Next Article in Journal
Application of Ionic Liquids as Mobile Phase Additives for Simultaneous Analysis of Nicotine and Its Metabolite Cotinine in Human Plasma by HPLC–DAD
Next Article in Special Issue
Hydrothermal Synthesis of Nickel Oxide and Its Application in the Additive Manufacturing of Planar Nanostructures
Previous Article in Journal
Preliminary Structural Characterization of Selenium Nanoparticle Composites Modified by Astragalus Polysaccharide and the Cytotoxicity Mechanism on Liver Cancer Cells
Previous Article in Special Issue
Semi-Polycrystalline Polyaniline-Activated Carbon Composite for Supercapacitor Application
 
 
Search for Articles:
Title / Keyword
Author / Affiliation / Email
Journal
Article Type
 
 
Advanced Search
 
Section
Special Issue
Volume
Issue
Number
Page
 
Journals
Molecules
Volume 28
Issue 4
10.3390/molecules28041562
molecules-logo
Submit to this Journal Review for this Journal Propose a Special Issue
► Article Menu

Article Menu

share Share announcement Help format_quote Cite question_answer Discuss in SciProfiles thumb_up
...
Endorse textsms
...
Comment
first_page
settings
Order Article Reprints
Font Type:
Arial Georgia Verdana
Font Size:
Aa Aa Aa
Line Spacing:
Column Width:
Background:
Article

Supercapacitor Performance of Magnetite Nanoparticles Enhanced by a Catecholate Dispersant: Experiment and Theory

by
Coulton Boucher
,
Oleg Rubel
and
Igor Zhitomirsky
*
Department of Materials Science and Engineering, McMaster University, Hamilton, ON L8S4L7, Canada
*
Author to whom correspondence should be addressed.
Molecules 2023, 28(4), 1562; https://doi.org/10.3390/molecules28041562
Submission received: 6 January 2023 / Revised: 29 January 2023 / Accepted: 31 January 2023 / Published: 6 February 2023
(This article belongs to the Special Issue Recent Trends and Advances in Supercapacitor’s Electrode Materials and Their Applications)
Browse Figures
Versions Notes

Abstract

:
The full potential of Fe3O4 for supercapacitor applications can be achieved by addressing challenges in colloidal fabrication of high active mass electrodes. Exceptional adsorption properties of catecholate-type 3,4-dihydroxybenzoic acid (DHBA) molecules are explored for surface modification of Fe3O4 nanoparticles to enhance their colloidal dispersion as verified by sedimentation test results and Fourier-transform infrared spectroscopy measurements. Electrodes prepared in the presence of DHBA show nearly double capacitance at slow charging rates as compared to the control samples without the dispersant or with benzoic acid as a non-catecholate dispersant. Such electrodes with active mass of 40 mg cm−2 show a capacitance of 4.59 F cm−2 from cyclic voltammetry data at a scan rate of 2 mV s−1 and 4.72 F cm−2 from galvanostatic charge–discharge data at a current density of 3 mA cm−2. Experimental results are corroborated by density functional theory (DFT) analysis of adsorption behaviour of DHBA and benzoic acid at the (001) surface of Fe3O4. The strongest adsorption energy (ca. −1.8 eV per molecule) is due to the catechol group of DHBA. DFT analysis provides understanding of the basic mechanism of DHBA adsorption on the surface of nanoparticles and opens the way for fabrication of electrodes with high capacitance.

1. Introduction

Surface modification of materials using molecules from the catechol family is emerging as a new area of technological and scientific interest [1,2]. Catecholate molecules can achieve extremely strong adhesion to inorganic surfaces by utilizing a similar adsorption mechanism to that of mussel proteins when bonded to different surfaces [2,3,4]. Very fast and very strong adsorption to various inorganic substrates is a necessity for mussels to avoid damage by sea waves. This adhesion mechanism is attributed to bonding of the catechol ligands of the mussel proteins to metal atoms on material surfaces [4,5,6,7,8].
Polymer molecules were modified with catechol ligands for the fabrication of adherent polymer and composite films [4,9,10,11,12]. Catecholate molecules were used as charged dispersants for electrophoretic deposition of inorganic and organic materials [5,13,14]. Catecholate molecules were also utilized as particle transfer vehicles for liquid–liquid extraction [15], which prevented nanoparticle agglomeration. In this technology, inorganic particles were modified with catechol ligands in the synthesis medium or at the liquid–liquid interface and transferred from the synthesis medium directly to the device processing medium [15]. Catechol molecules facilitated efficient and versatile extraction [16] of MnO2, Mn3O4, FeOOH, and ZnO for energy storage and sensor applications. The phase transfer of the particles resulted in reduced agglomeration, which allowed for improved electrolyte access to the particle surface [16] and improved device performance.
Recent studies highlighted benefits of catecholate molecules for surface modification of materials for applications in dye-sensitized solar cells and photoelectrochemical sensors [17,18,19]. For dye-sensitized solar cells, a staggered gap heterojunction can occur at a catechol-TiO2 interface [17], which facilitates electron injection into the TiO2 semiconductor [20]. Such configurations improved dye-sensitized solar cell efficiency. Redox properties of catechol, related to oxidation of their phenolic OH groups, were used for electron transfer mediation in electrochemical biosensors [21]. Moreover, redox properties of catechol are under investigation for applications in bioelectronics [19,22], catalysis [23], and energy storage devices [24,25]. Enhanced capacitance has been seen in catechol-modified carbon cloth electrodes due to the additional contribution of electrochemical oxidation of catechol OH groups [26].
The ability of catechol to oxidize electrochemically to o-benzoquinone allows for many uses in electropolymerization [27,28]. It is known that o-benzoquinone participates in polymerization reactions, including chemical oxidative polymerization [29], electrochemical oxidative polymerization [30], and bipolar electropolymerization [27], to be used in a variety of biomedical applications including targeted drug delivery to cancer cells [31], catechol-modified polymers with antimicrobial properties [32], and structural adhesives for tissue and bone [33]. Catechol molecules can play an additional role as charge-transfer mediators [34]. The use of catecholate dopants for polypyrrole facilitated charge transfer, reduced electropolymerization potential, and allowed the fabrication of adherent polypyrrole films on non-noble substrates [35,36,37].
The functionalization of ferrimagnetic nanoparticles with catecholate molecules induced improved magnetization [38]. Other investigations reported applications of catecholate molecules for the fabrication of quantum dots and luminescent materials [39,40]. Catecholates have generated significant interest for applications in nanotechnology as capping, reducing, and structure directing additives, which facilitated the fabrication of nanoparticles of metals and metal oxides with controlled size, shape, and functional properties [41,42,43,44,45]. Further progress in the application of catecholates in nanotechnology can result in the development of advanced functional nanomaterials for modern applications. Catecholates are of particular interest for the fabrication of devices, based on materials, combining advanced magnetic and electrical properties [41,46,47].
This investigation was motivated by interesting electrical charge storage properties of iron oxides, such as Fe2O3 and Fe3O4 [41,48]. Fe3O4 is of particular interest for the development of multifunctional devices, based on the high capacitance and advanced ferrimagnetic properties of this material. It is known that Fe3O4 exhibits higher conductivity compared to many other spinel ferrimagnetic materials [49]. The relatively high conductivity of Fe3O4 is beneficial for electrochemical charge–discharge processes [49]. The pseudocapacitive charging mechanism of this material, containing Fe2+ and Fe3+ ions (Fe2+Fe23+O4), is attributed to redox Fe3+ ↔ Fe2+ reactions. The charge storage properties in the positive potential range [50,51] are attributed to oxidation of Fe2+ ions (Fe2+ → Fe3+), whereas the charging mechanism in the negative potential range is based on reduction of Fe3+ ions (Fe3+ → Fe2+) [41,52,53]. Fe3O4 is especially important for the development of negative electrodes of advanced asymmetric supercapacitors with an enlarged voltage window. Recently, significant progress was achieved in the development of different materials for positive electrodes, which showed high capacitance [54,55,56]. However, lower capacitance of the negative electrodes, such as activated carbon, is a limiting factor in the development of advanced devices. The important tasks in the development of Fe3O4 electrodes are the fabrication of small nanoparticles and prevention of their agglomeration, which can result from Van der Waals forces and magnetic attraction forces. Moreover, efficient mixing of non-agglomerated and well-dispersed nanoparticles with conductive additives is necessary for good electrode performance. Therefore, advanced capping and dispersing agents are critically important for the synthesis of small non-agglomerated Fe3O4 nanoparticles and fabrication of composite electrodes.
The goal of this investigation is the fabrication of Fe3O4 electrodes for supercapacitors using a catecholate-type 3,4-dihydroxybenzoic acid (DHBA) as a capping and dispersing agent for Fe3O4 nanoparticles. This goal was achieved in experimental studies of the synthesis of Fe3O4 particles, fabrication, and testing of supercapacitor electrodes and application of density functional theory (DFT) [57] for the analysis of the DHBA adsorption mechanism. Fe3O4 has emerged as a promising supercapacitor material due to its low cost and environmentally benign nature [58]. Here, we aimed at improving electrochemical performance of fabricated Fe3O4 supercapacitor anodes and selected DHBA as a catechol molecule to play the role of a capping and dispersing agent. The chemical structure of DHBA contains adjacent phenolic OH functional groups on the 3rd and 4th carbons on the benzene ring (Figure 1), providing strong adsorption to the particle surface, while a carboxyl group can facilitate dispersion via electrostatic repulsion [59,60]. These adsorption and dispersion properties are critical to prevent agglomeration of nanoparticles in solution, particularly materials with magnetic properties, such as Fe3O4. Benzoic acid (BA) is chosen as a negative control in our experimental design. The chemical structures of DHBA and BA differ only by the adjacent phenolic OH groups present in DHBA but not in BA (Figure 1). To corroborate the understanding of the adsorption processes seen in our experimental results, we used DFT to model DHBA and BA adsorption on the surface of Fe3O4 and assess their binding affinities and mechanisms.

