Fired brick is a universal building material, produced by thousand-year-old technology, that throughout history has seldom served any other purpose. Here, we develop a scalable, cost-effective and versatile chemical synthesis using a fired brick to control oxidative radical polymerization and deposition of a nanofibrillar coating of the conducting polymer poly(3,4-ethylenedioxythiophene) (PEDOT). A fired brick’s open microstructure, mechanical robustness and ~8 wt% α-Fe2O3 content afford an ideal substrate for developing electrochemical PEDOT electrodes and stationary supercapacitors that readily stack into modules. Five-minute epoxy serves as a waterproof case enabling the operation of our supercapacitors while submerged underwater and a gel electrolyte extends cycling stability to 10,000 cycles with ~90% capacitance retention.
Fired brick, typically used for construction and architectural esthetics, is one of the most durable materials with a 5000-year history dating back to Neolithic China1. This masonry building block is commonly found in various red tones and mostly comprised of fused particles of silica (SiO2), alumina (Al2O3) and hematite (α-Fe2O3)2. The red color of a brick originates from hematite, a pigment first utilized by humans 73,000 years ago3,4 and serving today as a low-cost naturally abundant inorganic precursor for catalysts5, magnets6, and alloys7. State-of-the-art energy storage materials are also produced from hematite. For example, FeNx, FeP, and Li5FeO4 are synthesized via anionic or cationic exchange for potassium-ion batteries, Zn–air batteries, pseudocapacitors, and lithium-ion batteries8,9,10,11; electrochemical transformation of hematite leads to FeOOH supercapacitor anodes12.
This work is inspired by our recently published rust-assisted vapor phase polymerization13. Chemistries enabled by hematite provide an opportunity for developing cutting-edge functionalities on a fired brick where 8 wt% α-Fe2O3 content and a 3D porous microstructure afford an ideal substrate for engineering a mechanically robust electrode. Here, we develop a supercapacitor using a brick’s hematite microstructure as reactant to vapor-deposit a nanofibrillar coating of the conducting polymer poly(3,4-ethylenedioxythiophene) (PEDOT). Vapor-phase synthesis leads to PEDOT coatings exhibiting a high electronic conductivity14 and facile charge transfer, making it an ideal route for producing electrodes15. This synthesis utilizes a brick’s open microstructure and thermal stability to permeate acid and monomer vapor through its pores at 160 °C to control α-Fe2O3 dissolution and Fe3+ hydrolysis with concomitant oxidative radical polymerization.
A symmetric brick-based supercapacitor shows an areal capacitance of 1.60 F cm−2 and energy density of 222 µWh cm−2 at a current density of 0.5 mA cm−2. This two-electrode-based measurement is collected using 1 M H2SO4 aqueous electrolyte under 1 V operating voltage window. To mimic a “brick-mortar-brick” structure, a supercapacitor is modified using a quasi-solid-state electrolyte (poly(vinyl alcohol)/1 M H2SO4) that also plays the role of binder and separator. Our devices are water-resistant because they are coated with an epoxy encapsulating layer that protects them enabling charge storage at temperatures between −20 and 60 °C. A supercapacitor is stable in ambient conditions undergoing 10,000 charge–discharge cycles with ~100% coulombic efficiency and ~90% capacitance retention. Moreover, a supercapacitor brick module is produced reaching a 3.6 V voltage window by connecting three devices in series.
Conversion of a fired brick’s α-Fe2O3 to a PEDOT coating
Deposition of PEDOT nanofibers is initiated by dissolving α-Fe2O3 at 160 °C with HCl vapor; this process liberates Fe3+ ions, promotes hydrolysis and initiates precipitation of colloidal 1D FeOOH nuclei (Fig. 1a). As previously reported, partially dissolved FeOOH nuclei serving as templates oxidize 3,4-ethylenedioxythiophene (EDOT) monomer vapor and control oxidative radical polymerization13. Control of both stoichiometry and reaction time leads to PEDOT coatings with different thicknesses (Fig. 1b). We advance previous findings by demonstrating here that the synthesis utilizes two potential polymerization initiators, i.e., oxidant (Fe3+) and acid (HCl) where the former leads to oxidative radical polymerization and the latter, to acid-catalyzed polymerization (Supplementary Fig. 1). We readily control the polymerization mechanism as an acid-catalyzed polymerization typically produces nonconductive oligomers stemming from active chain termination16. Only PEDOT synthesized via oxidative radical polymerization exhibits long conjugation length, ordered chain packing, low electrical resistance, as well as high chemical and physical stability13,14,17,18.
