Optical spectroscopic analysis, supercapacitance, photocatalysis of BaTi_xFe_12-(4/3)xO₁₉ hexagonal nanoparticles

Obviously, BaTi_xFe_12-(4/3)xO₁₉ Hexagonal nanocrystals are excellent candidates as photocatalysts in water purification, as well as using them as electrode materials for supercapacitors and energy storage applications. M-Type Hexagonal nanoparticles (BaTi_xFe_12-(4/3)xO₁₉, 0 ≤ x ≤ 1) with the magneto-plumbite structure were formerly synthesized by co-precipitation procedure and investigated by several techniques such as XRD, FT-IR, Raman, Photoluminescence and UV-VL. XRD and FT-IR confirmed the structure, and Raman spectra showed 12 characterizing summits. Photoluminescence emission spectra indicated two summits at 448 and 501 nm. Optical UV-VL spectroscopic analysis parameters showed dependence on λ and x. Obviously, BaTi_0.75Fe₁₁O₁₉ nanocrystals as a sort of M-Type Hexagonal Ferrites showed excellent Photocatalytic activity on the Degradation of Organic Dyes like; Crystal Violet, Methyl Orange, … etc. Furthermore; these nanocrystals possess excellent electrochemical performance; which in turn introduces these materials for Supercapacitors Applications. Thus, the Photo-catalytic activity of BaTi_0.75Fe₁₁O₁₉ nanocrystals for the decolorization of Crystal Violet (CV) dye (1 × 10^-5 M) illuminated excellent photocatalytic efficiency reaching ≈ 85%. On the other hand; BaTi_0.75Fe₁₁O₁₉ nanoparticles exhibited a specific capacitance of 1858 mF/g at 50 mV/s. The current study introduces promising applications of BaTi_0.75Fe₁₁O₁₉ nanoparticles as electrode materials for super capacitance and energy storage.

Introduction

Hexagonal Nano-ferrites continue to be very substantial nanoparticles till the present time both from scientific, industrial as well as technological prospects ever since their discovery in 1950′s [1]. Specification of such nanocrystals as Nano-hexaferrite stems from their ultrafine crystallite size or tiny nanoparticles size as well as their hexagonal crystalline structure. Lately, the most advanced research vistas have greatly focused on developing and synthesizing new unique nanoparticles with ultra-small grains for implementations in so many, diverse and expanding fields of technology such as shielding technology, magnetic recording media, spintronics, and microwave absorbing materials due to their excellent chemical stability, high thermal stability, non-toxicity, and extremely high corrosion resistivity [1-3]. Concomitantly, these M-Type hexagonal nanoparticles are utilized in industrial implementations in RADAR, wireless communication technologies, networks, Mobile technologies, and permanent magnets [4,5]. Furthermore, these M-type hexagonal nanoparticles have been also largely applied in versatile vistas like multiferroics [4,5]. Concomitantly, M-Type hexagonal nanoparticles are candidate targets as RADAR attenuating substances imputing their high permeability and high saturation magnetization [5-8]. Many research studies were concerned with the preparation of M-type hexagonal nanoparticles with diverse ions permutation utilizing diverse synthesis routes and varied characterizing techniques for the obtained Nano-samples [5-8]. Particle sizes, lattice parameters, saturation magnetization, coercivity, magneton number, and dislocation density of such hexagonal nano-ferrites were affected by synthesis conditions, thermal treatments, and substitution processes [5-8].

For BaTi_xFe_12-(4/3)xO₁₉ Hexagonal nanocrystals; the introduction of Ti⁴⁺ cations instead of Fe³⁺ cations decreases the Band Gap Energy to the least value for x = 0.75 (BaTi_0.75Fe₁₁O₁₉ nanocrystals) which equals Eg = 3.3 eV. This in-tern increases its photocatalytic activity which is based on the hopping of electrons from the valency band to the conduction band, furthermore; for the small band gap of BaTi_0.75Fe₁₁O₁₉ nanocrystals; electrons become more easily to move from the valency band to conduction band with high drift mobility so that free radicals are formed according to Figure 1 [9-15]:

Figure 1: Photocatalysis mechanism of BaTi_0.75Fe₁₁O₁₉ for Degradation of Crystal Violet.

