tf_template_word_windows_2016epubs.surrey.ac.uk/850066/...solidelec-rreece-v3.docx · web...
TRANSCRIPT
A structural supercapacitor based on activated carbon fabric and a
solid electrolyte
Richard Reecea, C. Lekakoua*, P.A. Smitha
aDepartment of Mechanical Engineering Sciences, University of Surrey, Guildford,
GU2 7XH, UK
*email of the corresponding author: [email protected]
Short biographical notes on all contributors:
Richard Reece obtained his PhD in the Department of Mechanical Engineering at the
University of Surrey. His research focused on the development of different types of structural
supercapacitors and investigations into their electrochemical and structural performance.
Constantina Lekakou is a Reader at the University of Surrey. She completed her PhD in the
Department of Chemical Engineering at Imperial College. London. Her expertise covers the
areas of multi-materials processing and manufacturing of polymer composites as well as the
fabrication, characterisation and analysis of energy storage devices.
Paul Smith is Professor of Composite Materials at the University of Surrey and the Executive
Dean of the Faculty of Engineering and Physical Sciences. He holds a first Degree in
Engineering and a PhD from the University of Cambridge. His research interests focus on the
mechanical behaviour of composite materials.
A structural supercapacitor based on activated carbon fabric and a
solid electrolyte
This paper presents investigations to create a structural supercapacitor with
activated carbon fabric electrodes and a solid composite electrolyte, consisting of
organic liquid electrolyte 1 M TEABF4 in propylene carbonate and an epoxy
matrix where different compositions were considered of 1:2, 1:1 and 2:1 w/w
epoxy: liquid electrolyte. Vacuum-assisted resin transfer moulding was used for
the impregnation of the electrolyte mixture into the electrochemical double layer
capacitor (EDLC) assembly. The best electrochemical performance was exhibited
by the 1:2 w/w epoxy: liquid electrolyte ratio, with a cell equivalent-in-series
resistance of 160 cm2 and a maximum electrode specific capacitance of 101.6
mF g-1 while the flexural modulus and strength were 0.3 GPa and 29.1 MPa,
respectively, indicating a solid EDLC device.
Keywords: solid EDLC; VARTM; activated carbon fibre fabric; solid composite
electrolyte; TEABF4 in propylene carbonate; epoxy; three-point bend test.
Subject classification codes: 7. Composite materials; 8. Functional materials
1. Introduction
Structural composites typically consist of continuous fibre reinforcement and a polymer
matrix [1]. Depending on the type of fibre (mainly: carbon, glass or Kevlar® fibres in
continuous fibre, woven fabric or stitch-boned fabric format) and the type of matrix
(thermoset such as epoxy or polyester or thermoplastic such as poly(ether ether ketone)
(PEEK)), composite materials have a tensile modulus of 20-200 GPa, a tensile strength
of 300-1600 MPa and a density of 1400-1900 kg m-3 [2-3]. Composite materials are
involved in various types of energy harvesting some of which are high power methods
associated with short timescales: for example, wind turbines display continuous series
of power peaks as the wind suddenly changes direction or speed [4] while piezoelectric
energy harvesting related to vibrations [5] and RF energy harvesting [6] display a series
of incoming power pulses. In all these cases, a supercapacitor may be required in
combination with the battery [4-5], where the supercapacitor, with its high power
capability [7-8], may receive the high power peaks above a threshold and so protect the
battery from experiencing high current densities that would have led to fast battery
degradation. As supercapacitors are of high power density, frequently of 20 kW kg-1 [7],
a relatively small mass may be needed which might be integrated in a structural
composite material.