In our polymerization mechanism, the acid concentration determines both dissolution rate and synthetic pathways. A high H+ concentration facilitates the liberation of Fe3+ as well as oxidative radical polymerization while promoting acid-catalyzed polymerization that consumes EDOT and results in PEDOT of low conjugation length (Fig. 1c). To investigate the effect of H+ concentration, different volumes of concentrated HCl are added to the reactor and the HCl vapor concentration is calculated by dividing moles of HCl with reactor volume (assuming total evaporation). Using a HCl vapor concentration less than 4.8 mM leads to an incomplete reaction because both oxidative radical polymerization and acid-catalyzed polymerization are impeded (Supplementary Fig. 2a). Increasing concentration to 14 mM liberates Fe3+ and promotes oxidative radical polymerization resulting in PEDOT of low electrical resistance, whereas concentrations above 14 mM activate the acid-catalyzed polymerization pathway resulting in uncontrolled reactions (Supplementary Fig. 2b). When oxidative radical polymerization dominates, the EDOT vapor concentration determines the thickness of a polymer coating and its electrical resistance (Supplementary Fig. 2a, c).
Synthesis starts when a brick and chemical reactants are heated together in a sealed vessel; chemical and physical changes on a brick are monitored by collecting sample aliquots at different time intervals. Notably, there is no color change on a brick’s red surface during the first 4 h of reaction because brick dissolution is the rate-limiting step in our mixed synthetic mechanism that consists of (1) evaporation, (2) dissolution, (3) hydrolysis, and (4) polymerization. A blue PEDOT coating is visible on a brick 4 h after initiating a reaction and its thickness increases inversely proportional with electrical resistance until the end of reaction at 14 h. An extended polymerization time increases the polymer coating’s two-point probe electrical resistance (Supplementary Fig. 2d) because PEDOT loses dopant during heating18; fortunately, post-synthetic doping lowers the electrical resistance. Our synthesis produces a 400 µm thick nanofibrillar PEDOT coating (2.8 wt%) exhibiting 2Ω two-point probe electrical resistance and nanofibers characterized by a ~30 µm length and ~190 nm diameter (Supplementary Fig. 3a–d). Polymer, purified by repeated rinses in methanol, is comprised of S, C, O, and doped by Cl− in situ during polymerization as shown in energy-dispersive X-ray spectra (Supplementary Fig. 3e).
Our synthesis is general and applicable to different types of bricks. Here, three types of bricks (type 1–3) with different gravel (SiO2) sizes and porosities are investigated (Fig. 2). Type 1 brick shows the most open microstructure (Fig. 2a) that facilitates reagent vapor diffusion, therefore utilized for the synthesis study in Fig. 1 and Supplementary Figs. 1–3. Powder X-ray diffraction of pulverized type 1 brick shows that SiO2 is the major phase while α-Fe2O3 and Al2O3 are minor phases (Fig. 2c). These three types of bricks possess similar inorganic composition and concentration as shown by powder X-ray diffraction patterns (Fig. 2d). Porosity differences between brick types stem from various gravel sizes and manufacturing variables such as water content before sintering, sintering temperature and duration. Vapor-phase synthesis produces a contiguous polymer coating over the entire brick surface because dissolution generates an aqueous Fe3+ layer that coats inert gravel sites. Under identical reaction stoichiometries and time, PEDOT nanofibers of high aspect-ratio coat all types of bricks homogeneously (Fig. 2b). Our polymer coating technology is scalable (Fig. 2e) and patternable (Supplementary Fig. 4a) as demonstrated using type 1 brick. Nanofibrillar PEDOT coatings on all types of bricks show linear current–voltage curves with slopes that indicate ohmic behaviors and similar electrical resistances (~7Ω) (Fig. 3a). Note that a two-point probe multimeter measurement leads to a lower value (2Ω) because of a wide tip diameter that lowers contact resistance.
In order to study the effect of polymer coatings on the porosity of bricks, water absorption experiments are carried out before and after synthesis. A PEDOT-coated type 1 brick absorbs the most weight of water among the three types of polymer-coated bricks due to its open pore structure and large pore size and volume (Fig. 2a). A nanofibrillar PEDOT coating on type 1 brick exhibits minimal delamination via Scotch tape tests whereas a coating of the commercial product PEDOT:poly(styrenesulfonate) peels off readily and completely. Note that both type 2 and type 3 bricks show partial delamination (Fig. 3c) of our polymer coating because of a semi-closed brick microstructure (Fig. 2a) that impedes vapor reactant diffusion (Fig. 3e, f). Cross-sectional scanning electron micrographs reveal poor PEDOT interpenetration into the brick’s pores, this leads to a surface localized coating with minimal anchoring that is prone to delamination. Fortunately, type 1 brick’s open microstructure enables reagent vapor diffusion producing in situ PEDOT grafting; a nanofibrillar polymer coating is embedded as a network throughout pores resulting in strong adhesion (Fig. 3d). The addition of α-Fe2O3 particles enables deposition of PEDOT coatings on customized substrates such as concrete road pavers (Supplementary Fig. 4b) and Portland-based white concrete (Supplementary Fig. 4c).