Furthermore, the following equation demonstrates how the free radicals are formed:

$\begin{array}{l}{e}^{-}+O_2\stackrel{h\nu }{\to }{}^{•}O{}_2^{-}\\ e^{-}+H_{2}O\stackrel{h\nu }{\to }{H}^{+}+{}^{•}OH\end{array}$

In Nano-ferrites the electrons from the valency band are liberated to the conduction band leaving holes behind them in the valency band with the aid of photons from 100 W Tungsten lamb. Electrons in the conduction band unit with O₂ and OH give free radicals, which attack Crystal Violet (CV) dye with the help of photons from 100 W Tungsten lamp making degradation to CV dye easier giving degraded products in the form of CO₂ and H₂O according to the following equation [16-18]:

$O_2^{•-}+C{V}^{•+}\stackrel{h\nu }{\to }Degraded-\mathrm{Pr}oducts-(H_{2}O+C{O}_2)$

On the other hand; the substitution of Ti⁴⁺ instead of Fe³⁺ cations in BaTi_xFe_12-(4/3)xO₁₉ Hexagonal nanocrystals decreases the Band Gap Energy to the least value for x = 0.75 (BaTi_0.75Fe₁₁O₁₉) which equals Eg = 3.3 eV. The replacement of Ti⁴⁺ cations with a smaller ionic radius (0.61 Å) instead of Fe³⁺ cations with a larger ionic radius (0.64 Å) induces the decrease of hopping length between cations according to the following equation:

$\begin{array}{l}F{e}^{3+}+T{i}^{4+}\stackrel{}{\to }F{e}^{4+}+T{i}^{3+}\\ F{e}^{4+}+F{e}^{2+}\stackrel{}{\to }2F{e}^{3+}\end{array}$

Thus the oxidation and reduction processes are really occurring all the interaction time in BaTi_xFe_12-(4/3)xO₁₉ Hexagonal nanocrystals and the least band gap energy accompanied with the least hopping length is a fact chemical property for x = 0.75 (BaTi_0.75Fe₁₁O₁₉ nanocrystals). These natural, active, and fast oxidation and reduction processes occurring in BaTi_0.75Fe₁₁O₁₉ nanocrystals are the basis for the supercapacitor’s electrochemical performance indicating that BaTi_0.75Fe₁₁O₁₉ nanocrystals are excellent candidates for supercapacitor and energy storage applications [19-28]. Whereas; Barium element possesses only one oxidation state (Ba2+ cations) and it is a paramagnetic cation.

The current investigation is devoted to synthesizing M-type hexagonal BaTi_xFe_12-(4/3)xO₁₉ nanoparticles by the chemical co-precipitation method. The samples were characterized using X-ray diffraction (XRD), FTIR, Raman, Photoluminescence, and UV-VL spectral analysis. Furthermore, their Photocatalysis in the degradation of Crystal Violet (CV) and electrochemical performance, Supercapacitance were also investigated.

Experimental section

Chemical materials

All chemical reagents were extra-high purity AnalaR (AR) grade and used as received without further purification, and were purchased from Sigma-Aldrich. Stoichiometric proportion amounts of the high purity Ba(NO₃)₂, Ti(C₁₂H₂₈O₄), Fe(NO₃)₃ -9H₂O and NaOH were used. All aqueous solutions were freshly prepared using high-purity distilled water.

Materials synthesis

M-type hexagonal BaTi_xFe_12-(4/3)xO₁₉ nanoparticles, x = 0, 0.125, 0.25, 0.375, 0.5, 0.75, and 1 were prepared by the chemical co-precipitation method according to the equation [3];

Ba(NO₃)₂ + x Ti(C₁₂H₂₈O₄) + (12–(4)/(3)x) Fe(NO₃)₃-9H₂O + (38-4x) NaOH → BaTi_xFe_12-(4/3)xO₁₉ + (38-4x)NaNO₃ + 4x(CH₃)₂CHOH + (127-16x)H₂O

