization or point defects to the permittivity at higher frequencies. The second dielectric anomaly over regions II and III corresponds to the thermal feature b in Figure S2 and indicates a magnetic phase transition. The maximum of the permittivity occurs at a characteristic temperature, which shifts toward higher temperatures with increasing frequency. The frequency dispersion and diffusion of both dielectric peaks (in region I and through regions II and III) suggest that relaxation in the SFO hexaferrite can be attributed to point defects. The relaxation behavior should obey the Arrhenius law,54,55 as shown in Figure 3b,c.

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Figure 3.

Figure 3

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Temperature dependencies of the relative dielectric permittivity (ε′) and loss tangent (tan δ) of SFO (a) and SFN3O (d). (b, c) Arrhenius law fittings of the dielectric peaks of SFO in regions I and II, respectively. (e) Enlarged view of the loss tangent of SFN3O with a strong frequency dependence at temperatures between 25 and 160 °C. (f) Arrhenius law fitting of the dielectric peak in region II for the SFN3O hexaferrite.

where τ is the relaxation time of defects, τ0 is a time constant, Ea is the activation energy, kB is the Boltzmann constant, and T is the temperature linked with the maximum of ε′. The fitted activation energy Ea (0.037 eV) and relaxation time τ0 (3.8 × 10–8 s) for the first anomaly of SFO at around 100 °C suggest that the dielectric peak in region I is due to point defects, such as oxygen vacancies with long relaxation time. The second dielectric anomaly in the overlapping regions II and III is characterized by the values of Ea = 0.283 eV and τ0 = 2.24 × 10–11 s, which are characteristic of oxygen vacancies.

For the SFN3O sample, four dielectric anomalies with different dependence on frequency are observed at temperatures between 25 and 600 °C. In contrast to SFO, there is no anomaly in region I. With increasing temperature above 100 °C, a nearly frequency-independent permittivity anomaly occurs at around 270 °C in region II (Figure 3d). The corresponding loss peak is presented in Figure 3e. The fitted relaxation time τ0 = 1.30 × 10–9 s (see Figure 3f for the Arrhenius law fitting) is similar to that obtained for SFO, suggesting a contribution to the dielectric permittivity from defects. Instead, the dielectric anomaly of the SFN3O ceramic at 270 °C can be linked with a magnetic phase transition, which is consistent with the results of the DSC analysis (the event b in Figure S2b). The third, most intense anomaly is a frequency-independent feature occurring at about 400 °C. It is assumed that the loss peak at a slightly lower temperature (∼370 °C) is caused by enhanced domain wall activity, typical of ferroelectric materials.53,56 It should be mentioned that the fourth dielectric anomaly at around 500 °C shows a diffuse behavior but without a temperature shift. Moreover, this temperature is close to the thermal event c in the DSC curve (Figure S2b), suggesting the ferrimagnetic-to-paramagnetic phase transition. It is obvious that the Nb substitution increases the Curie temperature of the SrFe12O19 hexaferrite, which agrees well with the earlier study of Wang et al.57 This finding is further supported by the loss tangent minimum observed close to 500 °C.56 The origin of the dielectric anomalies (either the phase transition or point defects) is still under debate. Further studies are necessary to clarify the anomalous high-temperature critical behavior of hexaferrites.

The field cooling (FC) magnetization and zero-field cooling (ZFC) magnetization as a function of temperature for the respective SFO and SFN3O samples are shown in Figure 4a,b. At cryogenic temperatures, the FC magnetization increases from 0.013 emu/mg for SFO to 0.022 emu/mg for SFN3O. This increment of magnetization corresponds to the higher saturated magnetization Ms of SFN3O (see Table 1), as obtained from the M–H hysteresis loops in Figure 4c. For SFO and SFN3O, both the ZFC and FC magnetizations increase monotonously upon cooling from 300 K down to 100 K. Below 100 K, a plateau-like hump is observed due to the super spin-glass (SSG) behavior.58 Humbe et al.59 have reported on the magnetization peak in hexaferrites occurring at the blocking temperature (Tb), where a magnetic structure changes from a superparamagnetic to ferrimagnetic one. No other peak corresponding to a possible phase transition from ferrimagnetic to paramagnetic phase is observed in Figure 4a,b for the respective SFO and SFN3O ceramics over a temperature range of 1.8–400 K. Therefore, one can postulate that the two hexaferrites are ferrimagnets at room temperature.