Nanofibrillar PEDOT-coated brick electrochemical electrode
We present a summary of geometries and mass loadings for electrodes and devices in Supplementary Table 1 while areal, gravimetric, and volumetric capacitances, energy and power densities are shown in Supplementary Table 2 (calculations in detail are included in “Supplementary Methods” section). We choose areal metrics for evaluating our electrodes and devices because area is a practical parameter for evaluating our wall-like brick-based supercapacitor and it is directly related to the thin polymer coating (Supplementary Fig. 5) present on a wall. Areal metrics facilitate the estimation of capacitance and energy density delivered by a brick wall (Supplementary Discussion).
A 1 cm × 0.5 cm × 0.28 cm nanofibrillar PEDOT-coated type 1 brick (0.14 cm3) weighing 249 mg and carrying 6.97 mg PEDOT is fabricated into an electrode with one 1 cm × 0.5 cm face exposed (Fig. 4a). When calculating areal metrics, we use the area of the face exposed to electrolyte (0.5 cm2). The electrode exhibits a quasi-rectangular shaped three-electrode cyclic voltammogram and a capacitance of 2.61 F cm−2 (187 F g−1 based on PEDOT’s mass) at 2 mV s−1 in 1 M H2SO4 (Fig. 4b). The low scan rate of 2 mV s−1 enables enough time for charge transfer in the thick electrode to calculate maximum capacitance and energy density. We summarize capacitances obtained at scan rates from 2 to 100 mV s−1 in Supplementary Fig. 6a. The Fe3+/Fe2+ redox pair at 0.37 V and 0.49 V (vs. Ag/AgCl) arise due to iron species in brick and disappears as scan rate increases to 25 mV s−1 because Faradaic processes in PEDOT are faster than those occurring from solid Fe2O3 (Fig. 4c inset)15,19. Rate performance tests demonstrate capacitive behavior as scan rate increases to 100 mV s−1; however, due to limited charge transport the curve changes to fusiform shape20 (Fig. 4c). Capacitance is also dependent on the aqueous electrolyte and sulfuric acid leads to greater capacitance (1.64 F cm−2) than sodium sulfate (0.878 F cm−2) at 25 mV s−1 (Fig. 4d). This drastic difference is plausibly due to higher ionic mobility in H+ (36.23 × 10−8 m2 V−1 s−1) vs. Na+ (5.19 × 10−8 m2 V−1 s−1) or a lower electrical resistance caused by doping at low pH14. We probed this behavior further using electrochemical impedance spectroscopy. Nyquist plots and an equivalent circuit diagram demonstrate a significantly lower ion diffusion resistance for H2SO4 (1.7Ω) vs. Na2SO4 (4.6Ω) and minimal change in electrode material electrical resistance at low pH (Fig. 4e). To test the effect of an acidic electrolyte on a brick’s inorganic species, we pulverize and homogenize the entire polymer-coated brick electrode using mortar and pestle. Powder X-ray diffraction is carried out before and after electrodes are cycled in 1 M H2SO4 using sequential scan rates of 2, 5, 10, 25, 50, and 100 mV s−1 (10 cycles each). Diffraction patterns remain unchanged demonstrating that most inorganic species in a brick remain unaffected by synthesis and electrochemical cycling (Fig. 4f).
To quantify dissolution of a brick’s α-Fe2O3 and Al2O3 by 1 M H2SO4, we perform inductive coupled plasma mass spectrometry on the electrolyte after cycling experiments (Supplementary Fig. 6b, c). For a precise calculation, we control electrolyte volume (5 mL) and electrode mass (249 mg). Analysis shows negligible concentrations of Fe (4.44 µg mL−1) and Al (1.97 µg mL−1) in the electrolyte after cycling, these concentrations are equivalent to mass losses (based on the entire brick) of 0.0127 and 0.0075 wt% for α-Fe2O3 and Al2O3, respectively. These results confirm that inorganic species in a brick are preserved after electrochemical cycling.