Stoichiometric proportion amounts of the high purity AnalaR (AR) grade Ba(NO₃)₂, Ti(C₁₂H₂₈O₄), and Fe(NO₃)₃-9H₂O were dissolved in distilled water and kept at about 10 °C for one hour (h). The reactants were mixed and constantly stirred using a magnetic stirrer for 10 min. The NaOH solution was added drop-wise where the pH of the mixed solution was constantly monitored as pH ≈ 13. Then the solution was heated and maintained at 90 °C for 2 h under continuous stirring till the precipitation occurred. The precipitates were thoroughly washed with distilled water until the washings become free from sodium Nitrate. The precipitates were dried for a few days at room temperature. Then the samples were thoroughly ground in an agate mortar to obtain a fine powder. Thereafter, the samples were annealed for 20 h at 1200 °C and then slowly cooled to room temperature. The samples were ground to a fine powder and annealed again at 1200 °C for 20 h and then slowly cooled to room temperature. Finally, the nanoparticle samples were ground in an agate mortar to fine powder [3].

Characterization

Materials characterization: M-type hexagonal BaTi_xFe_12-(4/3)xO₁₉ nanoparticles, (x = 0, 0.125, 0.25, 0.375, 0.5, 0.75, and 1) were prepared by the chemical co-precipitation strategy; as reported earlier by Amer, et al. (2015) [3]. These samples have been characterized by an X-ray diffractometer (GNR APD 2000 Pro step scan type and CuKα1 radiation with wavelength λ = 1.540598 Å). FT-IR spectra for all nano-samples were exhibited by using Bruker-Tensor-27- FT-IR - type Spectrometer in the range 200 to 2000 cm^-1, at room temperature. Raman spectra were measured by JASCO NRS-3100 micro-spectrometer with an excitation radiation of 532 nm laser. Room temperature photoluminescence spectroscopy (KIMMON KOHA, Tokyo, Japan, excitation wavelength, λ = 325 nm). UV–vis spectra were registered using JASCO V570 UV–VIS-NIR scan-type spectrophotometer in the wavelengths 190–1200 nm at room temperature.

Photocatalytic activity: Photocatalytic features for BaTi_0.75Fe₁₁O₁₉ nanocrystals were scrutinized via photo-disintegration of the simulated dye wastewater of Crystal Violet (CV) dye solution under VL irradiation utilizing 100 Watt Tungsten lamp fixed at ~ 10 cm distance, as illustrated earlier by Ghoneim (2021) [29]. Aqueous suspension of CV-dye (1 × 10^-5 M) and BaTi_0.75Fe₁₁O₁₉ nanocrystals as photo-catalysts (0.1 g) were placed in a glass beaker. Prior to irradiation, each suspension was stirred in the dark for 2 hrs to establish adsorption-desorption equilibrium (between photo-catalysts and dye), followed by VL irradiation utilizing 100 Watt Tungsten lamp fixed at ~ 10 cm distance. At time spans (20 min), 3 mL of suspension was taken from the beaker, and then filtered to remove solid powders. Thence, solutions were analyzed by UV–VIS scan-type photometer in the wavelengths 190 – 1200 nm at ambient temperature to obtain relative concentration variations of solution. UV–vis spectra were registered using SPECTRO UV–VIS DUAL BEAM 8 AUTO CELL UVS-2700 scan-type spectrophotometer in the wavelengths 190–1200 nm at ambient temperature. Curve about concentration variations (C/Co) as a function of time was plotted, where C presented the concentration of CV at each time interval and C₀ was the initial concentration of CV after reaching adsorption-desorption equilibrium [29-31].

Electrochemical characterization: Electrochemical Performance measurements were carried out by a three-electrode cell system using a Solartron SI 1286 electrochemical workstation in 1 M KOH electrolyte solution at room temperature. The working electrode was prepared by mixing BaTi_0.75Fe₁₁O₁₉ nano-hexa-ferrites into a solution of isopropyl alcohol, water, and nafion (volume ratio 5:5:0.1) with the help of ultra-sonication (10 min) to form the homogeneous solution. From the mixed solution, a 10 μL amount of liquid was dropped on a glassy carbon electrode (GCE) (3 mm diameter) and the liquid was evaporated in air to dry the active materials. In three-electrode measurements, BaTi_0.75Fe₁₁O₁₉ Hexagonal nanoparticles, platinum (Pt) wire, and Hg/HgO work as working electrode, counter electrode, and reference electrode, respectively. Cyclic voltammetry (CV) and galvanostatic charging/discharging measurements were carried out to investigate the electrochemical performance of BaTi_0.75Fe₁₁O₁₉ Hexagonal nanoparticles electrode for super-capacitance SCs applications.

