Tailored Mesoporous Carbon/Vanadium Pentoxide Hybrid Electrodes for High Power Pseudocapacitive Lithium and Sodium Intercalation

Article abstract of DOI:10.1021/acs.chemmater.7b02533

In this study, atomic layer deposition (ALD) is employed to synthesize hybrid electrode materials of especially tailored mesoporous carbon and vanadium oxide. The highly conformal and precise character of ALD allowed for depositing up to 65 mass % of vanadium oxide inside the 5-20 nm mesopores of the carbon particles, without substantially obstructing internal surface area. The deposited phase was identified as orthorhombic V₂O₅, and an increasing crystalline order was detected for higher mass loadings. Employing the hybrid material as lithium and sodium intercalation hosts at a rate of 0.5C yielded specific capacities of 310 and 250 mAh/g per V₂O₅, respectively, while showing predominantly pseudocapacitive behavior, that is, capacitor-like voltage profiles. C-rate benchmarking revealed a retention of about 50% of the maximum capacity for both lithium and sodium at a high rate of 100C. When testing for longevity in lithium-containing electrolyte, a steadily increasing capacity was observed to 116% of the initial value after 2000 cycles. In sodium electrolyte, the capacity faded to 75% after 2000 cycles, which represents one of the most stable performances for sodium intercalation in the literature. Homogeneously distributed vanadium oxide that is locally confined in the tailored carbon mesopores was identified as the reason for enhanced cyclability and rate behavior of the hybrid material.

Full text of DOI:10.1021/acs.chemmater.7b02533

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Article
Tailored Mesoporous Carbon/Vanadium Pentoxide Hybrid Electrodes
for High Power Pseudocapacitive Lithium and Sodium Intercalation
Simon Fleischmann, Desirée Leistenschneider, Valeria Lemkova,
Benjamin Krüner, Marco Zeiger, Lars Borchardt, and Volker Presser
Chem. Mater., Just Accepted Manuscript • DOI: 10.1021/acs.chemmater.7b02533 • Publication Date (Web): 27 Sep 2017
Downloaded from http://pubs.acs.org on September 28, 2017
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Tailored Mesoporous Carbon/Vanadium Pentoxide
Hybrid Electrodes for High Power Pseudocapacitive
Lithium and Sodium Intercalation
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Simon Fleischmann, Desirée Leistenschneider, Valeria Lemkova,
1
,2
1,2
3,*
1,2,*
Benjamin Krüner, Marco Zeiger, Lars Borchardt, and Volker Presser
1
2
3
INM - Leibniz Institute for New Materials, 66123 Saarbrücken, Germany
Department of Materials Science and Engineering, Saarland University, 66123 Saarbrücken, Germany
Department of Inorganic Chemistry, Technische Universität Dresden, Bergstraße 66, 01062 Dresden,
Germany
*
Corresponding authors’ eMails: LB: lars.borchardt@tu-dresden.de; VP: volker.presser@leibniz-inm.de
Abstract
In this study, atomic layer deposition (ALD) is employed to synthesize hybrid electrode materials of
especially tailored mesoporous carbon and vanadium oxide. The highly conformal and precise
character of ALD allowed for depositing up to 65 mass% of vanadium oxide inside the 5-20 nm
mesopores of the carbon particles, without substantially obstructing internal surface area. The
2 5
deposited phase was identified as orthorhombic V O and an increasing crystalline order was
detected for higher mass loadings. Employing the hybrid material as lithium and sodium intercalation
hosts at a rate of 0.5C yielded specific capacities of 310 mAh/g and 250 mAh/g per V O , respectively,
2
5
while showing predominantly pseudocapacitive behavior, that is, capacitor-like voltage profiles. C-
rate benchmarking revealed a retention of about 50 % of the maximum capacity for both lithium and
sodium at a high rate of 100C. When testing for longevity in lithium electrolyte, a steadily increasing
capacity was observed to 116 % of the initial value after 2,000 cycles. In sodium electrolyte, the
capacity faded to 75 % after 2,000 cycles, which represents one of the most stable performances for
sodium intercalation in literature. Homogenously distributed vanadium oxide that is locally confined
in the tailored carbon mesopores was identified as the reason for enhanced cyclability and rate
behavior of the hybrid material.