Symmetric nanofibrillar PEDOT-coated brick supercapacitor
Two nanofibrillar PEDOT-coated bricks (1 cm × 0.5 cm × 0.28 cm) serve as electrodes in a symmetric supercapacitor (1 cm × 0.5 cm × 0.5625 cm) using 1 M H2SO4 aqueous electrolyte (Fig. 5a upper row and Supplementary Fig. 7a). A device consists of a volume (0.28 cm3) encompassing two PEDOT-coated bricks and a separator and its total mass (499 mg) includes 13.94 mg of PEDOT. Nyquist plot shows an aggregated internal resistance of 3Ω and a line with a ~45° slope between semicircle and low-frequency domain (Warburg region) (Supplementary Fig. 7b). This line is characteristic of thick electrodes where a tortuous path stifles ion diffusion. At the low-frequency region, the curve tends to form an arc because of Nernst diffusion impedance of H+ and SO42− in the electrolyte21; this plausibly stems from an increased ion diffusion distance caused by a separation gap between anode and cathode. Cyclic voltammogram shows a quasi-rectangular shape between 0 and 1 V (collected at 2 mV s−1) leading to a device areal capacitance of 1.59 F cm−2 calculated using the electrode area directly in contact with separator (0.5 cm2) (Fig. 5b, black curve and Supplementary Fig. 7c). In our device, a nanofibrillar PEDOT coating covers all six faces of a brick, two of the larger faces (1 cm × 0.5 cm) are directed towards each other and during cycling, ions travel through the inner brick pores resulting in an electrochemical contribution by the other faces. The areal metrics of this aqueous electrolyte supercapacitor are thus qualitative.
Our supercapacitor possesses low internal resistance resulting in a low IR drop (0.01 V) during galvanostatic charge-discharge experiments at 0.5 mA cm−2 current density in a 1 V window (Supplementary Fig. 7d). These curves demonstrate a device areal capacitance of 1.60 F cm−2 (2.84 F cm−3 for volumetric) as well as areal energy and power densities of 222 and 0.25 mW cm−2, respectively (394 µWh cm−3 and 0.44 mW cm−3 for volumetric). High power density (12.5 mW cm−2) is obtained at a current density of 25 mA cm−2 albeit with lowered capacitance (0.706 F cm−2) and energy density (98 µWh cm−2) because ion transport in our thick electrode is limited (shown by high IR drop of 0.4 V). Our device works in an extended voltage window (1.2 V) resulting in cyclic voltammograms and galvanostatic charge–discharge curves that retain shape (Supplementary Fig. 7e, f). However, the increased IR drop (0.07 V) at 1.2 V decreases coulombic efficiency as well as long term cycling stability leading to lower capacitance versus 1 V (Supplementary Fig. 7g, h). The energy densities at 1.2 V are higher than at 1 V as shown in a Ragone plot (Supplementary Fig. 7i) because a wider voltage window allows a device to store more charge (Supplementary Eq. 7 from “Supplementary Methods” section). Connecting three devices in series increases the voltage window to 3.6 V, this also triples the internal resistance and reduces output current to one-third (Supplementary Fig. 8a). A tandem device reaches an output voltage of 2.685 V (charged at 4.5 V for 15 s) and lights a white light-emitting diode for 11 min. The output voltage decreases to the same level as the light-emitting diode’s turn-on voltage (2.546 V) after discharging for 214 s (Supplementary Fig. 8b–d and Supplementary Movie 1).
Quasi-solid-state PEDOT-coated brick supercapacitor
To minimize electrolyte leakage, we develop a symmetric supercapacitor (1 cm × 0.5 cm × 0.63 cm) using a poly(vinyl alcohol)/1 M H2SO4 gel that binds PEDOT-coated bricks and serves as electrolyte and separator (Fig. 5a lower row and Supplementary Fig. 9a). The gel electrolyte layer (0.7 mm thick) prevents bricks (1 cm × 0.5 cm × 0.28 cm) from short-circuiting and leads to enhanced adhesion between electrodes. This sandwich-type supercapacitor is 0.32 cm3 in volume, 518 mg in weight (includes mass of electrodes and electrolyte) containing 13.94 mg of PEDOT. In a tensile test, our electrode–gel–electrode structure withstands a shearing force equal to 1000 times the device’s weight20 (Supplementary Fig. 9b). Intimate contact between gel and PEDOT nanofibers enhances charge transfer resulting in low internal resistance (2.5Ω) and a linear Nyquist plot (Supplementary Fig. 9c). Device areal capacitance (0.868 F cm−2) and areal energy density (121 µWh cm−2) originating from PEDOT-coated brick electrodes are calculated from galvanostatic charge–discharge curves (1.38 F cm−3 and 192 µWh cm−3 for volumetric, collected at 0.5 mA cm−2); cyclic voltammograms also show capacitive behavior (Fig. 5b, c, Supplementary Fig. 9d–g). The absence of redox peak from cyclic voltammogram indicates a minimal contribution from the α-Fe2O3 present in a brick to energy storage. A gel electrolyte leads to 50% lower areal capacitance and energy density than an aqueous electrolyte because of stifled gel permeation kinetics throughout the electrode preventing access of ions to all non-sandwiched PEDOT-coated faces (Fig. 5a, Supplementary Fig. 9h).