Results and discussion

X-Ray Diffraction (XRD) spectra analysis

X-ray diffraction patterns (XRD) and their initial analysis for M-type hexagonal BaTi_xFe_12-(4/3)xO₁₉ nanoparticles, (x = 0, 0.125, 0.25, 0.375, 0.5, 0.75 and 1) were investigated and published earlier by Amer, et al. (2015) [3] as indicated in Figure 2. XRD plots in Figure 2 proved that the samples have single-phase M-type hexagonal structure [3], which was affirmed by matching with JCPDS data (Card nos. 00-027-1029, 00-007-0276 and 01-079-1411).

Figure 2: XRD plots of BaTi_xFe_12-(4/3)xO₁₉ nanoparticles, (x = 0, 0.125, 0.25, 0.375, 0.5, 0.75 and 1).

Table 1 illustrates the relation between the unit cell volume Vcell and Ti⁴⁺ content x.

Unit cell volume for BaTi_xFe_12-(4/3)xO₁₉ M-type hexagonal nanoparticles has been calculated from the relation [31,32]; $V_{cell}=\frac{\sqrt{3}}{2}{a}^{2}c$

It is clear that V_cell for these nanoparticles increases with x; (Table 1).

Dislocation density δ was calculated by using the relation [33]:

$\delta =\frac{1}{R^2};$

Where R is the crystallite size.

The inter-chain separation r and the distortion parameter g have been calculated using the relations [33]:

$r=\frac{5\lambda }{8\sin \theta }$

$g=\frac{{\beta }_{\frac{1}{2}}}{\tan \theta }$

Table 1 displays the reliance of r, g, and δ with the change of Ti⁴⁺ content x.

It is clear that r, g, and δ increase with Ti⁴⁺ content x imputing to the substitution process.

Elastic Parameters

FT-IR spectra from 200 to 2000 cm^-1 and their initial analysis for M-type hexagonal BaTi_xFe_12-(4/3)xO₁₉ nanoparticles, (x = 0, 0.125, 0.25, 0.375, 0.5, 0.75 and 1) were investigated and published earlier by Amer et al (2015) [3].

Elastic Parameters extracted from FT-IR Spectra are presented in the following:

For investigating the elastic attributes of these nanocrystals, elastic moduli as Young’s modulus E, bulk modulus K, and modulus of rigidity G are concluded using the formulas [34-36]:

$\text{Young}\text{'}\text{s Modulus }E=\frac{\left(C_{11}-C_{12}\right)\left(C_{11}+2C_{12}\right)}{\left(C_{11}+C_{12}\right)}$

$\text{Rigidity Modulus }G=\frac{E}{2\left(\sigma +1\right)}$

$\text{Bulk Modulus }K=\frac{1}{3}\left(C_{11}+2C_{12}\right)$

Where C₁₁ and C₁₂ are stiffness constants, and σ is Poisson’s ratio [34-36].

Table 2 illuminates that the three moduli: E, K, and G change nonlinearly with x.

Wave velocities

Longitudinal elastic wave velocity (V_L), shear wave velocity (V_S), and the mean wave velocity (V_m) are concluded from the formulations [34,35]:

$\text{Longitudinal Velocity }{V}_L={\left(\frac{C_{11}}{D_x}\right)}^{\frac{1}{2}},$

$\text{Shear Velocity }{V}_S={\left(\frac{G_o}{D_x}\right)}^{\frac{1}{2}},$

PThe mean wave velocity V_m can be deduced using the relation: $\frac{3}{V_m^3}=\frac{1}{V_L^3}+\frac{2}{V_S^3},$

Where G_o is the rigidity modulus with zero pore fraction. Table 3 illustrates the variation of V_L, V_S, and V_m against x. It is plain that V_L, V_S, and V_m increase with Ti⁴⁺ ion increase x. Obviously, the dependence of density D_x on both elastic moduli and wave velocities influences their values. The elastic moduli and wave velocities rise to reflect the variation of crystal structure and prove that the wave velocities are strongly correlated with the nanocrystal’s density [34,35,37].