Figure 4.

Figure 4

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(a, b) ZFC and FC magnetization curves for SFO and SFN3O, respectively. (c) M–H hysteresis loops for SFO and SFN3O measured at 300 K.

Table 1. Magnetic Parameters of the SFO and SFN3O Hexaferrites, As Obtained at Room Temperature.

composition saturated magnetization Ms(emu/mg) remnant magnetization Mr(emu/mg) coercive field Hc (Oe) squareness ratio Mrs
SFO 0.068 0.033 4200 0.485
SFN3O 0.076 0.034 2850 0.447
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Figure 4c displays the M–H loops of the SFO and SFN3O samples measured at room temperature. Both SFO and SFN3O show typical ferrimagnetic behavior. The saturated magnetization Ms for SFO and SFN3O is 0.068 and 0.076 emu/mg, respectively. Both Ms and Mr for SFO are higher than the previous work9 possibly due to different preparation methods but agree well with other published work.15 According to earlier studies on the SFO-derived hexaferrites,60 a high value of Ms can be ascribed to the high concentration of Fe3+ ions in a high spin state and enhanced ferromagnetic exchange interactions between Fe ions caused by decreased oxygen deficiencies.58 In this case, nonmagnetic Nb5+ ions replacing the Fe ions at 4f1 and 4f2 sites (spin-down states) give rise to the increased net magnetic moment together due to the enhanced ferromagnetic exchange coupling along the z-axis via Fe3+–O–Nb5+ bonds. This is consistent with fitted XRD results and agrees well with previous findings that Nb or other diamagnetic ions prefer to enter the octahedral and tetrahedral sites of Fe in hexaferrites,23,61−63 and the intensity of antiferromagnetic exchange interactions is weakened as the oxygen vacancy decreases.64,65

It is expected that both SFO and SFN3O possess multidomain structures with the squareness ratio (Mrs = Mr/Ms) 0.485 and 0.447, respectively.61,66 A slimmer M–H loop of SFN3O is observed in Figure 4c compared with SFO. According to the domain wall theory,67Inline graphic, where A is the exchange stiffness, HA is the magneto-crystalline anisotropy, Ms is the saturation magnetization, and D is the grain size.68 The coercive field Hc is proportional to the inverse Ms and smaller grain size.69,70 Therefore, one would expect that the dominant reason for a large drop in Hc, nearly 30% of SFN3O, against the initial coercive field of SFO is the increment of saturation magnetization. The room-temperature magnetic parameters of the SFO and SFN3O samples are summarized in Table 1.

A schematic of the setup for measurement of the THz transmission response is shown in Figure 5. Using this setup, the Faraday rotation was determined by the refractive index measured for the left- and right-handed directions after magnetizing the samples at a DC field of 3500 Oe. The permittivity was obtained from the measured refractive index n using the following equation

graphic file with name am2c13088_m003.jpg 2

where μ′ and ε′ are the relative permeability and relative permittivity, respectively. Figure 6a shows the frequency dependencies of the dielectric permittivity and loss tangent of the as-prepared (nonmagnetized) SFO and SFN3O samples in the THz band. The permittivity of both hexaferrites is nearly independent of the frequency due to a large ionic polarization and partly because of electronic polarization71 within the 0.2–0.8 THz range. A slightly higher value of ε′ and tan δ of SFN3O can be attributed to the smaller grain size effect, reduced coercive field, and higher concentration of the ferrimagnetic active regions at THz frequencies. Figure 6b,c shows the respective complex refractive index for the right- and left-handed directions in the 0.2–0.8 THz range; n′ is the real part while n″ is the imaginary part of the refractive index. The value of Δn′ (n′left-handed – n′right-handed) is 0.75 for SFO, and it greatly increases to 1.30 for SFN3O. This result clearly demonstrates that the Nb substitution improves the magnetic properties of the pure SFO hexaferrite. Thus, the enhanced magneto-optical behavior, namely the Faraday rotation effect in SFN3O, can be attributed to the higher Ms and lower Ec. Moreover, the imaginary part of the right-handed refractive index (n’’) of SFN3O shows a steeper decline with decreasing frequency than that of SFO, reaching a value of n’’ of about 0.01 within 0.5 THz. This behavior can be explained by the reduced oxygen vacancies and partial oxidation of Fe2+ (Fe2+ → Fe3+) during thermal treatment.29

Figure 5.