Outdoor exposure is inevitable for a stationary supercapacitor and epoxy encapsulation affords a cost-effective, mechanically robust and waterproof housing. An epoxy-coated supercapacitor retains ~90% of original capacitance and exhibits ~100% coulombic efficiency after 10,000 charge–discharge cycles (collected at 25 mA cm−2) (Fig. 5d, red curves). This 5-min epoxy coating prevents water evaporation from the gel’s hydrated ionic percolation network22 (Supplementary Fig. 10a) enabling 10,000 charge–discharge cycles at 5 mA cm−2 (640 h of continuous operation) with ~87% capacitance retention (Fig. 5d, black curves). Gel electrolyte and encapsulation enables operation at temperatures between −20 and 60 °C (this range covers most outdoor temperatures) as shown by cyclic voltammograms and Nyquist plots (Supplementary Fig. 10b, c). The capacitance increases proportionally with temperature due to enhanced ionic transport22; PEDOT remains capacitive after repeated reversible heating-cooling cycles (Supplementary Fig. 10d). Temperatures below −20 °C or above 60 °C cause significant freezing or evaporation of water from the gel electrolyte leading to unstable electrical performance and breakage of epoxy seal.
Epoxy renders a stationary supercapacitor module waterproof. Three quasi-solid-state supercapacitors are sealed in epoxy pucks (Supplementary Fig. 9a) and connected in series by electrical wires. This entire module (including connection points) is coated by another layer of epoxy that leaves only cathode and anode exposed. After epoxy curing, the entire module is immersed in water except for two electrode-leads and is electrochemically cycled (electrical circuit shown in Fig. 5e inset and Supplementary Fig. 10e). The module’s cyclic voltammograms (Fig. 5e) collected while immersed demonstrate stable behavior identical to pre-immersion tests. A device charges to 3 V in 10 s while immersed in water and lights up a green light-emitting diode (2.155 V forward voltage) for ~10 min (Supplementary Fig. 10e, f). A gel electrolyte and our deposition technology enable scale up as demonstrated by connecting six large nanofibrillar PEDOT-coated brick electrodes (2 cm ⨯ 1 cm ⨯ 1 cm) in series resulting in a supercapacitor module that charges to 3 V in 5 s readily lighting up a green light-emitting diode (Fig. 5f, Supplementary Fig. 11). Notably, a brick wall constructed using our nanofibrillar PEDOT-coated bricks holds the potential to deliver a maximum device capacitance of 11.5 kF m−2 and an energy density of 1.61 Wh m−2 (Supplementary Fig. 12; Supplementary Discussion).
This proof-of-concept work demonstrates how to store energy on the surface of a common brick using α-Fe2O3 as an oxidant precursor to control oxidative radical polymerization and conformally deposit a capacitive nanofibrillar PEDOT coating from the vapor phase. A brick’s structural stability and open microstructure result in mechanically robust PEDOT-coated brick electrodes, that when connected in series and coated with epoxy, produce a stable stationary waterproof supercapacitor module. Our supercapacitor technology adds value to a “dirt-cheap” construction material and demonstrates a scalable process affording energy storage for powering embedded microdevices in architectural applications that utilize fired brick.
Chlorobenzene (99%), 3,4-ethylenedioxythiophene (97%), poly(vinyl alcohol) (Mw 89,000–98,000, 99+% hydrolyzed), methanol (≥99.8%), and hydrochloric acid (37%) are purchased from Sigma-Aldrich; sulfuric acid (AR) is purchased from Macron. The PEDOT:PSS solution (Clevios PH 1000) is purchased from Heraeus company. All chemicals are used without further purification. Platinum foil (0.025 mm thick, 99.9%) is purchased from Alfa Aesar and utilized for engineering electrode leads and Celgard 3501 membrane is used as a separator. Fired bricks are purchased from local hardware stores: The Home Depot Inc. (type 1 brick, https://www.homedepot.com, Internet #100323015, Model #RED0126MCO, Store SKU #393134), Lowe’s Inc. (type 2 brick, https://www.lowes.com, Item # 10298, Model # 600370) and Menards Inc. (type 3 brick, https://www.menards.com, Model Number: 1441901, Menards® SKU: 1441901). Road pavers are purchased from Menards Inc. (https://www.menards.com, Model Number: 1793028, Menards® SKU: 1793028) and all construction materials used for developing electrodes are cut using a diamond saw. Red cement color (α-Fe2O3 particles) produced by NewLook Inc. is purchased from The Home Depot Inc. (https://www.homedepot.com, Internet #203858654, Model #CC1LB105) and serves as an oxidant source for developing chemical syntheses. Materials for making concrete (purchased from The Home Depot Inc., https://www.homedepot.com) include commercial-grade Quikrete Portland cement (Type I/II) (Internet #100318486, Model #100700, Store SKU #616788), Quikrete all-purpose sand (Internet #100318450Model # 115251Store SKU #137263) and Pavestone multi-purpose patio/paver base (Internet #100580973, Model #98001, Store SKU #208618).