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1. Introduction
Fast-responding electrochemical energy storage (EES) is a key enabling technology for the transition
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from fossil to renewable energy sources. Electrical double-layer capacitors (EDLCs) rapidly store
energy via electrical double-layer formation at the charged interface of high surface area carbon
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electrodes and the electrolyte. They provide high specific power, charge efficiency, and stable
cycling behavior over many thousands of cycles owing to their purely physical charge storage
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mechanism of electrosorption. However, the specific capacitance of EDLCs is intrinsically limited to
2
4-5
about 0.1 F/m because of a minimum pore size accessible to the electrolyte ions. Among the best
known electrode materials for EDLCs are activated carbons (ACs) and carbide-derived carbons
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(CDCs), which offer a high specific surface area (SSA) of over 2000 m /g, related to their intraparticle
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microporosity. Carbon nanomaterials such as carbon nanotubes (CNTs) or carbon onions
can
offer even higher specific power, as their exclusively external surface area provides easier access for
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the electrolyte ions.
A promising route to enhance the specific energy of EDLCs is the hybridization of carbon electrodes
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,
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with faradaic materials.
Most prominently, layered metal oxides such as V
2
O
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x 2
V Ti1-xO ,
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,
0-21
22-23
24-25
Nb
2
O
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or MnO
2
have been employed, but also sulfur
and transition metal
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dichalcogenides recently found application in hybrid electrodes. Layered electrode materials
typically store energy via ion intercalation reactions in the interlayer space. In recent years, sodium
intercalation hosts for batteries and hybrid supercapacitor devices are explored as an alternative to
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lithium, because of the lower cost and natural abundance of sodium.
The substitution with
sodium is a crucial requisite on the path towards more sustainable energy storage systems, as the
2
9
availability of lithium is geographically limited to few local monopolies. Vanadium pentoxide has
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been widely studied as an intercalation host for lithium ions,
however, only few studies were
aerogel as
cathode and anode material in sodium batteries, yielding performances of about 150 mAh/g and
00 mAh/g, respectively, at low rates of C/10 and stable cycling over 200 cycles. Hybridizing carbon
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conducted on the intercalation behavior of sodium ions.
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Moretti et al. employed V O
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2
with vanadium oxide brings synergistic effects concerning rate handling and longevity of the
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material,
but so far, to the best of our knowledge, only one study exists on V
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O /carbon hybrids as
2 5
sodium intercalation hosts. Chen et al. studied layer-structured V O
/CNT hybrids mixed with
conductive additive and demonstrated pseudocapacitive charge storage behavior in sodium
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containing electrolyte. However, neither the influence of vanadium oxide loading nor half-cell
stability were investigated, creating the need for more thorough studies on high power sodium
intercalation electrodes.
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By implementing nanoscopic layers or clusters of ion intercalation materials into the conductive
carbon network, a high power handling can be maintained owing to rapid electron transport and
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short diffusion paths for the ions to the reactive sites. A major challenge for the synthesis of hybrid
electrodes is achieving a homogenous distribution of the Faradaic material throughout the carbon
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matrix. Therefore, appropriate synthesis techniques for metal oxide decoration have to be
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employed, which include atomic layer deposition (ALD),
wet-chemical approaches,
or
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vacuum infiltration . ALD is a vapor phase deposition technique with enhanced thickness control and
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layer conformity due to its cyclic and self-limiting characteristics. It has emerged as an advanced
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method to decorate nanomaterials with metal oxides at molecular precision. To ensure complete
accessibility for the metal oxide coating, carbons with exclusively external surface area such as CNTs,
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graphene, or carbon onions are preferred as substrates,
even though their SSA is inferior to
activated carbons with internal porosity. In theory, high SSA porous carbons as substrates would
allow to create larger interfaces between redox active coating and electrolyte. However, several
studies hybridized microporous carbon with metal oxides, but the attempts were unsuccessful due to
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pore blocking, or showed only little effect because micropores were inaccessible to the metal oxide
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precursors .