Supercapacitors consist of porous electrodes of large specific surface area, in
intimate contact with the corresponding current collectors, and an electrolyte which
might be liquid, gel or solid [9-12]. Activated carbon fibre (ACF) woven fabrics of
specific pore surface area of around 2000 m2 g-1 are excellent electrodes for high
performance supercapacitors with an aqueous or an organic electrolyte [13-14] and,
hence, are proposed to be investigated for multifunctional composite materials in this
study. Due to the low maximum voltage, Vmax, of aqueous electrolytes, about 1.1 V,
organic electrolytes (Vmax = 2.7 – 3 V) and ionic liquid (IL) electrolytes (Vmax = 3.5 – 4.5
V) are preferred for high voltage applications, such as electric vehicles [15-16]. Solid
electrolytes, although ideal for a structural supercapacitor, display low ion conductivity
[17]. Such investigated electrolytes include gel electrolytes based on a polymer gel
matrix such as polyethylene oxide or polyvinyl alcohol or a silica gel [18-19], Nafion
ionomer membranes [20] or ceramic membranes impregnated with a liquid electrolyte
or doped with ions [21-22].
A solid electrolyte acts as the solid-state matrix which has fully impregnated the
separator and the porous electrodes and, hence, offers the potential of creating a
structural composite with the additional functionality of supercapacitor. Past attempts to
create structural supercapacitors with both a solid electrolyte and carbon fibre
reinforcement of low porosity yielded supercapacitors of extremely low performance.
Shirshova et al [23] impregnated a glass fibre separator with a polyacrylonitrile gel
electrolyte or a crosslinking polyethylene glycol diglycidylether (PEGDGE) matrix,
both containing 0.1 M LiTFSI in a solvent mixture of ethylene carbonate (EC) and
propylene carbonate (PC). They used carbon fabrics with no activation, low activation
(BET = 21.4 m2 g-1) or high activation (BET = 1100 m2 g-1); data of single fibre
mechanical properties included: Young’s modulus E=204, 207 and 40 GPa and tensile
strength F = 3.3, 4 and 1.1 GPa, respectively, but the fibre specific capacitance in
aqueous 3 M KCl electrolyte was extremely low at: 0.06, 2.6 and 0.1 F g-1, respectively;
the highest electrode specific capacitance in solid electrolyte was observed for the
system ACF/PEGDGE/LiTFSI/IL to be 0.52 mF g-1, while for this system the
compressive modulus was 18 GPa and the compressive strength was 7.5 MPa. The
electrode specific capacitances above are very low when compared with good
supercapacitor performance, for example, 160 F g-1 for an ACF of BET = 2000 m2 g-1
and a liquid electrolyte of 1.5 M TEABF4 in acetonitrile [14]. This indicates not only
poor ion conductivity in the solid electrolyte but also lack of access of the small ions of
the electrolyte (even of the liquid aqueous electrolyte) to the pores of even the highly
activated carbon fabric in reference [23]. Carbon aerogel (CAG)-modified carbon fibres
[24] showed a maximum specific capacitance of 7.4 F g-1 at 9.1 wt% CAG in aqueous 3
M KCl electrolyte [25] and 90.5 mF g-1 for a composite PEGDGE with 10 wt% IL
electrolyte-fibre glass separator; the latter structural supercapacitor had a high in-series
resistance (ESR) of 79 k cm2, a shear modulus of 1.17 GPa and a shear strength of 9.8
MPa [25].
This study starts with ACF fabric electrodes of high performance in liquid
electrolyte TEABF4 in acetonitrile [7], in this case replacing the organic solvent with the
less volatile propylene carbonate (PC). Research focused on developing a composite
electrolyte of TEABF4 in PC and an RTM (resin transfer moulding) epoxy, so that the
low viscosity of this epoxy would contribute to complete filling [26-28] of the porous
electrodes, to their micropores, with the epoxy-electrolyte mixture in vacuum- assisted
resin transfer moulding (VARTM) [29], and provide an integrated structure with good
structural and electrochemical performance. Three different compositions were
investigated for the composite electrolyte: 1:2, 1:1 and 2:1 w/w epoxy: liquid organic
electrolyte.