2. Results and Discussion

2.1. Experimental Results

Dispersing properties of BA and DHBA were investigated by analysing the suspension stability of Fe3O4 particles in water (Figure 2). Fe3O4 suspensions without additives and containing BA showed rapid precipitation. However, the suspension prepared with DHBA as a dispersing agent remained stable, further confirming the role of the phenolic OH groups of the molecule for adsorption, which are functional groups that BA lacks. The synthesis of Fe3O4 was conducted at pH = 9, which is above the isoelectric point of Fe3O4 (pH = 6.5) [61]. Therefore, the as-prepared Fe3O4 particles were negatively charged. The adsorption of anionic DHBA on the negatively charged Fe3O4 particles indicated a strong adsorption power of the catecholate DHBA molecules.
The adsorption of DHBA on Fe3O4 particles was confirmed by results of Fourier Transform Infrared (FTIR) spectroscopy studies. Figure 3 compares FTIR spectra of Fe3O4 prepared without and with DHBA and pure DHBA.
The FTIR spectrum of Fe3O4 prepared without DHBA (Figure 3a) showed absorptions at 1355, 1475, and 1630 cm−1, which can be attributed [13,62] to stretching of surface OH groups and vibrations of adsorbed CO2. The broad absorption centred at 3260 cm−1 resulted from the O-H bending vibrations of adsorbed water [62]. Similar absorptions were observed in the spectrum of Fe3O4 prepared using DHBA (Figure 3b). However, the spectrum of Fe3O4 prepared using DHBA showed additional absorptions due to adsorbed DHBA. The absorptions at 1097 and 1122 cm−1 resulted from bending C-H vibrations [63,64]. Similar absorptions were observed in the spectrum of DHBA (Figure 3c). The C-O stretching and bending vibrations [7,64] of DHBA resulted in a broad absorption (Figure 3c) centred around 1245 cm−1 and corresponding absorptions at 1218 and 1270 cm−1 for Fe3O4 prepared using DHBA (Figure 3b), which were not observed in the spectrum of Fe3O4 prepared without DHBA (Figure 3a). FTIR studies also revealed additional peaks related to the C-C vibrations in the range of 1300–1600 cm−1 in the spectrum of Fe3O4 prepared using DHBA (Figure 3b), which were not observed in the spectrum of Fe3O4 prepared without DHBA (Figure 3a). Such peaks, related to C-C stretching of aromatic rings, were observed in the spectrum of pure DHBA (Figure 3c). Electrokinetic measurements showed that the adsorption of anionic DHBA resulted in increasing absolute value of negative zeta potential from −28.9 mV for Fe3O4 prepared without DHBA to −38.7 mV for Fe3O4 prepared using DHBA. Therefore, the results of sedimentation tests, zeta potential measurements, and FTIR spectroscopy indicated that DHBA adsorbed on Fe3O4 and facilitated the formation of suspensions with improved colloidal stability.
In this investigation, MWCNT were used as a conductive additive for the fabrication of composite Fe3O4-MWCNT electrodes with enhanced electronic conductivity. Figure 4 presents experimental results for the CV analysis of the Fe3O4-MWCNT composite electrodes. Electrodes were fabricated with synthesized Fe3O4 and MWCNT in the presence of DHBA, BA, and no dispersing agent to investigate the impact of a dispersant on capacitive behaviour. Electrodes prepared using DHBA showed significant improvement in capacitance at scan rates 2–50 mV s−1. The role of the phenolic OH groups of DHBA is evident when comparing CVs and obtained capacitances of electrodes fabricated with DHBA and BA as dispersants. The capacitance of 4.59 F cm−2 for DHBA at 2 mV s−1 scan rate represents significant improvement, compared to the 2.38 F cm−2 and 2.80 F cm−2 obtained when using no dispersing agent and BA dispersant, respectively. The slightly lower capacitance of electrodes prepared using DHBA at a high scan rate of 100 mV s−1 can be attributed to the insulating properties of adsorbed DHBA, which affect the capacitance at such high scan rate.
Figure 5 compares the galvanostatic charge–discharge curves (A–C) for different electrodes, with corresponding capacitances (D) calculated from the discharge data at different current densities. GCD was performed in a voltage window of −0.8–0 V vs. SCE. Nearly symmetrical and triangular charge–discharge curves are seen, confirming the pseudocapacitive behaviour. Electrodes prepared with DHBA showed significant increase in discharge time and significant improvement in capacitance when compared to electrodes prepared using BA or no dispersant. A capacitance of 4.72 F cm−2 was obtained for electrodes made with DHBA at a current density of 3 mA cm−2 and decreased to 3.16 F cm−2 with increasing current density. This capacitance shows significant improvement compared to the capacitances of 2.76 F cm−2 and 2.37 F cm−2 obtained for the electrodes prepared with BA as a dispersing agent and no dispersing agent, respectively, at the current density of 3 mA cm−2. It should be noted that capacitance decreases with increasing charge–discharge time. The difference in the capacitance values obtained using CV and GCD data can result from the different time scale ranges used in both experiments. The Coulombic efficiency at 3 mA cm−2 was 98.0%; it decreased with current density to the value of 97.7% at a current density of 40 mA cm−2. The electrodes prepared using DHBA showed significantly higher capacitance, compared to electrodes prepared with BA and without dispersant in the current density range of 3–40 mA cm−2. The high areal capacitance obtained in this investigation for negative electrodes is important for the development of asymmetric devices operating in Na2SO4 electrolyte [55,56]. The obtained capacitance is higher than the capacitance of carbon electrodes of the same mass operating in the negative potential range [54]. It is comparable with capacitance of advanced positive electrodes [55,56]. It should be noted that catechol exhibits redox active properties in a positive potential range [25,65]. Specifically, the redox activity is associated with the transition of phenolic groups of DHBA to a quinone-like structure [66,67]. In this investigation, a catecholate type DHBA dispersant was used for the fabrication of negative electrodes. Therefore, redox reaction contribution of this dispersant to the to the electrode capacitance in the negative potential range is not expected. However, adsorbed catecholate molecules can facilitate charge transfer [21,35,36].
The analysis of impedance data provides evidence of improved performance of the electrode fabricated using DHBA as a dispersing agent. Figure 6A shows significant increase in the low frequency capacitance (Cs′) for the electrode fabricated with DHBA as a dispersing agent compared to the electrodes where BA and no dispersing agent was used. The analysis of frequency dependences of CS″ shows an increase in the relaxation frequency for both electrodes prepared using DHBA and BA compared to the electrode prepared with no dispersing agent (Figure 6B). The Nyquist plot, presented in Figure 6C, shows relatively low real part of impedance (Z′), indicating low resistance. Furthermore, the large slope shown in the Z″ vs. Z′ curves indicate good capacitive behaviour. Modelling of impedance spectroscopy data using equivalent circuits is an important strategy for the analysis of supercapacitor electrodes [68]. In this investigation, an equivalent circuit developed for high active mass bulk electrodes [69] was used. The simulation results presented in Figure 6D showed good agreement with experimental data and indicated that the electrodes exhibited low charge transfer resistance (RT), which was found to be 0.08 Ohm.
Fe3O4 is a promising negative electrode material for the development of asymmetric supercapacitors [52] with enlarged voltage window for operation in mild electrolytes, such as K2SO4 or Na2SO4. However, the lower specific capacitance of the negative electrodes [52], compared to the capacitance of positive electrodes, limits the development of such devices. Another difficulty is related to significant decrease in specific capacitance with increasing active mass [70]. However, high active mass loading is necessary for practical applications.
The approach developed in this investigation allowed for improved utilization of capacitive properties of Fe3O4. Despite the high active mass of 40 mg cm−2, the capacitance of 114.8 F g−1 (4.59 F cm−2) was obtained from the CV data, which is higher than the reported capacitance [52] of 75 F g−1 at active mass of 8.8 mg cm−2.