In a recent study, we compared the suitability of carbons with external (carbon onions) and internal
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surface area (AC) as substrates for atomic layer deposited vanadium oxide. Our data showed that
AC can accommodate small mass loadings of vanadium oxide, but loadings exceeding about
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0 mass% lead to an obstruction of micropores below 1 nm, leading to inaccessibility of internal
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surface area to the electrolyte. Our present study explores for the first time a tailored mesoporous
carbon (TMC) as an advanced nanoporous carbon substrate that combines high internal surface area
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with pore volume accessible for ALD. The spherical pores are interconnected, uniform in size and
allow for a homogenous precursor adsorption during the ALD process and a high accessibility during
2
electrochemical cycling. TMC is synthesized via hard-templating using SiO nanoparticles, which are
removed by hydrofluoric acid, leaving spherical mesopores in the size of the former nanoparticles.
Herein, we employ TMC for hybridization with a metal oxide, namely vanadium oxide, via atomic
layer deposition. The resulting hybrid electrode will be structurally analyzed and comparatively
benchmarked for rate behavior and longevity as lithium and sodium intercalation hosts by
electrochemical half-cell experiments.
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2. Experimental
2.1. Preparation of carbon substrate electrodes
Firstly, 10 nm SiO
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nanoparticles have been synthesized by a modified Stöber method of Watanabe
et al. Therefore, 0.4 g L-arginine (Roth) have been dissolved in 400 g deionized water. After adding
3.94 g of tetraethylorthosilicate (TEOS, Sigma Aldrich) the mixture was stirred at 1000 rpm for 24 h
at 70 °C. After cooling down and solvent removal, the nanoparticles were calcinated in air at 550 °C
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for 3 h. Then, to obtain the mesoporous carbon, 3.0 g of the SiO nanoparticles were dispersed in a
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solution of 1.5 g sucrose (Roth) in 10 mL water and 0.3 g of H SO (95 mass% aqueous solution,
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Fischer Scientific) were added as a catalyst for the polymerization of the carbon precursor. The
dispersion was kept at 100 °C for 3 h and at 160 °C for another 3 h. The obtained polymer-SiO
composite was carbonized under argon atmosphere (flow rate 150 mL/min) at 900 °C for 2 h with a
heating rate of 150 °C/min. In the last step, the SiO nanoparticles have been removed by a
treatment with hydrofluoric acid (38-40 mass%, Merck) in ethanol and water (volume ratio: 1:1:1) for
4 h. After washing three times with water, the mesoporous carbon was received.
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Free-standing TMC electrodes were prepared by dispersion of the carbon powder in ethanol and
admixing of 10 mass% polytetrafluorethylene (PTFE, 60 mass% aqueous solution, Sigma Aldrich) in a
mortar. After thorough mixing, a dough-like mass was obtained and rolled to ca. 50 µm thick
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electrodes, which were dried in a vacuum oven (2·10 Pa) at 120 °C overnight prior to further use. A
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more detailed description of the electrode preparation procedure can be found in Ref. .
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.2. Plasma-enhanced atomic layer deposition of vanadium oxide
Plasma-enhanced atomic layer deposition (PEALD) was performed directly onto the free-standing
TMC electrodes with an open-load atomic layer deposition system (OpAL; Oxford Instruments).
Vanadium oxide was synthesized from vanadium(V)-oxytriisopropoxide (VOTIP; SAFC Hitech) as
metalorganic precursor and oxygen plasma as reactant gas. The VOTIP pot was preheated to 45 °C
and bubbled by argon carrier gas to deliver the precursor to the reaction chamber. In a typical PEALD
cycle, VOTIP was dosed for 20 s and the chamber pressure was set to 66.7 kPa, before argon was
used to purge the reactor for 10 s. Then, oxygen was introduced to the chamber and the pressure
was set to 21.3 kPa, before remote plasma with a power of 300 W was ignited and applied for 60 s.