Scanning electron micrographs and energy-dispersive X-ray spectra are collected with a JEOL 7001LVF FE-SEM. Two-point probe resistance measurements are carried out using a Fluke 177 True RMS digital multimeter with 3 mm distance between two probes. Thermogravimetric analysis is conducted on a Discovery TGA (TA Instruments). Cyclic voltammetry, galvanostatic charge–discharge measurements and electrochemical impedance spectroscopy are performed in a BioLogic VMP3 multipotentiostat. For electrochemical impedance spectroscopy, the sinusoidal disturbance is 10 mV with frequencies scanned between 100 kHz and 0.1 Hz. A Nyquist plot shows real impedance Z′ vs. imaginary impedance −Z′′ under a sinusoidal disturbance at the open circuit potential. Fitting of Nyquist plot using an equivalent circuit diagram contains solution resistance (Rs), electrode material resistance (Rm), material capacitance (Cm), double-layer capacitance (Cdl), and constant phase element (CPE). Here, Rs reflects the electrolyte ionic mobility and Rm represents the electrical resistance of the electrode. Powder X-ray diffraction spectra of brick powders pulverized by mortar and pestle are obtained in a Bruker d8 Advance X-ray diffractometer at room temperature, with a Cu Kα radiation source (λ = 1.5406 Å) and LynxEyeXe detector. The sample holder is a background-free silicon disk rotating at 30 rpm when collecting data with a 0.02° scan step at 40 kV and 40 mA. Current–voltage tests are performed on a 3D printed two-point probe station with two gold probes separated by 2 mm23. Water absorption experiments are performed as described in ASTM C67/C67M-18 except brick samples are 1 cm × 0.5 cm × 0.28 cm in size. Inductively coupled plasma mass spectrometry is performed on a Perkin Elmer ELAN DRC II ICP–MS. Samples for testing are obtained from electrolytes (5 mL 1 M H2SO4) after three-electrode cyclic voltammetry experiments and are diluted to 1/100 with Mili-Q water before analyses. External calibration curves are obtained with IV-ICPMS-71A standard solution purchased from Inorganic Ventures, Inc.
Preparation of poly(vinyl alcohol)/H2SO4 gel electrolyte
The gel electrolyte is formulated using 1 g of poly(vinyl alcohol) powder dissolved in 10 mL deionized water under vigorous stirring at 90 °C and cooled to around 50 °C. Dropwise addition of 1 g of concentrated H2SO4 (1 M) is then carried out by pipetting acid on the inner wall under vigorous stirring to prevent carbonization of poly(vinyl alcohol). Stirring minimizes localized heating and is carried out for 1 h resulting in a homogeneous, translucent, and colorless solution.
Synthesis of nanofibrillar PEDOT coating on a brick
Brick is cut using a diamond saw (±0.03 cm error) into the following 4 different sizes: 1.00 cm ⨯ 0.50 cm ⨯ 0.28 cm (for studying synthesis and electrochemistry), 1.27 cm ⨯ 1.27 cm ⨯ 0.20 cm (for patterning), 2.00 cm ⨯ 1.00 cm ⨯ 1.00 cm (for scaled-up supercapacitor) and 10.16 cm ⨯ 6.77 cm ⨯ 5.72 cm (for scaled-up synthesis). A brick is thrice washed with deionized water to remove surface dust then dried at 160 °C for 1 h and cooled to room temperature.
The syntheses of all types of 1 cm ⨯ 0.5 cm ⨯ 0.28 cm brick are performed in a 25 mL Teflon-lined stainless-steel autoclave as shown in Fig. 1a. A brick is placed on a glass reservoir then 200 µL of a 0.85 M EDOT/chlorobenzene solution is loaded in a separate glass reservoir and 30 µL of 12 M HCl is directly injected in the Teflon liner. The reactor is closed and introduced into an oven at 160 °C for 14 h. The product is washed thrice with excess methanol and dried at room temperature before carrying out tests. Similarly, the synthesis of a 2 cm ⨯ 1 cm ⨯ 1 cm brick is performed in a 125 mL Teflon-lined stainless-steel autoclave using 600 µL of a 0.70 M EDOT in chlorobenzene solution and 75 µL of 12 M HCl.