2. Materials and Methods
Activated carbon fibre plain-woven fabric, ACC-507-15 Kynol® Novoloid Fabric,
manufactured by Gun-ei Chemical Industry Co., was used as the electrode material with
a stated thickness of 0.5 mm, a measured areal density of 12 mg cm-2, and a specific
surface area (BET) of 1500 m2 g-1. 30G01 Toyal Carbo® aluminium carbide composite
foil, manufactured by Toyo Aluminium K.K. was used as electrode current collectors,
with a stated thickness of 30 μm and orthogonal aluminium carbide nano whiskers of
diameter 20-30 nm embedded in the backing aluminium foil. The cellulose paper
TF4060, manufactured by Nippon Kodoshi Corp., was used as separator with a stated
thickness of 60 μm and measured areal density of 2.5 mg cm-2.
A solid composite electrolyte was prepared consisting of an organic electrolyte
solution in an epoxy matrix. The organic electrolyte solution was 1 M TEABF4 in PC
(propylene carbonate), both supplied by Sigma Aldrich. The epoxy system comprised
araldite LY564-1 resin and Aradur HY2954 hardener in a ratio of 100:35 parts by
weight, respectively, where this is a low viscosity epoxy system usually employed in
resin transfer moulding (RTM). The composite electrolyte was a mixture of the organic
electrolyte solution and the epoxy matrix at the ratios of 1:2, 1:1, and 2:1 w/w.
Electrochemical double layer capacitors (EDLCs) with only liquid electrolyte 1M
TEABF4 in PC were also fabricated and tested.
115 μm polymer laminated aluminium foil EQ-alf-200-15M was used as casing
material, and 8 mm aluminium tabs EQ-PLiB-ATC8 were used for external circuit
connection (both were supplied by MTI Corporation).
The epoxy mixture of araldite LY564-1 resin and Aradur HY2954 hardener was
prepared at a ratio of 100:35 parts by weight and was mixed with the liquid electrolyte
solution 1 M TEABF4 in PC at the required ratio (1:2, 1:1, and 2:1 w/w). Vacuum-
assisted resin transfer moulding (VARTM) was used in which the first step was to
assemble the EDLC consisting of the outer parts of the casing as external layers, the
current collector foils, the ACF fabrics and the separator in the middle and place the
assembly on a flat glass plate. The whole assembly was then covered with a vacuum bag
as shown in Figure 1. Under the bag two spirals were placed adjacent to the cell to
maintain the vacuum bag over the assembly and allow the free application of vacuum
and the free flow of resin into the EDLC cell. Under vacuum the electrolyte-epoxy
mixture was injected into the EDLC assembly between the current collector foils and it
impregnated the separator and the porous ACF fabric electrodes. Once it was seen on
the other side at the beginning of the vacuum tube, the vacuum tube first and then the
feed tube were clamped. A solid plate of 10 kg was placed on top of the cell and the
epoxy was allowed to cure for 12 hr at room temperature. Upon curing of the epoxy, a
solid composite EDLC was created.
Electrochemical testing of pouch EDLC cells was carried out using a Versastat
MC from Princeton Technology. Electrochemical impedance spectroscopy (EIS)
characterisation of EDLC cells of an area of 16 cm2 was performed in the frequency
range of 10 mHz to 1 MHz. Larger pouch EDLC cells of an area of 72.16 cm2 were
subjected to cyclic voltammetry (CV) tests at scan rates of 0.01 to 1 V s-1 and
galvanostatic charge-discharge (GCD) tests at different currents.
Mechanical three-point bend testing of EDLC beam specimens of 40 mm length
and 15 mm width was undertaken using an Instron 500R universal testing machine,
according to ASTM.D790 [30] at a speed of the moving head of 1 mm/min. The
flexural strength σfm, expressed in MPa, was calculated using the applied load at failure
Pmax in Newtons, and the beam span L, width b, and thickness d in millimetres,
according to the equation:
σ fm=3 Pmax L2b d2 (1)
The flexural strain εf, expressed in millimetres per millimetre, was calculated using the
beam deflection δ, thickness d, and span L, all in millimetres, according to the equation:
ε f =6δdL2 (2)
A nominal flexural modulus, Ef, was obtained by considering the beam span L, width b,
and thickness d in millimetres, and the applied load-time derivative m=dPdt where P is
the load applied to the beam and t is time in seconds.