Raman spectra

Raman spectra investigated for M-type hexagonal BaTi_xFe_12-(4/3)xO₁₉ nanoparticles, (x = 0, 0.125, 0.25, 0.375, 0.5, 0.75 and 1) at room temperature are shown in Figure 3. In the frequency range of 100-800 cm^-1 for BaTi_xFe_12-(4/3)xO₁₉ nanoparticles, there appears 12 summits at frequencies ν ∼ 173, 183, 215, 282, 318, 345, 415, 470, 521, 616, 686 and 715 cm^-1. These results agree well with the previously earlier published work [1,2]. Summits ν in between 318 – 715 cm^-1 are essentially related to the oscillations of iron polyhedra. Summits at 345, 470, and 616 cm^-1 are due to vibrations of Fe1(2a)-O6 octahedra. Summits at 318, 521 and 616 cm^-1 are due to vibrations of Fe4(4fVI)/Ti4(4fVI)-O6 octahedra. Summits at 415, 521 and 616 cm^-1 are due to vibrations of Fe5(12k)/Ti5(12k)-O6 octahedra. Summits at 686 cm^-1 modes are related to oscillations of the bipyramidal anion Fe2(2b)-O5 sublattices, and Summits at 715 cm^-1 are related to oscillations of the tetrahedral anion Fe3(4f_IV)/Ti3(4f_IV)-O4 sublattices. The contribution of the Ti⁴⁺ diamagnetic cations in the nanocrystals leads to a shift and distortion of the Raman spectra [1,2].

Figure 3: Raman spectra at room temperature for M-type hexagonal BaTi_xFe_12-(4/3)xO₁₉ nanoparticles, (x = 0, 0.125, 0.25, 0.375, 0.5, 0.75, and 1).

Photoluminescence spectra

Photoluminescence (PL) spectroscopy was measured at room temperature to investigate the optical property of M-type hexagonal BaTi_xFe_12-(4/3)xO₁₉ nanoparticles, (x = 0, 0.125, 0.25, 0.375, 0.5, 0.75 and 1) as shown in Figure 4. Furthermore, it was further studied to survey the efficiency of photocatalytic charge carrier’s generation and mobility [38]. It gives information about the ability to separate photo-generate electrons-holes in BaTi_xFe_12-(4/3)xO₁₉ nanoparticles. Figure 4 displays the PL emission spectra of BaTi_xFe_12-(4/3)xO₁₉ nanoparticles with summits at 448 and 501 nm wavelengths as the excitation sources. The photoluminescence peaks are mainly the result of electron-hole pairs recombination. Obviously, the emission summits position is nearly unchanged. It could be concluded that M-type hexagonal BaTi_xFe_12-(4/3)xO₁₉ nanoparticles should possess the highest photocatalytic activity, which is in good agreement with the experiment of Photocatalytic Activity illustrated later.

Figure 4: (a) Photoluminescence (PL) spectra of M-type hexagonal BaTi_xFe_12-(4/3)xO₁₉ nanoparticles, (x = 0, 0.125, 0.25, 0.375, 0.5, 0.75 and 1), (b-d) Photo-catalytic efficiency and Photo-Degradation of CV (1 ×10^-5 M) utilizing BaTi_0.75Fe₁₁O₁₉ nanocrystals as photo-catalysts, with time duration 20 min.

Optical UV-VL spectroscopic analysis

UV-VL absorbance (A) as well as, the reflectance R and the transmittance T spectral plots for M-type hexagonal BaTi_xFe_12-(4/3)xO₁₉ nanoparticles, (x = 0, 0.125, 0.25, 0.375, 0.5, 0.75 and 1), were illuminated in Figure 5. Where the transmittance T has been concluded by using the formula [39]:

Figure 5: Absorbance A, Reflectance R, Transmittance T, refractive index (n), and optical band gap energy (Eg) for BaTi_xFe_12-(4/3)xO₁₉ nanoparticles.