A brick (1.27 cm ⨯ 1.27 cm ⨯ 0.20 cm) is patterned using a polyimide tape mask. Synthesis is carried out at 150 °C for 14 h in a 125 mL Teflon-lined stainless-steel autoclave containing 1 mL of a 0.85 M EDOT solution in chlorobenzene and 0.6 mL of 12 M HCl (Supplementary Fig. 4a).
Scaling is carried in a glass reactor (12.30 cm ⨯ 8.55 cm ⨯ 11.30 cm) with a large brick (10.16 cm ⨯ 6.77 cm ⨯ 5.72 cm). The reaction is carried out using 15 mL of 12 M HCl and 15 mL of a 0.85 M EDOT in chlorobenzene solution at 150 °C for 6 h (Fig. 2e).
We produce a PEDOT coating on concrete by applying α-Fe2O3 particles to a concrete surface (Supplementary Fig. 4c). This composite is produced by mixing sand, stone, Portland cement and water in a weight ratio of 3:1.5:1:0.7. An uncured concrete slurry is then injected into a 1.27 cm ⨯ 1.27 cm ⨯ 2.54 cm mold, stirred to remove gas bubbles, and cured for 3 days in ambient conditions. A partially cured concrete bar is dipped in an aqueous dispersion of α-Fe2O3 (0.25 g mL−1) for 3 s, then dried in air. Synthesis is performed at 150 °C for 14 h in a 125 mL Teflon-lined stainless-steel autoclave loaded with 1 mL of a 0.45 M EDOT in chlorobenzene solution and 0.1 mL of 12 M HCl.
Fabrication of a quasi-solid-state supercapacitor
The brick is attached to Pt as shown in Supplementary Fig. 7a (left top) prior to gel casting. The gel electrolyte (0.1 g mL−1 poly(vinyl alcohol)/1 M H2SO4) is pipetted onto two 1 cm ⨯ 0.5 cm ⨯ 0.28 cm PEDOT-coated bricks (100 µL each brick on the 1 cm ⨯ 0.5 cm face). This electrolyte is allowed to impregnate for 12 h at ambient conditions (25 °C, 30–60% relative humidity) forming a semidry gel layer. An additional 25 µL of gel electrolyte is added serving as a binder between two bricks to assemble a sandwich-type supercapacitor. A device is dried in ambient conditions (25 °C, 30–60% relative humidity) for 1 h before sealing with epoxy (Supplementary Fig. 9a).
Fabrication of a tandem supercapacitor
The gel electrolyte is a mixture of 0.1 g of poly(vinyl alcohol) in 1 mL of 1 M H2SO4 and 200 µL are added to a PEDOT-coated brick face (1 cm ⨯ 1 cm). This electrolyte is allowed to stabilize for 12 h at ambient conditions (25 °C, 30–60% relative humidity); this process is repeated for all brick electrodes resulting in a thick gel layer (Supplementary Fig. 11a). An additional 50 µL of poly(vinyl alcohol)/H2SO4 solution is added serving as a binder between bricks. Devices are dried in an oven at 50 °C for 2 h and platinum foil, serving as a lead, is attached to bricks using polyimide tape.
The data that support the findings of this study are available from the corresponding author on request.
Yang, Y., Yu, S.-Y., Zhu, Y. & Shao, J. The making of fired clay bricks in China some 5000 years ago. Archaeometry 56, 220–227 (2014).
Kreimeyer, R. Some notes on the firing colour of clay bricks. Appl. Clay Sci. 2, 175–183 (1987).
Henshilwood, C. S. et al. An abstract drawing from the 73,000-year-old levels at Blombos Cave, South Africa. Nature 562, 115–118 (2018).
Proceedings of the National Academy of Sciences Roebroeks W. et al. Use of red ochre by early Neandertals. Proc. Natl Acad. Sci. USA 109, 1889–1894 (2012).
Liu, Q. et al. Aligned Fe2TiO5-containing nanotube arrays with low onset potential for visible-light water oxidation. Nat. Commun. 5, 5122 (2014).
Jia, C.-J. et al. Large-scale synthesis of single-crystalline iron oxide magnetic nanorings. J. Am. Chem. Soc. 130, 16968–16977 (2008).