At the end of each cycle, the reactor was evacuated for 8 s. Prior to the coating process, oxygen
plasma was applied for 10 min to the electrodes to create suitable surface functionalities, yielding a
more homogenous precursor adsorption during the first PEALD cycle. The table temperature inside
the reactor was kept at 180 °C. The free-standing electrodes were arranged on a sample holder that
allows precursor penetration from both sides. This way, a homogenous precursor penetration along
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the entire thickness of the electrodes is ensured. The nomenclature of the samples indicates the
number of PEALD cycles applied; for example, sample TMC+100VOx was coated with 100 PEALD
cycles of vanadium oxide.
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.3. Structural characterization
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Scanning electron microscopy (SEM) was conducted using a JSM-7500F (JEOL) with an operating
voltage of 3 kV. Energy dispersive X-ray spectroscopy (EDX) was used to determine the elemental
composition with an X-Max-150 (Oxford Instruments) attached to the SEM chamber. The spectra
were recorded at 10 kV.
Transmission electron microscopy (TEM) was carried out using a 2100F system (JEOL) at an operating
voltage of 200 kV. For sample preparation, electrodes were dispersed in isopropanol by tip sonication
and placed on a copper grid with lacey carbon film (Gatan Inc.).
For thermogravimetric analysis (TGA), a TG 209 F1 Libra system (Netzsch) was used. The samples
with masses of around 10 mg were heated in alumina crucibles in synthetic air atmosphere (flow
rate: 20 sccm) to 650 °C with a heating rate of 5 °C/min. The mass retention was used to derive the
metal oxide content of the samples. The relative mass gain was calculated by dividing the metal
oxide mass by the mass of the electrode prior to PEALD.
For X-ray diffraction (XRD) measurements, a D8 Advance XRD (Bruker AXS) diffractometer, calibrated
with a corundum standard, was used. It employed a copper X-ray source (Cu , 40 kV, 40 mA), a
Kα
Göbel mirror, a 0.5 mm point focus and a two-dimensional detector (VANTEC-500). The detector
covered a 2θ-range of about 20° and was positioned at 20°, 40°, and 60° 2θ for 17 min measurement
steps. The diffractograms were derived by integration of the areal intensities with a step width of
0
.02° 2θ.
Raman measurements were performed with a Renishaw inVia Raman Microscope employing an Nd-
YAG laser with an excitation wavelength of 532 nm. A grating with 2400 lines/mm and a 50x
-1
objective (numeric aperture: 0.9) were used to reach a spectral resolution of about 1.2 cm . The
laser spot on the sample was about 1 µm in diameter at a power of 0.05 mW. Spectra were recorded
with 10 accumulations and 30 s acquisition time.
An Autosorb iQ System from Quantachrome was used for nitrogen gas sorption analysis (GSA) on
free-standing electrode samples with masses of ca. 20 mg. Electrodes were degassed at 150 °C for
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0 h at 100 Pa, before being measured with liquid nitrogen (-196 °C) in a relative pressure range from
-
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·10 to 1.0 in 68 steps. The SSA was calculated via Brunauer-Emmett-Teller (BET) equation in the
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linear pressure range using ASQwin software. Quenched-solid density functional theory (QSDFT)
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with a slit-cylindrical-spherical pore model was employed to derive the pore size distribution (PSD)
and the total pore volume.
2.4. Electrochemical characterization
The electrochemical characterization was performed in a custom-built three-electrode setup (half-
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cell), as it has been described in Ref. . In short, TMC/vanadium oxide hybrids with a mass of 1.5-
mg were employed as working electrodes and an oversized PTFE-bound AC electrode (type YP-80F,
2
Kuraray, 5 mass% PTFE, total mass ca. 15 mg) was used as counter electrode, separated by a 13 mm
glass fiber disc (GF/A, Whatman). As current collectors, 12 mm diameter carbon-coated aluminum
foil (Zflo 2653, Exopack Technologies) was employed. Instead of the conventionally used lithium
reference in carbonate-based electrolytes, AC (type YP-50F, Kuraray) was employed as a quasi-
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reference electrode because of the instability of acetonitrile in the presence of metallic lithium.