E f=L3 m604 b d3 (3)
3. Results
Figure 2 presents the Nyquist plots from the EIS data of the tested EDLCs for different
compositions of the composite electrolyte, from 100 wt% liquid electrolyte 1 M
TEABF4/PC to 2:1 w/w solid epoxy:liquid electrolyte 1 M TEABF4/PC. The plots
display an increasing ESR resistance as the epoxy content increases from 12.8 cm-2
for pure liquid electrolyte, to 160 cm-2 for 1:2 w/w epoxy:liquid electrolyte to finally
880 k cm-2 for 2:1 w/w epoxy:liquid electrolyte and an increasing loss tangent at low
frequencies (tan = Zre/Zim) while at the same time the capacitance, C, decreases,
where C = (2 f Zim)-1, f is the frequency and Zim is the imaginary impedance
component (ignoring the inductance term of impedance, 2 f Lind, for the majority of
frequencies). In the solid epoxy:liquid electrolyte 1 M TEABF4/PC mixture, the liquid
electrolyte is the only constituent providing conductivity via ion transport (of the TEA+
and BF4- ions), while the epoxy acts as an insulator of electronic transport; hence, as the
proportion of epoxy is raised in the mixture, the resistance increases in the form of three
resistance components: (a) higher solid electrolyte mixture resistance due to higher
proportion of epoxy insulator, (b) higher contact resistance between the ACF fabric and
the current collector foil due to the solid electrolyte mixture interlayer dominated by the
insulating epoxy, and (c) increasing loss tangent at low frequencies due to slower ion
diffusion through the small micropores of the ACF electrode, as the ions have to diffuse
through an increased proportion of solid epoxy matrix of low diffusivity. As a result,
fewer ions reach the walls of micropores, which means that the capacitance at low
frequencies also decreases as the proportion of epoxy is increased (Figure 2(d)).
Given the electrochemical performance of the above structural EDLCs, the ratio
of 1:2 w/w epoxy: electrolyte solution was therefore chosen to proceed with fabricating
a larger 8×9 cm2 cell of 1.73 g ACF fabric mass for both electrodes and 18.5 g total cell
mass, to test in cyclic voltammetry and galvanostatic charge-discharge. Figure 3
presents the voltammograms at different charge-discharge rates from 0.01 V s-1 to 1 V s-
1. The EDLC demonstrates low specific capacitance, reaching a maximum of 0.34 F g-1
and a mean specific capacitance of 0.1 F g-1 at a scan rate of 0.01 V s-1.
Figure 4(a) displays the data from the galvanostatic charge-discharge tests for
the 16 cm2 EDLC with the liquid 1 M TEABF4/PC electrolyte, which yield a cell
specific capacitance of 30.4 F g-1 (i.e. per gram of both ACF fabric electrodes) and an
electrode specific capacitance of 121.5 F g-1 at a current density of 0.0625 mA cm-2 of
cell area. Figure 4(b) displays the GCD data for the 72.16 cm2 EDLC cell with the
composite epoxy: electrolyte 1 M TEABF4/PC at 1:2 w/w, which yield a cell specific
capacitance of 1.15 mF g-1 (i.e. per gram of both ACF fabric electrodes) and an
electrode specific capacitance of 4.6 mF g-1 at the same current density of 0.0625 mA
cm-2. At the lowest tested current density 5.54 A cm-2 of this composite EDLC yields a
maximum cell specific capacitance of 25.4 mF g-1 and an electrode specific capacitance
of 101.6 mF g-1 but the GCD curves are non-linear at current densities below 11 A cm-
2 indicating low energy efficiency in the charge-discharge process. Figure 5(b) shows
that the Ragone plot derived from the discharge phase of the GCD data of Figure 4(b) at
different discharge currents demonstrates a maximum measured energy density of 5
mWh/kg of ACF electrodes mass and a maximum measured power density of 2 W/kg of
ACF electrodes mass. This may be compared with the maximum measured energy and
power density of 32 Wh/kg and 1200 W/kg of ACF electrodes mass for the EDLC with
only 1 M TEABF4/PC liquid electrolyte in Figure 5(a).