2.2. DFT Modeling of Adsorption on Fe3O4 (001) Surface

Next, we performed DFT modelling of adsorption of molecules studied experimentally at the surface of Fe3O4. For this purpose, we established the most stable surface of Fe3O4 and its reconstruction. Relaxation of a bulk cubic Fe3O4 unit cell was conducted. The corresponding lattice parameter, bond lengths, and magnetic moments were in good agreement with values obtained in a prior DFT+U Fe3O4 study [71] and the experimental values found in literature. Table 1 summarizes these results, where differences between the two DFT studies may be attributed to the selection of a slightly different value for Ueff, as well as the Van der Waals interaction, accounted for in our work but not in the prior study [71].
For the purposes of this study, adsorption investigations were performed exclusively on the (001) surface of the Fe3O4 crystal. The abundance of the (001) surface on Fe3O4 nanoparticles has been confirmed experimentally [74]. The Fe3O4 nanoparticle surface was modelled as a slab of 2 × 2 R 45 ∘ supercell of bulk cubic magnetite. The exact structure of (001) surface of magnetite is a delicate topic [75,76], sensitive to the chemical potential of species involved. We selected a stochiometric surface terminated with tetrahedrally coordinated Fe atoms (Fetet), which is in line with previous computational studies [77,78,79] that identified this (001) surface and its termination as the most energetically favourable.
Slabs of varying thicknesses (9, 15, and 23 layers) separated from its periodic image by a 25 Å vacuum layer were constructed to test for convergence of the surface energy (Figure 7). The resulting slabs were constrained by fixing the positions of the middle three layers of atoms at their relaxed bulk positions (the region enclosed by dashed lines in Figure 7) to simulate the bulk phase of Fe3O4, while the remaining outer layers of atoms were allowed to relax during optimization to simulate the surface reconstruction. The surface energy was calculated as
γ = E s l a b - N E b u l k 2 A
where Eslab is the total energy of the constructed surface slab, N is the equivalent number of Fe3O4 formula units in the slab, Ebulk is the total energy per formula unit of the bulk Fe3O4, and A is the area of the surface slab. The calculated surface energies were compared to the surface energy found in a prior DFT study of Fe3O4 (001) surface [79]. These results can be seen in Table 2, where surface energy and Fe-O bond length are compared.
The bond length converges quickly as a function of the number of layers, while the surface energy converges very slowly. Due to computational constraints, we selected the 9-layer surface to investigate the physicochemical nature of the catechol adhesion. Figure 7 shows the final 9-layer force relaxed surface of which DHBA and BA adsorption will be modelled using DFT. One can see that the tetrahedrally coordinated Fe atoms on the top and bottom of the surface (shown by arrows) moved towards the bulk during relaxation, which is in agreement with literature [77].

2.3. DFT Analysis of DHBA and BA Adsorption at the (001) Surface

Previous adsorption studies [79,80,81] of single adatoms and water molecules on the surface of Fe3O4 have found favourable adsorption sites and have reported adsorption energies for the various species. Ni adatoms were found to adsorb favourably onto the (001) surface and reported an adsorption enthalpy of −3.21 eV [79]. This study also reported the incorporation of Ni and Ti into the subsurface by replacing Fe tetrahedral and octahedral sites, respectively. Incorporation energies of −3.39 eV for the Ni and −8.29 eV for the Ti were reported [79]. Gargallo-Caballero et al. [76] reported co-adatom adsorption as well as incorporation at octahedral/tetrahedral sites with energies of the order of –5.5 eV for the magnetite (001) surface. Additionally, adsorption enthalpies of −0.76 eV for H2O molecules adsorbing to surface Fetet atoms and −0.85 eV for single H atoms adsorbing to surface O atoms were reported [80,81]. For adsorption of DHBA onto the Fe3O4 surface, bonding to both tetrahedrally and octahedrally coordinated Fe atoms were considered, in a manner that maintained coordination seen in the bulk crystal.
Adsorption of DHBA is modelled on the (001) surface in four different configurations, seen in Figure 8. Two H atoms are cleaved from phenolic OH groups, in the case of Figure 8A,B,D, and are accommodated on surface O atoms. In the cases where the carboxyl group is responsible for adsorption (Figure 8C and Figure 9A), only one H atom is cleaved and accommodated by Fe3O4 forming a surface OH group. Adsorption strength of molecules to the surface of Fe3O4 is evaluated by the calculation of an adsorption enthalpy (Hads), which represents the difference between the total energy (Etot) of the adsorbed and nonadsorbed states
H a d s = E t o t a d s o r b e d - E t o t n o n a d s o r b e d
The nonadsorbed state is modelled as the surface slab with the respective molecule in a fixed, nonadsorbed state 10 Å above the surface in the vacuum layer. The calculated adsorption enthalpies are shown within Figure 8. The DFT study reveals that the three adsorbed configurations are energetically favourable, while the Fetet-detached configuration (Figure 8D) is not. Figure 8A,C,D include adsorption of DHBA to a surface Fetet atom where Figure 8B captures adsorption of DHBA to two surface octahedrally coordinated Fe atoms (Feoct). The chelating bidentate configuration is the most energetically favourable, closely followed by the bridging bidentate; the carboxyl bidentate configuration is the least favourable. These trends can be explained by examining the resulting bond angles. In the case of the chelating bidentate adsorption of DHBA via phenolic OH groups (Figure 8A), the Fetet atom is pulled away from the surface. This causes the bond angle between the surface Fetet atom and the surface O atom to change from 157.26° to 103.79°, seen in Figure 9A, returning the bond angle to a value much closer to what occurs in the bulk crystal (109.47°). This configuration also forms a bond angle with O atoms in the DHBA molecule of 94.64° (Figure 9B).
In the case where DHBA is adsorbed via carboxyl group, we again see the bond angles changing, this time to 115.45° between the surface O and Fetet and 69.40° between the O atoms in the carboxyl group and Fetet, shown in Figure 9C,D, respectively. This less drastic change in the bond angle towards what is seen in the bulk crystal may contribute to the less favourable adsorption energy seen when adsorption occurs via the carboxyl group. Another consideration is that less energy may be required during the cleaving/adsorption process of the H atom in one of the phenolic OH groups (Figure 8A) compared to breaking the double bonded O in the carboxyl group (Figure 8C) to bond to the Fetet atom. We see similar changes in bond angle for adsorption via carboxyl group for BA to that of adsorption via carboxyl group for DHBA, this time changing to 114.33° in the case of Figure 9C and to 65.12° in the case of Figure 9D. This further explains the results seen experimentally, describing the role of phenolic OH groups for adsorption onto the Fe3O4 surface. In all configurations, the DHBA adsorption restores the coordination of the metal ions involved in bonding.
Two different configurations of BA on the surface of Fe3O4 can be seen in Figure 10. In the chelating bidentate configuration (Figure 10A) adsorption energy is similar to that of the chelating bidentate adsorption via carboxyl group seen with DHBA (Figure 8C). In both cases where the carboxyl group is responsible for adsorption, the adsorption energy is much less than that of the chelating bidentate adsorption via phenolic OH groups. Figure 10B shows the optimized position of BA when it is positioned above the surface so that the H atoms point toward the surface. We can see that in this case adsorption is very weak. To explain the clear difference seen in the experimental results, where dispersion and capacitive properties are greatly improved with the use of DHBA, and the use of BA compares similarly to no dispersing agent at all; it is the electrostatic repulsion that must differ and not adsorption. For DHBA, adsorption utilizing the two adjacent OH groups results in the most energetically favourable adsorption configuration. Then, the carboxyl group is available to facilitate the electrostatic repulsion needed for good dispersion. However, in the case of BA, where the carboxyl functional group is involved in adsorption to the surface, there are no functional groups to provide the charge essential for electrostatic repulsion.
During the modelling of adsorption of both DHBA and BA, the presence of a solvent was neglected. Since the synthesis of Fe3O4 was conducted in a water medium, we would expect adsorption energies to reduce by approximately a factor of two [82] without changing trends. Thus, the presence of a solvent in our calculations would not affect the main conclusions, since we are interested in the trend of adsorption energy across different configurations and molecules, and not in the magnitude of adsorption energy seen.