3
The cells were dried in a vacuum oven (2·10 Pa) prior to electrolyte filling at 120 °C overnight, before
being transferred to an argon filled glove box (MBraun Labmaster 130, O
being vacuum-backfilled with 1 M LiClO and 1 M NaClO in acetonitrile (Sigma Aldrich) as
electrolytes. Acetonitrile was chosen as a solvent because of its increased ionic conductivity as
2 2
and H O < 1 ppm) and
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compared to carbonate-based electrolytes, making it more attractive for high-power applications.
For electrochemical measurements, cyclic voltammetry (CV) and galvanostatic cycling with potential
limitation (GCPL) were carried out with a potentiostat/galvanostat (VSP300, Bio-Logic). CVs were
recorded in a potential range from -1.2 V to +1.0 V vs. carbon at a scan rate of 1 mV/s. Galvanostatic
cycling was performed in the same potential range with specific currents between 0.05-20 A/g and C-
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rates between 0.5C-50C (for LiClO electrolyte: 1C = 0.167 A/g, for NaClO electrolyte: 1C = 0.107 A/g)
respectively, all normalized to the mass of the working electrodes including carbon and vanadium
oxide, but excluding PTFE-binder. The specific (gravimetric) capacity Csp was calculated from the GCPL
data by integration of the cathodic current over the time by Eq. 1:
ꢇ
ꢇꢈ
ꢃ
ꢄꢅꢆ
ꢀꢁꢂ
=
(Eq. 1)
ꢉ
where I is the cathodic current, t the step time, and m the mass of the working electrode including
carbon and vanadium oxide, but excluding PTFE-binder.
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3. Results and discussion
3.1. Structural characterization
The synthesis process of the TMC/vanadia hybrids is illustrated in Fig. 1A. In a first step, the sucrose
matrix surrounding the spherical SiO particles is carbonized, before the silica particles are removed
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from the carbon matrix via hydrofluoric acid treatment. Porous carbon is formed with primary
particle sizes between 0.5-2.0 µm (Fig. 1B). The carbon particles show a high inner porosity with a
uniform distribution of mesopores in the size range of the former silica particles that are engulfed by
microporous carbon shells, as can be seen by TEM in Fig. 1C. When applying PEALD coating to TMC,
no direct changes to the primary particles are visible by SEM (Fig. 1D), but vanadium oxide mainly
forms in the mesopore volume inside the TMC particles, as can be observed in the TEM image in
Fig. 1E (exemplified for TMC+150VOx, images of the remaining hybrid samples are found in Fig. S1A-
C). This confirms the original assumption that mesopores of this size are well accessible to the PEALD
process.
To determine the vanadium oxide mass in the hybrid electrodes, thermogravimetric analysis is
conducted and the results are shown in Fig. 2A. By heating in synthetic air up to 650 °C, all non-
vanadia species, that is, carbon and PTFE-binder, are burned off. The observed mass loss up to a
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temperature of about 120 °C is caused by evaporation of adsorbed surface water and has to be
considered when calculating the composition of the electrode. The mass retentions are determined
to 23 mass%, 48 mass%, 52 mass%, and 64 mass%, leading to dry electrode vanadium oxide contents
of 24 mass%, 51 mass%, 56 mass%, and 65 mass% for samples coated with 50, 100, 150, and 200
PEALD cycles, respectively. The electrode composition has to be calculated in the dry state that is
representative of the electrodes’ electrochemical testing conditions. The mass increase due to
vanadium oxide coating increases linearly per PEALD cycle number, as can be seen in Fig. 2B. This
behavior corresponds with an ideal PEALD process and is typical for coating exohedral carbon
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substrates, that is, carbons with exclusively external surface area. In contrast, when coating
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carbons with high inner particle porosity (such as activated carbon), we would observe a saturation
1
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in mass gain with increased number of PEALD cycles. This saturation is related to blocking of
internal surface area by growing layers of the coating, making less surface area accessible for further
1
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ALD precursor adsorption. The fact that no saturation in mass gain is observed clearly shows that
the pore volume remains highly accessible to the reagents and substantial blocking of the internal
surface area is avoided when coating TMC via PEALD.