The results of the three-point bend tests are presented in Figure 6 in which it can
be seen that the specimens with composite epoxy: liquid electrolyte at 1:2 and 1:1 w/w
ratio show similar behaviour whereas the specimen with 2:1 w/w epoxy: liquid
electrolyte exhibits much better mechanical performance. Table 1 summarises all values
of key performance indicators regarding both electrochemical and mechanical
properties: it can be seen that the specimen with 2:1 w/w epoxy: liquid electrolyte has a
flexural modulus and strength of 24.1 GPa and 1.357 GPa, respectively, whereas the
specimen with 1:2 w/w epoxy: liquid electrolyte has Ef = 0.3 GPa and fm = 29.1 MPa.
4. Discussion
There are several novel aspects investigated in this study all of which have an impact on
the resulted electrochemical and mechanical performance of the composite
supercapacitors. First of all, this is the first time where the electrolyte 1 M TEABF4
dissolved in PC has been used for a ACF Kynol® fabric. ACF Kynol® fabrics are
phenolic-derived, generally with a very narrow pore size distribution around 1-2 nm
width of slit-type pores [7], which means that acetonitrile (AN) is preferred as the
electrolyte solvent consisting of a small molecule and forming solvated cations
TEA+/AN with dimensions of the van der Waals volume: Lmin = 1.1 nm and Lmax = 1.25
nm [14], which means that they fit very well in the majority of pores and provide a high
energy density and a medium power density of 39 Wh/kg and 6 kW/kg of the two ACF
fabric electrodes, respectively [7]. Replacing AN with the less volatile propylene
carbonate (PC) as the solvent, means that the dimensions of the van der Waals volume
of the solvated cations TEA+/PC are larger: Lmin = 1.96 nm and Lmax = 2.05 nm [31],
closer to the pore slit width of the ACF material, which means that although double
layer capacitance might increase [32], ion transport is much slower and ions might not
have access to all small pores. While PC is a popular non-volatile electrolyte, it is
usually employed as a solvent for TEABF4 for coating-based electrodes which display a
wide pore size distribution [7, 33-34], so ion transport occurs faster through a
hierarchical pore network from macro- to meso- to micro-pores [35-36]. The present
study demonstrated that the liquid electrolyte 1M TEABF4/PC leads to higher electrode
specific capacitance, 121.5 F g-1 than in previous studies [35-36], due to the good
matching between the solvated ion size and the pore slit width. However, it leads to
lower cell power density, 1.2 kW/kg, against 6 kW/kg for the same ACF-based cells
with TEABF4 in AN [7], due to the slower transport of PC-solvated TEA+ ions through
the narrow pores of the ACF fabric electrode.
The composite supercapacitor with 2:1 w/w epoxy:liquid electrolyte matrix
exhibits a flexural modulus and flexural strength of 24.1 GPa and 1.357 GPa,
respectively. This mechanical performance outperforms the mechanical performance of
the other two composite supercapacitors with higher proportion of liquid electrolyte and
is equivalent to that of a low performance carbon reinforced epoxy composite [3].
However, the ESR resistance of this composite cell is very high, 880 k cm2, which
does not recommend it as a supercapacitor device. The best composite supercapacitor
fabricated and tested in this study is the cell with 1:2 w/w epoxy: liquid electrolyte
matrix which provides an ESR resistance of 160 cm2 and a maximum electrode
specific capacitance of 101.6 mF g-1, higher than previously reported for composite
supercapacitors [23, 25] with highly activated carbon electrodes but different liquid
electrolytes and solid matrix (PEGDGE with LiTFSI or IL electrolyte in [23, 25]). The
flexural modulus and flexural strength of this composite supercapacitor were 0.3 GPa
and 29.1 MPa, respectively, which place it in the range of solid devices but not for
advanced structural applications [3].