3. Materials and Methods

3.1. Materials and Experimental Methods

Iron (II) chloride tetrahydrate, iron (III) chloride hexahydrate, ammonium hydroxide, 3,4-dihydroxybenzoic acid, benzoic acid, poly (vinyl butyral-co-vinyl alcohol-co-vinyl acetate) (PVB, MilliporeSigma, Canada), multiwalled carbon nanotubes (MWCNT, ID 4 nm, OD 13 nm, length 1–2 μm, Bayer, Leverkusen, Germany), and nickel foam (porosity 95%, thickness 1.6 mm, Vale, Toronto, ON, Canada), were used as starting materials.
Synthesis of Fe3O4 was performed by a chemical precipitation method [41,53] using aqueous solutions of iron (II) chloride and iron (III) chloride. The molar ratio of FeCl2 to FeCl3 in the solutions was 1:2. A similar procedure was carried with DHBA to analyse the influence of DHBA on the electrode performance, as well as with BA to gain insight into the dispersion and adsorption mechanisms involved. For the synthesis of Fe3O4 in the presence of MWCNT, a 3 g L−1 MWCNT suspension, containing 1.5 g L−1 DHBA or BA, was initially prepared. Preparation included ultrasonication of the MWCNT suspensions using a high energy Cole-Parmer (VCX 500, Cole-Parmer, Quebec City, QC, Canada) ultrasonic processor. Iron (II) chloride tetrahydrate and iron (III) chloride hexahydrate were added to the suspension, allowing for an Fe3O4:MWCNT mass ratio of 4:1. The pH of the solutions was adjusted to pH = 9 by ammonium hydroxide. Chemical precipitation was performed at 50 °C at continuous stirring. Obtained suspensions were filtrated, washed to remove non-adsorbed dispersant and reaction by-products, and dried overnight in an oven at 60 °C.
Electrodes were prepared by impregnation of Ni foam current collectors with slurries, containing Fe3O4, MWCNT and PVB binder. The mass ratio of Fe3O4:MWCNT:PVB was 80:20:3. The mass of the impregnated material after drying was 40 mg cm−2. The impregnated Ni foams were pressed to 30% of their original thickness in order to improve electrical contact of the impregnated material and current collector.
A Bruker Vertex 70 spectrometer (Bruker, Milton, ON, Canada) was used for the Fourier Transform Infrared Spectroscopy (FTIR) experiments. Zeta potential measurements were performed using a dynamic light scattering instrument (DelsaMax Pro: Beckman Coulter, Brea, CA, USA). Electrochemical studies were performed in aqueous 0.5 M Na2SO4 electrolyte using PARSTAT 2273 potentiostat (AMETEK, Berwyn, PA, USA) for cyclic voltammetry (CV) and electrochemical impedance spectroscopy (EIS). Galvanostatic charge–discharge (GCD) investigations were performed using Biologic VMP 300 potentiostat (BioLogic, Seyssinet-Pariset, France). Testing was performed using a 3-electrode electrochemical cell containing a working (impregnated Ni foam), counter-electrode (Pt mesh, MiliporeSigma, Oakville, ON, Canada), and a reference electrode(SCE, saturated calomel electrode, AMETEK, Berwyn, PA, USA). Mass and area normalized capacitances were calculated from the corresponding CV and GCD data, as described by previous studies [83,84]. The capacitances calculated from the CV and GCD data represented integral capacitances measured in a potential window of −0.8–0 V versus SCE. The capacitances calculated from the EIS data represented differential capacitances measured at an open circuit potential at voltage amplitude of 5 mV. CV results were obtained at 2, 5, 10, 20, 50, and 100 mV s−1 scan rates with EIS measurements performed afterwards. GCD results were obtained at 3, 5, 7, 10, 20, 30, and 40 mA cm−2 current densities.

3.2. Computational

The first-principles electronic structure calculations were performed in the framework of DFT [57] using Perdew–Burke–Ernzerhof (PBE) generalized gradient approximation [85] for the exchange correlation functional, augmented by the DFT-D3 correction with Becke–Johnson damping [86,87] to capture van der Waals interactions. The Vienna ab initio simulation program (VASP) (version 5.4.4, University of Vienna, Vienna, Austria) [88,89,90] and projector augmented-wave potentials [91] were used, where the p semi-core states were treated as valence states for Fe potentials in all calculations. Standard potentials were used for all other elements. The cut-off energy for a plane wave expansion of 500 eV was used for the relaxation of the bulk and surface structures to achieve an accurate stress tensor, and the cut-off energy of 400 eV was used in the case of adsorption calculations. During bulk relaxation, atomic position, cell shape, and cell volume were relaxed, whereas only atomic positions were relaxed during the surface and adsorption calculations. We included on-site Coulomb interaction to treat the highly correlated Fe 3d-electrons in the framework of Dudarev et al. [92] using an effective Hubbard energy of U = 3.7 eV [79]. Collinear spin-polarized calculations were performed for all structures. Magnetic moments were initialized with opposing spin orientations of magnitude 4.0 µB for tetrahedrally and octahedrally coordinated Fe atoms [93]. Full self-consistent structural optimization was performed for the bulk, while only forces were relaxed for surface models of Fe3O4 with additional constrains (see Section 2.2 for more details). The structure was considered as optimized when the magnitude of Hellmann–Feynman forces acting on atoms dropped below 50 meV/Å and components of the stress tensor did not exceed 1 kbar. The ground-state energy was calculated using first order Methfessel–Paxton smearing with a width of 0.02 eV. A blocked-Davidson algorithm with high precision is used during the relaxation of the bulk and surface Fe3O4 structures. The Brillouin zone was sampled with a Γ-centered k-mesh generated automatically with a linear density of 15 divisions per 1 Å−1 of the reciprocal space. Adsorption calculations utilize a preconditioned conjugate gradient with normal precision and automatic Γ-centered k-mesh with 30 divisions per 1 Å−1. Construction of the Fe3O4 (001) surfaces is discussed in the results and discussions section. All structure files and VASP input files used in this work can be found in the Supporting Information section. Structure files can be visualized in VESTA [94].

4. Conclusions

We have investigated the role DHBA has on the electrochemical performance of composite Fe3O4-MWCNT anode material for use in supercapacitors. DHBA’s exceptional adsorption and dispersing properties, utilized during synthesis of Fe3O4, contribute to the significant increase in capacitance at low values of impedance. With a mass loading of 40 mg cm−2, a capacitance of 4.59 F cm−2 was obtained from CV data at a scan rate of 2 mV s−1 and 4.72 F cm−2 from GCD data at a current density of 3 mA cm−2. DFT surface and adsorption study of DHBA and BA on the Fe3O4 (001) surface sheds light on the adsorption and dispersion mechanisms seen experimentally. The largest magnitudes of adsorption enthalpies, −1.8 and −1.7 eV, are seen for DHBA chelating bidentate and DHBA bridging bidentate configurations, respectively. Lower adsorption enthalpies were calculated for adsorption of DHBA and BA via bidentate bonding of the carboxyl group, where we see comparable adsorption enthalpies of −1.2 and −1.3 eV, respectively. One can therefore conclude that, due to favourable and comparable adsorption enthalpies of DHBA and BA utilizing a carboxyl functional group, the difference in dispersion and electrochemical performance seen when comparing these two molecules as dispersing agents is dependent on the means of electrostatic repulsion. We see that the more favourable adsorption configurations for DHBA are those that rely on the phenolic OH groups for adsorption, allowing the carboxyl group to facilitate electrostatic repulsion. The Fe3O4-MWCNT anode obtained with the use of DHBA as a dispersing agent, showing improved electrochemical properties, is favourable in the development of advanced energy storage devices.

Supplementary Materials

The following supporting information can be downloaded at: https://www.mdpi.com/article/10.3390/molecules28041562/s1. This paper is accompanied by a ZIP archive file that contains VASP files (POSCAR) for all structures calculated in the present work. In addition, structure-specific input files (INCAR) as well as KPOINTS files are provided. POSCAR files can be visualized using VESTA [94].

Author Contributions

Conceptualization, C.B., O.R. and I.Z.; methodology, O.R. and I.Z.; software, C.B. and O.R.; validation, C.B., O.R. and I.Z.; formal analysis, C.B., O.R. and I.Z.; investigation, C.B.; resources, O.R. and I.Z.; data curation, C.B.; writing—original draft preparation, C.B., O.R. and I.Z.; writing—review and editing, C.B., O.R. and I.Z.; visualization, C.B.; supervision, O.R. and I.Z; project administration, O.R. and I.Z; funding acquisition, O.R. and I.Z. All authors have read and agreed to the published version of the manuscript.

Funding

This research was funded by the Natural Sciences and Engineering Research Council of Canada and Faculty of Engineering of McMaster University. Calculations were performed using the Compute Canada infrastructure supported by the Canada Foundation for Innovation under John R. Evans Leaders Fund.

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

The data is available in this manuscript and Supplementary information.

Acknowledgments

O.R. is thankful to Peter Blaha (TU Vienna) for insightful discussions on the model of magnetite (001) surface.

Conflicts of Interest

The authors declare no conflict of interest.

Sample Availability

Samples of Fe3O4 are available from the authors.