A quantitative examination of the porosity and pore size distribution of TMC and TMC/vanadium
oxide hybrids is carried out via nitrogen gas sorption analysis (GSA). The adsorption/desorption
isotherms of all samples are shown in Fig. 3A. As-synthesized TMC shows an isotherm shape of type
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IV(a), with an additional steep increase of adsorbed volume in the low pressure range resembling a
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type I(b) shape, according to the 2015 IUPAC classification. The steep increase at low relative
pressure is associated with micropores and small mesopores below 2.5 nm, which are found in the
microporous carbon shells surrounding the mesopores. The remaining isotherm shows a distinct
hysteresis loop that is associated with well-defined mesoporosity. The TMC/vanadium oxide hybrid
samples show the same isotherm shape, except for the steep increase at low pressure, which
indicates the occupation of small micropores by the coating. This, though, does not obstruct the
accessibility of mesopores, as evidenced by hysteresis loops observed for all coated samples. The
hysteresis shape can best be described by type H1, characteristic for ordered mesoporous materials.
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Additional contribution of H2 is present, typical for cavitation-like mesopores in the structure
related to spherical pores with narrow pore necks. Even though the shape of the isotherms is similar
for all samples, the magnitude of specific adsorbed volume decreases for higher coating thicknesses.
The reasons for this behavior are (1) the growing electrode density with higher mass loadings of
vanadium oxide that is heavier than carbon and (2) the decreasing total pore volume associated with
gradual vanadium oxide filling.
These qualitative observations are confirmed by quantitative SSA values derived from both BET and
QSDFT models, as well as the specific pore volume calculated by QSDFT (Table 1). The SSABET of TMC
2
2
electrodes is around 1000 m /g and decreases to 421, 290, 164, and 186 m /g for 50, 100, 150, and
00 ALD cycles of vanadium oxide coating, respectively. The decrease of SSA is, on the one hand,
2
related to the additional mass of vanadium oxide that does not bring any additional surface area, and
on the other hand to the blocking of micropores that can already be observed after 50 ALD cycles.
The cumulative pore volume as a function of the pore width derived by QSDFT (Fig. 3B) shows a
3
micropore volume of about 0.13 cm /g for uncoated TMC (that is about 10 % of the total pore
volume) and significantly smaller values for all coated TMC/vanadium oxide hybrid samples. The
largest fraction of pore volume is formed by mesopores in the range of about 6-25 nm for uncoated
3
TMC up to a pore volume about 1.3 cm /g. The specific pore volume of hybrid samples decreases to
3
0
.74, 0.54, 0.3, and 0.21 cm /g for 50, 100, 150, and 200 ALD cycles, respectively, because of
additional mass and gradual filling of the pore volume with vanadium oxide.
Raman spectra of TMC and TMC/vanadium oxide samples are recorded and given in Fig. 4A. All
spectra exhibit the characteristic D- and G-peaks of carbon, however, a clear shift to higher vibration
-
1
frequencies is observed for the D-peak (1336-1360 cm ) and to a smaller extent for the G-peak
-1
(
1605-1610 cm ) when comparing uncoated to coated samples (dashed line in Fig. 4A). This blueshift
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2
has been described by Ferrari et al. for disordered graphite and was recently traced back to surface
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stresses introduced by non-epitaxially grown ALD layers on the carbon substrate. Furthermore,
TMC/vanadium oxide hybrid electrodes exhibit several peaks characteristic for vanadium oxide.
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Depending on the coating thickness, the observed peaks vary in position and shape. Samples
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TMC+150VOx and TMC+200VOx show typical sharp signals of V O , which broaden and shift
2
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significantly for TMC+50VOx and TMC+100VOx. Peak broadening as well as wavenumber shifting are
an indication for smaller domain sizes of vanadium oxide in these samples in agreement with
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literature for nanometer-sized metal oxide structures because of phonon confinement.