Figure 5

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Schematic of the Faraday rotation measurement setup based on the modified THz time-domain spectroscopy. M1–M5: flat reflection mirrors; Si: silicon wafer; E: THz photoconductive emitter; GPM1-GPM5: parabolic mirrors to focus and collimate THz beams; S.H: sample holder; D: THz photoconductive detector; and AM: adjustable retroreflection mirror. The black lines guided by arrows are the transmission THz beam, and the blue lines guided by arrows are the 780 nm probe beam.

Figure 6.

Figure 6

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(a) Relative dielectric permittivity and loss tangent of the as-prepared SFO and SFN3O samples at the 0.2–0.8 THz band. (b, c) Complex refractive index of the right- and left-handed directions for the magnetized SFO and SFN3O samples, respectively, at frequencies from 0.2 to 0.8 THz.

It can be concluded that the introduction of Nb into M-type hexaferrites is an effective way to improve their room-temperature ferrimagnetic properties and, at the same time, enhance their dielectric behavior in the THz band. The proposed chemical design with donor Nb5+ doping in the hexaferrites enables the development of advanced functional materials with improved magneto-optical properties and low dissipation for high-performance imaging and sensing applications in the THz band.

Conclusions

The M-type hexaferrites of SrFe12–xNbxO19 (x = 0.00 and 0.03) were prepared by the solid-state reaction. The room-temperature XRD data demonstrate that the two ceramics are single-phase materials with the P63/mmc space group. The mixed valence states of Fe (Fe3+/Fe2+) together with oxygen vacancies were revealed by XPS analysis, with SFN3O having fewer oxygen vacancies than SFO. SQUID measurements of the field dependence of magnetization and ZFC/FC magnetization over the temperature range 1.8–400 K evidenced the ferrimagnetic behavior of these two compositions. The increased saturated magnetization (0.076 emu/mg) in the x = 0.03 sample was explained by the preferred arrangement of Fe3+ ions in the spin-up state. The composition-driven enhancement of both the multidomain structure and ferromagnetic exchange coupling led to a higher saturation and lower coercivity of the Nb-doped hexaferrite. Moreover, this enhanced magnetic performance is accompanied by a large Faraday rotation (Δn′ = 1.30) and high relative permittivity in the THz band. Overall, the Nb-doped SrFe12O19 hexaferrite with excellent magnetic properties in the THz band provides a competitive performance for microwave devices, filters, and recording media.

Acknowledgments

The authors would like to acknowledge the National Natural Science Foundation of China (nos. 12174146 and 91963201), the 111 Project under grant no. B2006, the Grant Agency of the Slovak Academy of Sciences (VEGA grant nos. 2/0038/20 and 2/0034/23), and the Chinese Scholarship Council (no. CSC201806370199) for supporting this work.

Supporting Information Available

The Supporting Information is available free of charge at https://pubs.acs.org/doi/10.1021/acsami.2c13088.

  • Fitted XRD patterns at room temperature; crystal and refinement parameters; fitted results for O 1s and Fe 2p XPS spectra; and DSC thermograms in heating and cooling regimes for SFO and SFN3O (PDF)

Author Contributions

Z.H. carried out laboratory research and data analysis and wrote the draft of the manuscript. G.B.G. Stenning conducted the magnetic measurement. V.K. contributed to manuscript proofreading. J.W. performed sample synthesis. B.Y. contributed to the THz measurement. A.L. contributed to magnetizing samples. R.W. contributed to the material design. M.J.R. and C.J. contributed to the theoretical discussion. H.Y. contributed to the theoretical discussion and manuscript proofreading.

The authors declare no competing financial interest.

Supplementary Material

am2c13088_si_001.pdf (229.8KB, pdf)

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