References

  1. Zhang, T.; Wojtal, P.; Rubel, O.; Zhitomirsky, I. Density functional theory and experimental studies of caffeic acid adsorption on zinc oxide and titanium dioxide nanoparticles. R. Soc. Chem. Adv. 2015, 5, 106877–106885. [Google Scholar] [CrossRef]
  2. Melrose, J. High Performance Marine and Terrestrial Bioadhesives and the Biomedical Applications They Have Inspired. Molecules 2022, 27, 8982. [Google Scholar] [CrossRef] [PubMed]
  3. Forouzandeh, P.; Kumaravel, V.; Pillai, S.C. Electrode Materials for Supercapacitors: A Review of Recent Advances. Catalysts 2020, 10, 969. [Google Scholar] [CrossRef]
  4. Hennig, K.; Meyer, W. Synthesis and Characterization of Catechol-Containing Polyacrylamides with Adhesive Properties. Molecules 2022, 27, 4027. [Google Scholar] [CrossRef]
  5. Ata, M.S.; Liu, Y.; Zhitomirsky, I. A review of new methods of surface chemical modification, dispersion and electrophoretic deposition of metal oxide particles. R. Soc. Chem. Adv. 2014, 4, 22716–22732. [Google Scholar] [CrossRef]
  6. Ahn, B.K. Perspectives on Mussel-Inspired Wet Adhesion. J. Am. Chem. Soc. 2017, 139, 10166–10171. [Google Scholar] [CrossRef]
  7. Jankovic, I.A. Surface Modification of Colloidal TiO2 Nanoparticles with Bidentate Benzene Derivatives. J. Phys. Chem. C 2009, 113, 12645–12652. [Google Scholar] [CrossRef]
  8. Cornard, J.P. Theoretical and Spectroscopic Investigations of a Complex of Al(III) with Caffeic Acid. J. Phys. Chem. A 2004, 108, 4470–4478. [Google Scholar] [CrossRef]
  9. Faure, E.; Falentin-Daudré, C.; Jérôme, C.; Lyskawa, J.; Fournier, D.; Woisel, P.; Detrembleur, C. Catechols as versatile platforms in polymer chemistry. Prog. Polym. Sci. 2013, 38, 236–270. [Google Scholar] [CrossRef]
  10. Clifford, A.; Pang, X.; Zhitomirsky, I. Biomimetically modified chitosan for electrophoretic deposition of composites. Colloids Surf. A Physicochem. Eng. Asp. 2018, 544, 28–34. [Google Scholar] [CrossRef]
  11. Clifford, A.; Lee, B.; Grandfield, K.; Zhitomirsky, I. Biomimetic modification of poly-L-lysine and electrodeposition of nanocomposite coatings for orthopaedic applications. Colloids Surf. B Biointerfaces 2019, 176, 115–121. [Google Scholar] [CrossRef] [PubMed]
  12. Sikkema, R.; Baker, K.; Zhitomirsky, I. Electrophoretic deposition of polymers and proteins for biomedical applications. Adv. Colloid Interface Sci. 2020, 284, 102272. [Google Scholar] [CrossRef] [PubMed]
  13. Wu, K.; Wang, Y.; Zhitomirsky, I. Electrophoretic deposition of TiO2 and composite TiO2–MnO2 films using benzoic acid and phenolic molecules as charging additives. J. Colloid Interface Sci. 2010, 352, 371–378. [Google Scholar] [CrossRef] [PubMed]
  14. Zhao, Q.; Zhitomirsky, I. Biomimetic strategy for electrophoretic deposition of composite ferroelectric poly(vinylidene, fluoride-co-hexafluoropropylene)—Ferrimagnetic NiFe2O4 films. Colloids Surf. A Physicochem. Eng. Asp. 2022, 651, 129743. [Google Scholar] [CrossRef]
  15. Silva, R.M.E.; Poon, R.; Milne, J.; Syed, A.; Zhitomirsky, I. New developments in liquid-liquid extraction, surface modification and agglomerate-free processing of inorganic particles. Adv. Colloid Interface Sci. 2018, 261, 15–27. [Google Scholar] [CrossRef]
  16. Milne, J.; Marques Silva, R.; Zhitomirsky, I. Surface modification and dispersion of ceramic particles using liquid-liquid extraction method for application in supercapacitor electrodes. J. Eur. Ceram. Soc. 2019, 39, 3450–3455. [Google Scholar] [CrossRef]
  17. Mowbray, D.J.; Migani, A. Optical Absorption Spectra and Excitons of Dye-Substrate Interfaces: Catechol on TiO2(110). J. Chem. Theory Comput. 2016, 12, 2843–2852. [Google Scholar] [CrossRef]
  18. Sakib, S.; Pandey, R.; Soleymani, L.; Zhitomirsky, I. Surface modification of TiO2 for photoelectrochemical DNA biosensors. Med. Devices Sens. 2020, 3, e10066. [Google Scholar] [CrossRef]
  19. Savin, R.; Blanck, C.; Benzaamia, N.-O.; Boulmedais, F. Optimization of Nanohybrid Biosensors Based on Electro-Crosslinked Tannic Acid Capped Nanoparticles/Enzyme. Molecules 2022, 27, 3309. [Google Scholar] [CrossRef]
  20. Pinto, A.L.; Cruz, L.; Gomes, V.; Cruz, H.; Calogero, G.; de Freitas, V.; Pina, F.; Parola, A.J.; Carlos Lima, J. Catechol versus carboxyl linkage impact on DSSC performance of synthetic pyranoflavylium salts. Dye. Pigment. 2019, 170, 107577. [Google Scholar] [CrossRef]
  21. Yan, K.; Liu, Y.; Guan, Y.; Bhokisham, N.; Tsao, C.Y.; Kim, E.; Shi, X.W.; Wang, Q.; Bentley, W.E.; Payne, G.F. Catechol-chitosan redox capacitor for added amplification in electrochemical immunoanalysis. Colloids Surf. B Biointerfaces 2018, 169, 470–477. [Google Scholar] [CrossRef] [PubMed]
  22. Wu, S.; Kim, E.; Li, J.; Bentley, W.E.; Shi, X.-W.; Payne, G.F. Catechol-based capacitor for redox-linked bioelectronics. J. Am. Chem. Soc. Appl. Electron. Mater. 2019, 1, 1337–1347. [Google Scholar] [CrossRef] [PubMed]
  23. Segoviano-Garfias, J.J.N.; Zanor, G.A.; Ávila-Ramos, F.; Bivián-Castro, E.Y. Equilibrium Studies of Iron (III) Complexes with Either Pyrazine, Quinoxaline, or Phenazine and Their Catecholase Activity in Methanol. Molecules 2022, 27, 3257. [Google Scholar] [CrossRef] [PubMed]
  24. Touzé, E.; Gohier, F.; Daffos, B.; Taberna, P.-L.; Cougnon, C. Improvement of electrochemical performances of catechol-based supercapacitor electrodes by tuning the redox potential via different-sized O-protected catechol diazonium salts. Electrochim. Acta 2018, 265, 121–130. [Google Scholar] [CrossRef]
  25. Jokar, E.; Shahrokhian, S. Electrochemical functionalization of graphene nanosheets with catechol derivatives as an effective method for preparation of highly performance supercapacitors. Electrochim. Acta 2014, 147, 136–142. [Google Scholar] [CrossRef]
  26. Malka, D.; Giladi, S.; Hanna, O.; Weitman, M.; Cohen, R.; Elias, Y.; Attias, R.; Brousse, T.; Frimer, A.A.; Aurbach, D. Catechol-Modified Carbon Cloth as Hybrid Electrode for Energy Storage Devices. J. Electrochem. Soc. 2019, 166, A1147–A1153. [Google Scholar] [CrossRef]
  27. Pourghobadi, R.; Nematollahi, D.; Baezzat, M.R.; Alizadeh, S.; Goljani, H. Electropolymerization of catechol on wireless graphite electrode. Unusual cathodic polycatechol formation. J. Electroanal. Chem. 2020, 866, 114180. [Google Scholar] [CrossRef]
  28. Beiginejad, H.; Nematollahi, D.; Bayat, M.; Varmaghani, F.; Nazaripour, A. Experimental and Theoretical Analysis of the Electrochemical Oxidation of Catechol and Hydroquinone Derivatives in the Presence of Various Nucleophiles. J. Electrochem. Soc. 2013, 160, H693–H698. [Google Scholar] [CrossRef]
  29. Sadaba, N.; Salsamendi, M.; Casado, N.; Zuza, E.; Munoz, J.; Sarasua, J.R.; Mecerreyes, D.; Mantione, D.; Detrembleur, C.; Sardon, H. Catechol End-Functionalized Polylactide by Organocatalyzed Ring-Opening Polymerization. Polymers 2018, 10, 155. [Google Scholar] [CrossRef]
  30. Barham, A.S.; Kennedy, B.M.; Cunnane, V.J.; Daous, M.A. The Electrochemical polymerisation of 1,2 dihydroxybenzene and 2-hydroxybenzyl alcohol prepared in different solutions media. Electrochim. Acta 2014, 147, 19–24. [Google Scholar] [CrossRef]
  31. Su, J.; Chen, F.; Cryns, V.L.; Messersmith, P.B. Catechol polymers for pH-responsive, targeted drug delivery to cancer cells. J. Am. Chem. Soc. 2011, 133, 11850–11853. [Google Scholar] [CrossRef] [PubMed]
  32. Razaviamri, S.; Wang, K.; Liu, B.; Lee, B.P. Catechol-Based Antimicrobial Polymers. Molecules 2021, 26, 559. [Google Scholar] [CrossRef] [PubMed]
  33. Kim, J.; Lee, C.; Ryu, J.H. Adhesive Catechol-Conjugated Hyaluronic Acid for Biomedical Applications: A Mini Review. Appl. Sci. 2020, 11, 21. [Google Scholar] [CrossRef]