5. Conclusion
The present study includes investigations to create a structural supercapacitor with a
novel solid composite electrolyte of epoxy and 1M TEABF4 in PC, and activated carbon
fibre fabric electrodes of high specific surface area of 1500 m2 g-1. Different
compositions of the composite electrolyte were considered, including 1:2, 1:1 and 2:1
w/w solid epoxy: liquid 1M TEABF4/PC. Increasing the proportion of epoxy raised the
structural performance of the material, resulting in a flexural modulus of 24.1 GPa and a
flexural strength of 1.357 GPa for the 2:1 w/w epoxy:liquid electrolyte mixture, which
was found equivalent to that of a low performance carbon reinforced epoxy composite
[3]. However, the higher epoxy content was detrimental for the electrochemical
performance of the supercapacitor, raising the device resistance and lowering its
maximum tested capacitance, which yield lower power density and energy density,
respectively. The lowest resistance and highest capacitance were obtained for
supercapacitor with 1:2 w/w epoxy: liquid electrolyte matrix, which exhibited an ESR
resistance of 160 cm2 and a maximum electrode specific capacitance of 101.6 mF g-1
but lower mechanical performance, with Ef = 0.3 GPa and fm = 29.1 MPa.
Acknowledgements
We gratefully acknowledge the funding by the UK Defence Science Technology
Laboratory (DSTL) in the form of a PhD studentship for the first author.
References
1. Bader MG, Lekakou C. Processing for laminates structures. In: Composites
Engineering Handbook. Ed. Mallick PK. New York, USA; 1997: 371-468.
2. Mall S. Laminated polymer matrix composites. In: Composites Engineering
Handbook. Ed. Mallick PK. New York, USA; 1997: 811-890.
3. Astrom BT. Manufacturing of polymer composites. London, UK; Chapman & Hall;
1997: 161-177.
4. van Voorden AM, Ramirez Elizondo LM, Paap GC, et al. The application of super
capacitors to relieve battery-storage systems in autonomous renewable energy
systems. Proceedings of the 2007 IEEE Lausanne Power Tech, 2007 July 1-5;
Lausanne, Switzerland. IEEE; 2018; 290: 1-6.
5. Pörhönen J, Rajala (Née Kärki), Lehtimäki SS, et al. Flexible piezoelectric energy
harvesting circuit with printable supercapacitor and diodes. IEEE Transactions on
Electron Devices. 2014; 61: 3303-3308.
6. Shumbayawonda E, Salifu AA, Lekakou C, et al. Numerical and experimental
simulations of the wireless energy transmission and harvesting by a camera pill.
ASME Transactions - Journal of Medical Devices. 2018; 12:
doi:10.1115/1.4039390, 9pp.
7. Fields R, Lei C, Markoulidis F, et al. The composite supercapacitor. Energy
Technology. 2016; 4: 517–525.
8. Santucci A, Sorniotti A, Lekakou C. Power split strategies for hybrid energy storage
systems for vehicular applications. Journal of Power Sources. 2014; 258: 395-407.
9. Libich J, Máca J, Vondrák J, et al. Supercapacitors: Properties and applications.
Journal of Energy Storage. 2018; 17: 224-227.
10. Wang F, Wu X, Yuan X, et al. Latest advances in supercapacitors: from new
electrode materials to novel device designs. Chem. Soc. Rev. 2017; 46: 6816-6854.
11. Chen X, Paul R, Dai L. Carbon-based supercapacitors for efficient energy storage.
National Science Review. 2017; 4: 453–489.
12. Eftekhari A. The mechanism of ultrafast supercapacitors. Journal of Materials
Chemistry A. 2018; 6: 2866-2876.
13. Fic K, Meller M, Frackowiak E. Interfacial redox phenomena for enhanced aqueous
supercapacitors. Journal of The Electrochemical Society. 2015; 162: A5140-A5147.
14. Markoulidis F, Lei C, Lekakou C. Investigations of activated carbon fabric-based
supercapacitors with different interlayers via experiments and modelling of
electrochemical processes of different timescales. Electrochimica Acta. 2017; 249:
122-134.
15. Zhong C, Deng Y, Hu W, et al. A review of electrolyte materials and compositions
for electrochemical supercapacitors. Chem. Soc. Rev. 2015; 44: 7484-7539.
16. Béguin F, Presser V, Balducci A, et al. Carbons and electrolytes for advanced
supercapacitors. Advanced Materials. 2014; 26: 2219-2251.