A + R + T = 1

The absorption coefficient α (ν) as presented in Figure 6 for BaTi_xFe_12-(4/3)xO₁₉ nanoparticles with increasing x can be confirmed using the formula [39]:

Figure 6: Variation of ε′ the real part and ε″ the imaginary part of the dielectric constant, dielectric loss Tan δ, optical conductivity (σ_optical), absorption coefficient α (ν) and extinction coefficient K(cm^-1) with λ.

$\alpha (\nu )=2.303\left(\frac{A}{d}\right),$

Where A is the absorbance, and d is the nano-sample thickness.

Absorption edge and band-gap energy (Eg) were derived from [40-45]:

$(\alpha \cdot h\nu )=B{\left(h\nu -E_g\right)}^n,$

Where hν is the photon’s energy, α is the optical coefficient of absorbed power and B is a transmission constant of electrons [41,42]. The absorption peak observed at 580 nm corresponds to M-type hexagonal BaTi_xFe_12-(4/3)xO₁₉ nanoparticles, as illustrated in Figures 5,7 clarifies the relation between (αhν)² and photon energy (hν (eV)). It is explicit that the UV cut-off trend is reversible to the optical energy gap of nanocrystals with varying x at which it is acquired from plot-tangent (Figure 7). The absorption detected edge in the visible section for these nanomaterials is in synchrony with the electron hopping from O-2p level into Fe-3d level for these nanocrystals [41,42].

Figure 7: The optical energy gap for BaTi_xFe_12-(4/3)xO₁₉ nanoparticles.

The decrease of Eg with x (Fig. 5) reflects the substitution process as well as the increase of lattice spacing and oxygen ion concentration in the sample [40,43,45].

The extinction coefficient as shown in Figure 6 is usually calculated using the well-known relation [39]: $K=\frac{\alpha \lambda }{4\pi }$

Substantially, Refractive index n was derived from reflectance R [39,40]; according to:

$R=\frac{{\left(n-1\right)}^2}{{\left(n+1\right)}^2}$

Changing of n with UV-photon wavelength λ (nm) was demonstrated in Figure 5. Optical conductivity (σ_optical) demeanor with λ for the nanocrystals was displayed in Figure 6, whereas the distinctive evaluation of σ_optical was concluded from the formula [39,40]:

${\sigma }_{Optical}=\frac{\alpha \cdot n\cdot C}{4\pi },$

Where α is the optical coefficient of absorbed power and C is light velocity. The optical conductivity (σ_optical) for all the annealed nanoparticles showed a sharp increase with λ up to ~ 580 nm and decreases thereafter in a gradual manner. Complex dielectric constant has real and imaginary parts that are explained [39,44] using the expressions:

$\epsilon \text{'}=n^2-K^2\text{ and }\epsilon "=2nK$

Regarding the reliance of ε′ with λ (nm) as indicated in Figure 6; an explicit dispersion of ε′ was observed for all nano-samples, i.e., ε′ values are high at long wavelengths and shows a peaking behavior at ~ 580 nm and gradually decrease thereafter. Whilst ε” gradually increases with λ as shown in Figure 6. Dielectric loss tangent (Tan δ) was calculated from the following expression [46]:

$Tan\delta =\frac{\epsilon "}{\epsilon \text{'}}$

It is clear that Tan δ increase with λ (nm) as indicated in Figure 4.

Photocatalytic Activity of BaTi_0.75Fe₁₁O₁₉ nanocrystals

The photo-catalytic activity of BaTi_0.75Fe₁₁O₁₉ nanocrystals for the sequent decolorization of Crystal Violet (_CV) dye (1 × 10^-5 M) in aqueous solution under VL irradiation via 100-Watt Tungsten lamp fixed at ~ 10 cm distance, investigated with an increase of time intervals up to 180 minutes, (time duration is 20 min) were affirmed in Figure 4. All of the catalytic disintegration reactions followed pseudo-first-order kinetics, confirmed with the plot of (C/C_o) against time (min), and the plot of ln (C/C_o) against contact time (min), (Figure 4). Clearly, _CV concentrations decrease with the increase of stirring time affirming the photocatalytic activity of BaTi_0.75Fe₁₁O₁₉ nanocrystals. Photo-Degradation Efficiency was obtained by the following equation [29-31]:

$Degradation-Efficiency=\left(1-\frac{C}{C_o}\right)\times 100$

Photo-catalytic efficiency of BaTi_0.75Fe₁₁O₁₉ nanocrystals for _CV decolorization was easily shown in Figure 4, confirming the increase of their activity in the photo-degradation of _CV dye, and referring to how excellent quality will be the outcome of H₂O produced by this strategy. Obviously; the Photo-catalytic activity of BaTi_0.75Fe₁₁O₁₉ nanocrystals for the decolorization of Crystal Violet (_CV) dye (1 × 10^-5 M) illuminated excellent photocatalytic efficiency reaching ≈ 85%.