  34. Nawwar, M.; Sahu, R.P.; Puri, I.K.; Zhitomirsky, I. Pseudocapacitive behavior of ferrimagnetic NiFe2O4-carbon nanotube electrodes prepared with a multifunctional dispersing agent. Open Ceram. 2021, 6, 100127. [Google Scholar] [CrossRef]
  35. Tallman, D.; Vang, C.; Wallace, G.; Bierwagen, G. Direct electrodeposition of polypyrrole on aluminum and aluminum alloy by electron transfer mediation. J. Electrochem. Soc. 2002, 149, C173. [Google Scholar] [CrossRef]
  36. Shi, C.; Zhitomirsky, I. Electrodeposition of composite polypyrrole–carbon nanotube films. Surf. Eng. 2011, 27, 655–661. [Google Scholar] [CrossRef]
  37. Shi, C.; Zhitomirsky, I. Electrodeposition and Capacitive Behavior of Films for Electrodes of Electrochemical Supercapacitors. Nanoscale Res. Lett. 2010, 5, 518. [Google Scholar] [CrossRef]
  38. Nagesha, D.K.; Plouffe, B.D.; Phan, M.; Lewis, L.H.; Sridhar, S.; Murthy, S.K. Functionalization-induced improvement in magnetic properties of Fe3O4 nanoparticles for biomedical applications. J. Appl. Phys. 2009, 105, 07B317. [Google Scholar] [CrossRef]
  39. Huang, W.; Jiang, P.; Wei, C.; Zhuang, D.; Shi, J. Low-temperature one-step synthesis of covalently chelated ZnO/dopamine hybrid nanoparticles and their optical properties. J. Mater. Res. 2008, 23, 1946–1952. [Google Scholar] [CrossRef]
  40. Bloemen, M.; Debruyne, D.; Demeyer, P.-J.; Clays, K.; Gils, A.; Geukens, N.; Bartic, C.; Verbiest, T. Catechols as ligands for CdSe–ZnS quantum dots. R. Soc. Chem. Adv. 2014, 4, 10208–10211. [Google Scholar] [CrossRef]
  41. Nawwar, M.; Poon, R.; Sahu, R.P.; Puri, I.K.; Zhitomirsky, I. Fe3O4 spinel-Mn3O4 spinel supercapacitor prepared using Celestine blue as a dispersant, capping agent and charge transfer mediator. Ceram. Int. 2020, 46, 18851–18858. [Google Scholar] [CrossRef]
  42. Togashi, T.; Takami, S.; Kawakami, K.; Yamamoto, H.; Naka, T.; Sato, K.; Abe, K.; Adschiri, T. Continuous hydrothermal synthesis of 3,4-dihydroxyhydrocinnamic acid-modified magnetite nanoparticles with stealth-functionality against immunological response. J. Mater. Chem. 2012, 22, 9041–9045. [Google Scholar] [CrossRef]
  43. Sugimoto, T.; Itoh, H.; Mochida, T. Shape control of monodisperse hematite particles by organic additives in the gel–sol system. J. Colloid Interface Sci. 1998, 205, 42–52. [Google Scholar] [CrossRef] [PubMed]
  44. Hori, M.; Pagnoux, C.; Baumard, J.-F.; Nogami, M. Preparation of gold nanoparticles (GNP) aqueous suspensions by a new method involving Tiron. J. Mater. Sci. 2007, 42, 80–86. [Google Scholar] [CrossRef]
  45. Huang, X.; Pang, Y.; Liu, Y.; Zhou, Y.; Wang, Z.; Hu, Q. Green synthesis of silver nanoparticles with high antimicrobial activity and low cytotoxicity using catechol-conjugated chitosan. R. Soc. Chem. Adv. 2016, 6, 64357–64363. [Google Scholar] [CrossRef]
  46. Zhang, L.; Wu, D.; Yan, X. Applications of magnetic field for electrochemical energy storage. Appl. Phys. Rev. 2022, 9, 031307. [Google Scholar] [CrossRef]
  47. Venevtsev, Y.N.; Gagulin, V.; Zhitomirsky, I. Material science aspects of seignette-magnetism problem. Ferroelectrics 1987, 73, 221–248. [Google Scholar] [CrossRef]
  48. Poudel, M.B.; Kim, H.J. Confinement of Zn-Mg-Al-layered double hydroxide and α-Fe2O3 nanorods on hollow porous carbon nanofibers: A free-standing electrode for solid-state symmetric supercapacitors. Chem. Eng. J. 2022, 429, 132345. [Google Scholar] [CrossRef]
  49. Malaie, K.; Ganjali, M.R. Spinel nano-ferrites for aqueous supercapacitors; linking abundant resources and low-cost processes for sustainable energy storage. J. Energy Storage 2021, 33, 102097. [Google Scholar] [CrossRef]
  50. Ghasemi, S.; Ahmadi, F. Effect of surfactant on the electrochemical performance of graphene/iron oxide electrode for supercapacitor. J. Power Sources 2015, 289, 129–137. [Google Scholar] [CrossRef]
  51. Li, X.; Zhang, L.; He, G. Fe3O4 doped double-shelled hollow carbon spheres with hierarchical pore network for durable high-performance supercapacitor. Carbon 2016, 99, 514–522. [Google Scholar] [CrossRef]
  52. Brousse, T.; Bélanger, D. A hybrid Fe3O4 MnO2 capacitor in mild aqueous electrolyte. Electrochem. Solid-State Lett. 2003, 6, A244. [Google Scholar] [CrossRef]
  53. Nawwar, M.; Poon, R.; Chen, R.; Sahu, R.P.; Puri, I.K.; Zhitomirsky, I. High areal capacitance of Fe3O4-decorated carbon nanotubes for supercapacitor electrodes. Carbon Energy 2019, 1, 124–133. [Google Scholar] [CrossRef]
  54. Chen, R.; Yu, M.; Sahu, R.P.; Puri, I.K.; Zhitomirsky, I. The development of pseudocapacitor electrodes and devices with high active mass loading. Adv. Energy Mater. 2020, 10, 1903848. [Google Scholar] [CrossRef]
  55. Wickramaarachchi, K.; Minakshi, M. Status on electrodeposited manganese dioxide and biowaste carbon for hybrid capacitors: The case of high-quality oxide composites, mechanisms, and prospects. J. Energy Storage 2022, 56, 106099. [Google Scholar] [CrossRef]
  56. Wickramaarachchi, K.; Minakshi, M. Consequences of electrodeposition parameters on the microstructure and electrochemical behavior of electrolytic manganese dioxide (EMD) for supercapacitor. Ceram. Int. 2022, 48, 19913–19924. [Google Scholar] [CrossRef]
  57. Kohn, W.; Sham, L.J. Self-Consistent Equations Including Exchange and Correlation Effects. Phys. Rev. 1965, 140, A1133–A1138. [Google Scholar] [CrossRef]
  58. Wang, L.; Ji, H.; Wang, S.; Kong, L.; Jiang, X.; Yang, G. Preparation of Fe3O4 with high specific surface area and improved capacitance as a supercapacitor. Nanoscale 2013, 5, 3793–3799. [Google Scholar] [CrossRef]
  59. Saikia, N.; Sarma, J.; Borah, J.M.; Mahiuddin, S. Adsorption of 3,4-dihydroxybenzoic acid onto hematite surface in aqueous medium: Importance of position of phenolic -OH groups and understanding of the same using catechol as an auxiliary model. J. Colloid Interface Sci. 2013, 398, 227–233. [Google Scholar] [CrossRef]
  60. Borah, J.M.; Sarma, J.; Mahiuddin, S. Adsorption comparison at the α-alumina/water interface: 3,4-Dihydroxybenzoic acid vs. catechol. Colloids Surf. A Physicochem. Eng. Asp. 2011, 387, 50–56. [Google Scholar] [CrossRef]
  61. Parks, G.A. The Isoelectric Points of Solid Oxides, Solid Hydroxides, and Aqueous Hydroxo Complex Systems. Chem. Rev. 1965, 65, 177–198. [Google Scholar] [CrossRef]
  62. Kamakshi, T.; Sundari, G.S.; Erothu, H.; Singh, R.S. Effect of nickel dopant on structural morphological and optical characteristics of Fe3O4 nanoparticles. Rasayan J. Chem 2019, 12, 531–536. [Google Scholar] [CrossRef]
  63. Dobson, K.D.; McQuillan, A.J. In situ infrared spectroscopic analysis of the adsorption of aromatic carboxylic acids to TiO2, ZrO2, Al2O3, and Ta2O5 from aqueous solutions. Spectrochim. Acta Part A Mol. Biomol. Spectrosc. 2000, 56, 557–565. [Google Scholar] [CrossRef] [PubMed]
  64. Gulley-Stahl, H.; Hogan, P.A.; Schmidt, W.L.; Wall, S.J.; Buhrlage, A.; Bullen, H.A. Surface complexation of catechol to metal oxides: An ATR-FTIR, adsorption, and dissolution study. Environ. Sci. Technol. 2010, 44, 4116–4121. [Google Scholar] [CrossRef] [PubMed]
  65. Choi, J.; Yang, M.; Kim, S.-K. Pseudocapacitive organic catechol derivative-functionalized three-dimensional graphene aerogel hybrid electrodes for high-performance supercapacitors. Appl. Surf. Sci. 2017, 422, 316–320. [Google Scholar] [CrossRef]
  66. Golabi, S.; Nematollahi, D. Electrochemical study of 3,4-dihydroxybenzoic acid and 4-tert-butylcatechol in the presence of 4-hydroxycoumarin application to the electro-organic synthesis of coumestan derivatives. J. Electroanal. Chem. 1997, 430, 141–146. [Google Scholar] [CrossRef]