17. Uddin M-J, Cho S-J. Reassessing the bulk ionic conductivity of solid state
electrolytes. Sustainable Energy & Fuels, 2018; 2: 1458-1462.
18. Lekakou C, Moudam O, Markoulidis F, et al. Carbon-based fibrous EDLC
capacitors and supercapacitors. Journal of Nanotechnology. 2011; Article number
409382: doi: 10.1155/2011/409382C.
19. Lavine MS. A solid electrolyte. Science. 2018; 359: 1115-1116.
20. Staiti P, Minutoli M, Lufrano F. All solid electric double layer capacitors based on
Nafion ionomer. Electrochemica Acta. 2002; 47: 2795-2800.
21. Hu X, Chen YL, Hu ZC, et al. All-solid-state supercapacitors based on a carbon-
filled porous/dense/porous layered ceramic electrolyte. J. Electrochem. Soc. 2018;
165: A1269-A1274.
22. Zheng F, Kotobuki M, Song S, et al. Review on solid electrolytes for all-solid-state
lithium-ion batteries. J. Power Sources. 2018; 389: 198-213.
23. Shirshova N, Qian H, Shaffer MSP, et al. Structural composite supercapacitors.
Composites Part A. 2013; 46: 96-107.
24. Qian H, Kucernak AR, Greenhalgh ES, et al. Multifunctional structural
supercapacitor composites based on carbon aerogel modified high performance
carbon fiber fabric. ACS Appl. Mater. Interfaces. 2013; 5: 6113−6122.
25. Shirshova N, Qian H, Houlle M, et al. Multifunctional structural energy storage
composite supercapacitors. Faraday Discuss. 2014; 172: 81-103.
26. Amico S, Lekakou C. Flow through a two-scale porosity, oriented fibre porous
medium. Transport in Porous Media. 2004; 54: 35-53.
27. Amico SC, Lekakou C. Axial impregnation of a fibre bundle. Part 2. Theoretical
analysis. Polymer Composites. 2002; 23: 264-273.
28. Lekakou C, Edwards S, Bell G, et al. Computer modelling for the prediction of the
in-plane permeability of non-crimp stitch bonded fabrics. Composites A: Applied
Science and Manufacturing. 2006; 37: 820-825.
29. Yoon M-K, Baidoo J, Gillespie JW Jr. et al. Vacuum assisted resin transfer molding
(VARTM) process incorporating gravitational effects: a closed-form solution.
Journal of Composite Materials. 2005; 39: 2227-2242.
30. ASTM D790 – 17. Standard test methods for flexural properties of unreinforced and
reinforced plastics and electrical insulating materials. ASTM Standards. West
Conshohocken, PA; ASTM International; 2017; DOI: 10.1520/D0790-17.
31. Galhena DTL, Bayer BC, Hofmann S, et al. Understanding capacitance variation in
sub-nanometer pores by in-situ tuning of interlayer constrictions. ACS Nano. 2016;
10: 747–754.
32. Huang J, Sumpter BG, Meunier V. A universal model for nanoporous carbon
supercapacitors applicable to diverse pore regimes, Carbon Materials, and
Electrolytes. Chemistry Eur. J.. 2008; 14: 6614-6626.
33. Markoulidis F, Lei C, Lekakou C. et al. A method to increase the energy density of
supercapacitor cells by the addition of multiwall carbon nanotubes into activated
carbon electrodes. Carbon. 2014; 68: 58-66.
34. Markoulidis F, Lei C, Lekakou C. Fabrication of high-performance supercapacitors
based on transversely oriented carbon nanotubes. Applied Physics A: Materials
Science and Processing. 2013; 111: 227-236.
35. Lei C, Lekakou C. Activated carbon–carbon nanotube nanocomposite coatings for
supercapacitor application. Surface and Coatings Technology. 2013; 232: 326-330.
36. Lei L, Amini N, Markoulidis F, et al. Activated carbon from phenolic resin with
controlled mesoporosity for an electric double-layer capacitor (EDLC). Journal of
Materials Chemistry A. 2013; 1: 6037-6042.