Kenel, C., Casati, N. P. M. & Dunand, D. C. 3D ink-extrusion additive manufacturing of CoCrFeNi high-entropy alloy micro-lattices. Nat. Commun. 10, 904 (2019).
Yang, F. et al. Yolk–shell structured FeP@C nanoboxes as advanced anode materials for rechargeable lithium‐/potassium‐ion batteries. Adv. Funct. Mater. 29, 1808291 (2019).
Han, S., Hu, X., Wang, J., Fang, X. & Zhu, Y. Novel route to Fe-based cathode as an efficient bifunctional catalysts for rechargeable Zn-Air battery. Adv. Energy Mater. 8, 1800955 (2018).
Dong, Y. et al. Air-stable porous Fe2N encapsulated in carbon microboxes with high volumetric lithium storage capacity and a long cycle life. Nano Lett. 17, 5740–5746 (2017).
Zhan, C. et al. Enabling the high capacity of lithium-rich anti-fluorite lithium iron oxide by simultaneous anionic and cationic redox. Nat. Energy 2, 963–971 (2017).
Owusu, K. A. et al. Low-crystalline iron oxide hydroxide nanoparticle anode for high-performance supercapacitors. Nat. Commun. 8, 14264 (2017).
Diao, Y. et al. Converting rust to PEDOT nanofibers for supercapacitors. ACS Appl. Energy Mater. 2, 3435–3444 (2019).
Wang, X. et al. High electrical conductivity and carrier mobility in oCVD PEDOT thin films by engineered crystallization and acid treatment. Sci. Adv. 4, eaat5780 (2018).
Berggren, M. & Malliaras, G. G. How conducting polymer electrodes operate. Science 364, 233–234 (2019).
Zhang, S. et al. p-Toluenesulfonic acid catalytic polymerization of EDOT without oxidants. Mater. Lett. 222, 105–108 (2018).
Xiao, H. et al. Stretchable tandem micro-supercapacitors with high voltage output and exceptional mechanical robustness. Energy Storage Mater. 13, 233–240 (2018).
Wang, H. et al. Self-woven nanofibrillar PEDOT mats for impact-resistant supercapacitors. Sustain. Energy Fuels 3, 1154–1162 (2019).
Ding, M. et al. Effect of Fe(III) on the positive electrolyte for vanadium redox flow battery. R. Soc. Open Sci. 6, 181309 (2019).
Li, X. et al. High energy flexible supercapacitors formed via bottom-up infilling of gel electrolytes into thick porous electrodes. Nat. Commun. 9, 2578 (2018).
Zhou, H. et al. Printable fabrication of Pt-and-ITO free counter electrodes for completely flexible quasi-solid dye-sensitized solar cells. J. Mater. Chem. A 1, 3932–3937 (2013).
Dubal, D. P., Chodankar, N. R., Kim, D. H. & Gomez-Romero, P. Towards flexible solid-state supercapacitors for smart and wearable electronics. Chem. Soc. Rev. 47, 2065–2129 (2018).
Lu, Y., Santino, L. M., Acharya, S., Anandarajah, H. & D’Arcy, J. M. Studying electrical conductivity using a 3D printed four-point probe station. J. Chem. Educ. 94, 950–955 (2017).
We thank Dr. Bryce Sadtler from the Department of Chemistry and Dr. Anne M. Hofmeister from the Department of Earth and Planetary Sciences at Washington University for providing fruitful discussions. We are grateful to Dr. Huafang Li from the Institute of Materials Science & Engineering at Washington University for helping with electron microscopy. We also acknowledge helpful technical input from Dr. Luciano M. Santino and Mr. Haozhe Chen and are grateful to Dr. G.S. D’Arcy for editing this work.
The authors declare no competing interests.
Peer review information Nature Communications thanks Yu Wang and the other, anonymous, reviewer(s) for their contribution to the peer review of this work. Peer reviewer reports are available.
Publisher’s note Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.
About this article
Cite this article
Wang, H., Diao, Y., Lu, Y. et al. Energy storing bricks for stationary PEDOT supercapacitors. Nat Commun 11, 3882 (2020). https://doi.org/10.1038/s41467-020-17708-1
Journal of Alloys and Compounds (2021)
Rational design of ZIF-8 assimilated hierarchical porous carbon nanofibers as binder-free electrodes for supercapacitors
Journal of Electroanalytical Chemistry (2021)
MoO2 coated few layers of MoS2 and FeS2 nanoflower decorated S-doped graphene interoverlapped network for high-energy asymmetric supercapacitor
Journal of Colloid and Interface Science (2021)
The interwoven porous CoCHH@PEDOT nanowire network structure improves electrochemical performance of carbon cloth for flexible supercapacitors
Applied Surface Science (2021)