  67. Litos, C.; Aletras, V.; Hatzipanayioti, D.; Kamariotaki, M.; Lymberopoulou-Karaliota, A. CV and NMR study on the reaction of Mo (VI) with 3, 4-dihydroxybenzoic acid and ascorbic acid in aqueous solution. Inorg. Chim. Acta 2007, 360, 2321–2330. [Google Scholar] [CrossRef]
  68. Poudel, M.B.; Kim, A.R.; Ramakrishan, S.; Logeshwaran, N.; Ramasamy, S.K.; Kim, H.J.; Yoo, D.J. Integrating the essence of metal organic framework-derived ZnCoTe–N–C/MoS2 cathode and ZnCo-NPS-N-CNT as anode for high-energy density hybrid supercapacitors. Compos. Part B Eng. 2022, 247, 110339. [Google Scholar] [CrossRef]
  69. Wang, Y.; Liu, Y.; Zhitomirsky, I. Surface modification of MnO2 and carbon nanotubes using organic dyes for nanotechnology of electrochemical supercapacitors. J. Mater. Chem. A 2013, 1, 12519–12526. [Google Scholar] [CrossRef]
  70. Shi, K.; Zhitomirsky, I. Fabrication of Polypyrrole-Coated Carbon Nanotubes Using Oxidant–Surfactant Nanocrystals for Supercapacitor Electrodes with High Mass Loading and Enhanced Performance. ACS Appl. Mater. Interfaces 2013, 5, 13161–13170. [Google Scholar] [CrossRef]
  71. Noh, J.; Osman, O.I.; Aziz, S.G.; Winget, P.; Bredas, J.L. A density functional theory investigation of the electronic structure and spin moments of magnetite. Sci. Technol. Adv. Mater. 2014, 15, 044202. [Google Scholar] [CrossRef] [PubMed]
  72. Petrov, V.N.; Ustinov, A.B. Magnetic properties of Fe3O4 surface. J. Surf. Investig. X-ray Synchrotron Neutron Tech. 2010, 4, 395–400. [Google Scholar] [CrossRef]
  73. Jain, A.; Ong, S.P.; Hautier, G.; Chen, W.; Richards, W.D.; Dacek, S.; Cholia, S.; Gunter, D.; Skinner, D.; Ceder, G.; et al. Commentary: The Materials Project: A materials genome approach to accelerating materials innovation. APL Mater. 2013, 1, 011002. [Google Scholar] [CrossRef]
  74. Zhao, L.; Zhang, H.; Xing, Y.; Song, S.; Yu, S.; Shi, W.; Guo, X.; Yang, J.; Lei, Y.; Cao, F. Morphology-Controlled Synthesis of Magnetites with Nanoporous Structures and Excellent Magnetic Properties. Chem. Mater. 2007, 20, 198–204. [Google Scholar] [CrossRef]
  75. Bliem, R.; McDermott, E.; Ferstl, P.; Setvin, M.; Gamba, O.; Pavelec, J.; Schneider, M.A.; Schmid, M.; Diebold, U.; Blaha, P.; et al. Subsurface cation vacancy stabilization of the magnetite (001) surface. Science 2014, 346, 1215–1218. [Google Scholar] [CrossRef]
  76. Gargallo-Caballero, R.; Martin-Garcia, L.; Quesada, A.; Granados-Miralles, C.; Foerster, M.; Aballe, L.; Bliem, R.; Parkinson, G.S.; Blaha, P.; Marco, J.F.; et al. Co on Fe3O4(001): Towards precise control of surface properties. J. Chem. Phys. 2016, 144, 094704. [Google Scholar] [CrossRef]
  77. Santos-Carballal, D.; Roldan, A.; Grau-Crespo, R.; de Leeuw, N.H. A DFT study of the structures, stabilities and redox behaviour of the major surfaces of magnetite Fe3O4. R. Soc. Chem. Phys. Chem. Chem. Phys. 2014, 16, 21082–21097. [Google Scholar] [CrossRef]
  78. Yang, T.; Wen, X.-d.; Ren, J.; Li, Y.-w.; Wang, J.-g.; Huo, C.-f. Surface structures of Fe3O4 (111), (110), and (001): A density functional theory study. J. Fuel Chem. Technol. 2010, 38, 121–128. [Google Scholar] [CrossRef]
  79. Bliem, R.; Pavelec, J.; Gamba, O.; McDermott, E.; Wang, Z.; Gerhold, S.; Wagner, M.; Osiecki, J.; Schulte, K.; Schmid, M.; et al. Adsorption and incorporation of transition metals at the magnetite Fe3O4(001) surface. Phys. Rev. B 2015, 92, 075440. [Google Scholar] [CrossRef]
  80. Mulakaluri, N. Coverage-Dependent Adsorption Mode of Water on Fe3O4(001): Insights from First Principles Calculations. J. Phys. Chem. C 2010, 114, 11148–11156. [Google Scholar] [CrossRef]
  81. Mulakaluri, N.; Pentcheva, R. Hydrogen Adsorption and Site-Selective Reduction of the Fe3O4(001) Surface: Insights from First Principles. J. Phys. Chem. C 2012, 116, 16447–16453. [Google Scholar] [CrossRef]
  82. Albert, M.; Clifford, A.; Zhitomirsky, I.; Rubel, O. Adsorption of Maleic Acid Monomer on the Surface of Hydroxyapatite and TiO2: A Pathway toward Biomaterial Composites. J. Am. Chem. Soc. Appl. Mater. Interfaces 2018, 10, 24382–24391. [Google Scholar] [CrossRef] [PubMed]
  83. Shi, K.; Zhitomirsky, I. Electrophoretic nanotechnology of graphene-carbon nanotube and graphene-polypyrrole nanofiber composites for electrochemical supercapacitors. J. Colloid Interface Sci. 2013, 407, 474–481. [Google Scholar] [CrossRef] [PubMed]
  84. Yan, D.; Li, Y.; Liu, Y.; Zhuo, R.; Wu, Z.; Geng, B.; Wang, J.; Ren, P.; Yan, P.; Geng, Z. Hydrothermal synthesis and electrochemical properties of hexagonal hydrohausmannite plates as supercapacitor electrode material. Mater. Lett. 2014, 117, 62–65. [Google Scholar] [CrossRef]
  85. Perdew, J.P.; Burke, K.; Ernzerhof, M. Generalized Gradient Approximation Made Simple. Phys. Rev. Lett. 1996, 77, 3865–3868. [Google Scholar] [CrossRef]
  86. Grimme, S.; Ehrlich, S.; Goerigk, L. Effect of the Damping Function in Dispersion Corrected Density Functional Theory. J. Comput. Chem. 2011, 32, 1456–1465. [Google Scholar] [CrossRef]
  87. Grimme, S.; Antony, J.; Ehrlich, S.; Krieg, H. A consistent and accurate ab initio parametrization of density functional dispersion correction (DFT-D) for the 94 elements H-Pu. J. Chem. Phys. 2010, 132, 154104. [Google Scholar] [CrossRef]
  88. Kresse, G.; Hafner, J. Ab initio molecular dynamics for liquid metals. Phys. Rev. B 1993, 47, 558–561. [Google Scholar] [CrossRef]
  89. Kresse, G.; Furthmüller, J. Efficiency of ab-initio total energy calculations for metals and semiconductors using a plane-wave basis set. Comput. Mater. Sci. 1996, 6, 15–50. [Google Scholar] [CrossRef]
  90. Kresse, G.; Furthmüller, J. Efficient iterative schemes for ab initio total-energy calculations using a plane-wave basis set. Phys. Rev. B 1996, 54, 11169–11186. [Google Scholar] [CrossRef]
  91. Kresse, G.; Joubert, D. From ultrasoft pseudopotentials to the projector augmented-wave method. Phys. Rev. B 1999, 59, 1758–1775. [Google Scholar] [CrossRef]
  92. Dudarev, S.L. Electron-energy-loss spectra and the structural stability of nickel oxide: An LSDA+U study. Phys. Rev. B 1998, 57, 1505–1509. [Google Scholar] [CrossRef]
  93. Chiter, F.; Nguyen, V.B.; Tarrat, N.; Benoit, M.; Tang, H.; Lacaze-Dufaure, C. Effect of van der Waals corrections on DFT-computed metallic surface properties. Mater. Res. Express 2016, 3, 046501. [Google Scholar] [CrossRef]
  94. Momma, K.; Izumi, F. VESTA 3 for three-dimensional visualization of crystal, volumetric and morphology data. J. Appl. Crystallogr. 2011, 44, 1272–1276. [Google Scholar] [CrossRef]
Molecules 28 01562 g001 550
Figure 1. Chemical structure of 3,4-dihydroxybenzoic acid (left) and benzoic acid (right).
Figure 1. Chemical structure of 3,4-dihydroxybenzoic acid (left) and benzoic acid (right).
Molecules 28 01562 g001
Molecules 28 01562 g002 550
Figure 2. Fe3O4 suspension in water with (A) no dispersing agent, (B) BA as a dispersing agent, and (C) DHBA as a dispersing agent 1 h after ultrasonication.
Figure 2. Fe3O4 suspension in water with (A) no dispersing agent, (B) BA as a dispersing agent, and (C) DHBA as a dispersing agent 1 h after ultrasonication.
Molecules 28 01562 g002
Molecules 28 01562 g003 550
Figure 3. FTIR spectra of (a) Fe3O4 prepared without DHBA, (b) Fe3O4 prepared using DHBA, and (c) pure as-received DHBA.
Figure 3. FTIR spectra of (a) Fe3O4 prepared without DHBA, (b) Fe3O4 prepared using DHBA, and (c) pure as-received DHBA.
Molecules 28 01562 g003
Molecules 28 01562 g004 550
Figure 4. (A–C) CVs at scan rates of (a) 20, (b) 5, and (c) 2 mV s−1 for Fe3O4–MWCNT electrodes prepared with (A) DHBA as dispersing agent, (B) BA as dispersing agent, and (C) no dispersing agent. (D) Capacitance vs. scan rate for Fe3O4–MWCNT electrodes prepared with (a) DHBA as dispersing agent, (b) BA as dispersing agent, and (c) no dispersing agent.