Electrochemical characterization of BaTi_0.75Fe₁₁O₁₉

The electrochemical performance of BaTi_0.75Fe₁₁O₁₉ nanoparticles was investigated by Cyclic Voltammetry (_CV) and tested in 1 M KOH electrolytes at room temperature. _CV curve of BaTi_0.75Fe₁₁O₁₉ nanoparticles electrode was determined at scan rates of (50 mV/s) in the potential range of −0.5–0.5 V as shown in Figure 8. BaTi_0.75Fe₁₁O₁₉ nanoparticles electrode exhibited larger _CV curve area, indicating its superior electrochemical performance, where _CV curve showed redox peaks. The nearly rectangular shape of the cyclic voltammetry curve revealed that electric double-layer capacitance was dominant [47-50]. This represents that the redox reactions on the electrode surface were fast and reversible. The specific capacitance of BaTi_0.75Fe₁₁O₁₉ nanoparticle electrode materials equals 1858 mF/g, proving that BaTi_0.75Fe₁₁O₁₉ nanoparticles are electrode materials for Supercapacitance applications. The electrical behavior of electrode materials for SCs applications was investigated by electrochemical impedance spectroscopy (EIS). Figure 8 shows the Nyquist plots for BaTi_0.75Fe₁₁O₁₉ nanoparticles in the frequency range from 1.0 Hz to 20 kHz. Solution resistance (Rs) equals 22 Ω. There is a direct proportionality between Z′′ and Z′ giving diffusive resistance [47-50].

Figure 8: The electrochemical performance of BaTi_0.75Fe₁₁O₁₉ nanoparticles electrode. (a) CV curves at a scan rate of 50 mV/s and (b) Nyquist plot of BaTi_0.75Fe₁₁O₁₉ nanoparticles.

Conclusion

M-Type BaTi_xFe_12-(4/3)xO₁₉ nanoparticles were synthesized by co-precipitation strategy and examined using XRD, FT-IR, Raman, Photoluminescence, and UV-VL. XRD and FT-IR confirmed their M-Type Hexagonal structure, and Raman spectra showed 12 characterizing summits. Photoluminescence emission spectra of BaTi_xFe_12-(4/3)xO₁₉ nanoparticles indicated two summits at 448 and 501 nm wavelengths as the excitation sources. Band gap energy Eg decreases with Ti⁴⁺ ion content x reflecting the substitution process as well as the increase of lattice spacing and oxygen ion concentrations in the samples. All the optical UV-VL spectroscopic analysis parameters showed reliance on λ and x. The photocatalytic activity of BaTi_0.75Fe₁₁O₁₉ nanocrystals was acquired throughout the decolorization of Crystal Violet (CV) dye (1 × 10^-5 M) in aqueous solution under VL irradiation via 100 Watt Tungsten lamp fixed at ~ 10 cm distance. Cyclic voltammetry for studying super capacitance of BaTi_0.75Fe₁₁O₁₉ nanoparticles in 1.0 M KOH electrolyte solution. BaTi_0.75Fe₁₁O₁₉ nanoparticles exhibited a specific capacitance of 1858 mF/g at 50 mV/s. The nearly rectangular shape of the cyclic voltammetry curve revealed that electric double-layer capacitance was dominated. The current study introduces a promising application of BaTi_0.75Fe₁₁O₁₉ nanoparticles as electrode materials for super capacitance and energy storage. Nyquist plots for BaTi_0.75Fe₁₁O₁₉ nanoparticles were taken in the frequency range from 1.0 Hz to 20 kHz, and solution resistance (Rs) equals 22 Ω.

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