LIST OF TABLES
Table 1. Key performance indicators of the electrochemical and mechanical
performance of composite structural supercapacitors and also the electrochemical
performance of the corresponding supercapacitor with only the liquid electrolyte
LIST OF FIGURES
Figure 1. Schematic of the VARTM process for the impregnation of the electrolyte-
epoxy mixture into the EDLC mounted on a flat glass plate.
Figure 2. Nyquist plots of the EIS data for EDLCs of an area of 16 cm2: (a) electrolyte
1 M TEABF4/PC; (b) epoxy: electrolyte 1 M TEABF4/PC at 1:2 w/w; (c) epoxy:
electrolyte 1 M TEABF4/PC at 1:1 w/w; (d) epoxy: electrolyte 1 M TEABF4/PC at 2:1
w/w.
Figure 3. Cyclic Voltammograms for EDLC cell of 72.16 cm2 with 1:2 w/w epoxy:
electrolyte 1M TEABF4/PC.
Figure 4. Results of the galvanostatic charge-discharge tests for: (a) the EDLC of 16
cm2 with 1M TEABF4/PC electrolyte; (b) the EDLC of 72.16 cm2 with 1:2 w/w epoxy:
electrolyte 1M TEABF4/PC.
Figure 5. Ragone plots from the discharge phase of the galvanostatic charge-discharge
data for: (a) the EDLC with 1M TEABF4/PC electrolyte; (b) the EDLC with 1:2 w/w
epoxy: electrolyte 1M TEABF4/PC.
Figure 6. Mechanical three-point bend test data for: (a) 1:2 and 1: 1 w/w, (b) 2:1 w/w
epoxy: electrolyte 1 M TEABF4/PC composite specimens.
TABLES
Table 1. Key performance indicators of the electrochemical and mechanical performance of composite structural supercapacitors and also the electrochemical performance of the corresponding supercapacitor with only the liquid electrolyte
Epoxy:1M
TEABF4/PC w/w
ESR
cm2)
Cel,sp
@ 10mHz (F g-1)
Cel,sp
@ 0.0625 mA cm-2 (F g-1)
Flexural modulus
Ef
(GPa)
Flexural strength
fm
(MPa)
0:1 12.8 83 121.5
1:2 160 94 x10-3 4.6x10-3 0.3 29.1
1:1 3.2x103 26x10-3 0.6 36.7
2:1 880x103 1.8x10-3 24.1 1357
FIGURES
Figure 1. Schematic of the VARTM process for the impregnation of the electrolyte-
epoxy mixture into the EDLC mounted on a flat glass plate.
(a)
(b)
(c)
(d)
Figure 2. Nyquist plots of the EIS data for EDLCs of an area of 16 cm2: (a) electrolyte
1 M TEABF4/PC; (b) epoxy: electrolyte 1 M TEABF4/PC at 1:2 w/w; (c) epoxy:
electrolyte 1 M TEABF4/PC at 1:1 w/w; (d) epoxy: electrolyte 1 M TEABF4/PC at 2:1
w/w.
Figure 3. Cyclic Voltammograms for EDLC cell of 72.16 cm2 with 1:2 w/w epoxy:
electrolyte 1M TEABF4/PC.
(a)
(b)
Figure 4. Results of the galvanostatic charge-discharge tests for: (a) the EDLC of 16
cm2 with 1M TEABF4/PC electrolyte; (b) the EDLC of 72.16 cm2 with 1:2 w/w epoxy:
electrolyte 1M TEABF4/PC.
(a)
(b)
Figure 5. Ragone plots from the discharge phase of the galvanostatic charge-discharge
data for: (a) the EDLC with 1M TEABF4/PC electrolyte; (b) the EDLC with 1:2 w/w
epoxy: electrolyte 1M TEABF4/PC.
(a)
(b)
Figure 6. Mechanical three-point bend test data for: (a) 1:2 and 1: 1 w/w, (b) 2:1 w/w
epoxy: electrolyte 1 M TEABF4/PC composite specimens.