Figure 4. (A–C) CVs at scan rates of (a) 20, (b) 5, and (c) 2 mV s−1 for Fe3O4–MWCNT electrodes prepared with (A) DHBA as dispersing agent, (B) BA as dispersing agent, and (C) no dispersing agent. (D) Capacitance vs. scan rate for Fe3O4–MWCNT electrodes prepared with (a) DHBA as dispersing agent, (b) BA as dispersing agent, and (c) no dispersing agent.
Molecules 28 01562 g004
Molecules 28 01562 g005 550
Figure 5. (A–C) charge–discharge curves at current densities of (a) 7 mA cm−2, (b) 5 mA cm−2, and (c) 3 mA cm−2 for Fe3O4–MWCNT electrodes prepared with (A) DHBA as dispersing agent, (B) BA as dispersing agent, and (C) no dispersing agent. (D) Capacitance vs. current density profiles for Fe3O4–MWCNT electrodes prepared with (a) DHBA as dispersing agent, (b) BA as dispersing agent, and (c) no dispersing agent.
Figure 5. (A–C) charge–discharge curves at current densities of (a) 7 mA cm−2, (b) 5 mA cm−2, and (c) 3 mA cm−2 for Fe3O4–MWCNT electrodes prepared with (A) DHBA as dispersing agent, (B) BA as dispersing agent, and (C) no dispersing agent. (D) Capacitance vs. current density profiles for Fe3O4–MWCNT electrodes prepared with (a) DHBA as dispersing agent, (b) BA as dispersing agent, and (c) no dispersing agent.
Molecules 28 01562 g005
Molecules 28 01562 g006 550
Figure 6. (A) Real part of capacitance (Cs′) vs. frequency, (B) imaginary part of capacitance (Cs″) vs. frequency, and (C) Nyquist plot for Fe3O4–MWCNT electrodes prepared with (a) DHBA as dispersing agent, (b) BA as dispersing agent, and (c) no dispersing agent, and (D) modelling of impedance for Fe3O4 electrode prepared using DHBA and corresponding equivalent circuit (inset).
Figure 6. (A) Real part of capacitance (Cs′) vs. frequency, (B) imaginary part of capacitance (Cs″) vs. frequency, and (C) Nyquist plot for Fe3O4–MWCNT electrodes prepared with (a) DHBA as dispersing agent, (b) BA as dispersing agent, and (c) no dispersing agent, and (D) modelling of impedance for Fe3O4 electrode prepared using DHBA and corresponding equivalent circuit (inset).
Molecules 28 01562 g006
Molecules 28 01562 g007 550
Figure 7. The 9-layer (A), 15-layer (B), and 23-layer (C) relaxed surfaces with Hubbard U correction. Dashed rectangle indicates region where atoms within are constrained to their relaxed bulk positions. The arrows point at Fetet atoms in the first surface termination layer.
Figure 7. The 9-layer (A), 15-layer (B), and 23-layer (C) relaxed surfaces with Hubbard U correction. Dashed rectangle indicates region where atoms within are constrained to their relaxed bulk positions. The arrows point at Fetet atoms in the first surface termination layer.
Molecules 28 01562 g007
Molecules 28 01562 g008 550
Figure 8. Adsorption of DHBA on the (001) surface of Fe3O4 in three different configurations, (A) chelating bidentate via phenolic OH groups, (B) bridging bidentate via phenolic OH groups, (C) chelating bidentate via carboxyl group, and (D) scenario where molecule adsorbs and detaches with Fe atom. The adsorption is accompanied by the surface adsorption of H+ ions displaced from OH groups. Values on each panel represent respective adsorption energies.
Figure 8. Adsorption of DHBA on the (001) surface of Fe3O4 in three different configurations, (A) chelating bidentate via phenolic OH groups, (B) bridging bidentate via phenolic OH groups, (C) chelating bidentate via carboxyl group, and (D) scenario where molecule adsorbs and detaches with Fe atom. The adsorption is accompanied by the surface adsorption of H+ ions displaced from OH groups. Values on each panel represent respective adsorption energies.
Molecules 28 01562 g008
Molecules 28 01562 g009 550
Figure 9. Surface Fe bond angles for (A) bottom of DHBA via phenolic OH group adsorption, (B) top of DHBA via phenolic OH group adsorption, (C) bottom of DHBA via carboxyl group adsorption, (D) top of DHBA via carboxyl group adsorption. Values of bond angles in degrees are shown on each panel.
Figure 9. Surface Fe bond angles for (A) bottom of DHBA via phenolic OH group adsorption, (B) top of DHBA via phenolic OH group adsorption, (C) bottom of DHBA via carboxyl group adsorption, (D) top of DHBA via carboxyl group adsorption. Values of bond angles in degrees are shown on each panel.
Molecules 28 01562 g009
Molecules 28 01562 g010 550
Figure 10. Adsorption of BA in two different configurations, (A) chelating bidentate via carboxyl groups, and (B) bonding of H to Fe3O4 surface O atoms. The adsorption can be accompanied by the surface adsorption of H+ ions displaced from OH groups.
Figure 10. Adsorption of BA in two different configurations, (A) chelating bidentate via carboxyl groups, and (B) bonding of H to Fe3O4 surface O atoms. The adsorption can be accompanied by the surface adsorption of H+ ions displaced from OH groups.
Molecules 28 01562 g010
Table
Table 1. Comparison of lattice parameter, O-Fe bond lengths, magnetic moments to previous DFT study of bulk Fe3O4 and experimentally reported values.
Table 1. Comparison of lattice parameter, O-Fe bond lengths, magnetic moments to previous DFT study of bulk Fe3O4 and experimentally reported values.
ParameterLiterature PBE+U [71]This Work PBE+U+D3Experimental
Lattice parameter (Å)8.4888.4538.396 [72]
Bond length (oct) (Å)2.092.072.07 [73]
Bond length (tet) (Å)1.901.911.88 [73]
Magnetic moment (Feoct) (μB)3.963.92-
Magnetic moment (Fetet) (μB)4.094.02-
Magnetic moment (O) (μB)0.0300.045-
Total magnetic moment (μB /f.u.)4.04.04.1 [72]
Table
Table 2. Fe3O4 (001) surface energy and Fe-O bond length of surface tetrahedrally coordinated Fe, for 23-layer, 15-layer, and 9-layer slabs calculated at PBE+U+D3 level of theory and compared to previous surface study using PBE+U.
Table 2. Fe3O4 (001) surface energy and Fe-O bond length of surface tetrahedrally coordinated Fe, for 23-layer, 15-layer, and 9-layer slabs calculated at PBE+U+D3 level of theory and compared to previous surface study using PBE+U.
Surfaces (PBE+U+D3)Surface Energy (J m−2)Surface Fe-O Bond Length (Å)
23 layers0.481.92
15 layers0.731.81
9 layers0.901.90
Literature, 9 layers (PBE+U)0.96 [77]1.89 [78]
Disclaimer/Publisher’s Note: The statements, opinions and data contained in all publications are solely those of the individual author(s) and contributor(s) and not of MDPI and/or the editor(s). MDPI and/or the editor(s) disclaim responsibility for any injury to people or property resulting from any ideas, methods, instructions or products referred to in the content.

Share and Cite

MDPI and ACS Style

Boucher, C.; Rubel, O.; Zhitomirsky, I. Supercapacitor Performance of Magnetite Nanoparticles Enhanced by a Catecholate Dispersant: Experiment and Theory. Molecules 2023, 28, 1562. https://doi.org/10.3390/molecules28041562

AMA Style

Boucher C, Rubel O, Zhitomirsky I. Supercapacitor Performance of Magnetite Nanoparticles Enhanced by a Catecholate Dispersant: Experiment and Theory. Molecules. 2023; 28(4):1562. https://doi.org/10.3390/molecules28041562

Chicago/Turabian Style

Boucher, Coulton, Oleg Rubel, and Igor Zhitomirsky. 2023. "Supercapacitor Performance of Magnetite Nanoparticles Enhanced by a Catecholate Dispersant: Experiment and Theory" Molecules 28, no. 4: 1562. https://doi.org/10.3390/molecules28041562

APA Style

Boucher, C., Rubel, O., & Zhitomirsky, I. (2023). Supercapacitor Performance of Magnetite Nanoparticles Enhanced by a Catecholate Dispersant: Experiment and Theory. Molecules, 28(4), 1562. https://doi.org/10.3390/molecules28041562

Article Metrics

Back to TopTop