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X-ray diffraction was carried out for a complementary confirmation of the vanadium oxide oxidation
state (Fig. 4B). All diffractograms exhibit a peak at 18.5° 2θ associated with the PTFE binder according
to PDF 54-1595 and a broad shoulder around 25.5° 2θ from amorphous carbon. The relative intensity
of this shoulder decreases for higher coating thicknesses because of the decreasing carbon content
of the samples. The vanadium oxide phase of TMC+150VOx and TMC+200VOx is clearly found to be
2 5
orthorhombic V O in Pmmn space group, according to PDF 41-1426. Like the observations made in
the Raman section, these peaks broaden and decrease in intensity for TMC+50VOx and TMC+100VOx
because of nanoscopic domain sizes in the confined mesopore space.
3
.2. Electrochemical characterization
Electrochemical measurements of TMC/vanadium oxide hybrid electrodes were carried out in both
lithium and sodium containing electrolytes; namely, 1 M LiClO and 1 M NaClO both dissolved in
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ACN. Cyclic voltammetry (CV) in lithium electrolyte was performed using TMC and TMC/vanadium
oxide electrodes as working electrodes in a half-cell setup (Fig. 5A). Uncoated TMC electrodes exhibit
a rectangular CV signal characteristic for the purely capacitive charge storage mechanism of porous
3
carbon materials.
TMC coated with vanadium oxide shows significantly enhanced charge storage capacity, specifically
in the negative potential range, where several mechanisms are contributing to the overall charge
storage. The enhanced current signal can be divided into two contributions: (1) An enlarged
rectangular signal and (2) two small pairs of redox peaks that become more stretched out and show
larger potential gaps between cathodic and anodic scan with increasing coating thickness. The
rectangular signal originates, to the most part (besides a small capacitive contribution from the
carbon substrate), from pseudocapacitive lithium intercalation reactions that have been described
40
2 5
for nanocrystalline V O in literature. Pseudocapacitance describes Faradaic charge storage
exhibiting a capacitor-like electrical response in form of a rectangular CV signal and a sloping voltage
6
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profile. Pseudocapacitive intercalation causes no phase transformation of the host lattice and can
occur in parts of the nanometer-sized V O coatings where intercalation kinetics are no longer limited
2
5
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0
by solid-state diffusion. Diffusion-limited, battery-like lithium intercalation, that is, Faradaic charge
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storage exhibiting a plateau in the voltage profile, is observed to a smaller extent and occurs with a
redox peak at around -0.6 V vs. carbon in the cathodic scan for samples TMC+50VOx and
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TMC+100VOx. This peak becomes broader and is shifted towards lower potentials for samples
TMC+150VOx and TMC+200VOx as a result of decreased electrical conductivity and longer diffusion
paths for lithium ions caused by higher coating thicknesses. The reaction mechanism of lithium
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intercalation in vanadium pentoxide is typically described by Eq. 2:
ꢒ
ꢔ
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ꢊ ꢌ + ꢎꢏꢐꢑ + ꢎꢏꢓ ꢎ↔ ꢐꢑ ꢊ ꢌ ꢎ
(Eq. 2)
ꢋ
ꢍ
ꢕ ꢋ ꢍ
with x representing the mole fraction of intercalated lithium ions.
A quantitative assessment of the specific capacity and rate handling was conducted by galvanostatic
cycling at various currents (Fig. 5B). It should be noted that all capacity values are given with respect
to the combined mass of carbon and vanadium oxide. While uncoated TMC exhibits a maximum
specific capacity of 60 mAh/g, ALD coating with 50 cycles already increased the maximum capacity to
100 mAh/g. For higher mass loadings of vanadium oxide, the capacity increased up to a maximum
value of about 210 mAh/g for TMC+200VOx. When analyzing the rate behavior, it is evident that
higher vanadium oxide loadings lead to quicker capacity fading at higher rates. The reason for this
behavior is the decreasing electrode conductivity as well as longer diffusion paths for lithium ions to
the reactive sites. The specific capacity of TMC+150VOx drops to 25 mAh/g at 10 A/g, whereas
TMC+200VOx drops to 14 mAh/g already when cycling at 5 A/g. Sample TMC+100VOx offers a good
compromise of capacity and rate handling by showing a maximum of about 170 mAh/g with a
retention of almost 60 mAh/g at a high rate of 20 A/g (corresponding to a rate of 118C).
Consequently, depending on the application, the desired properties in terms of maximum capacity or
high rate behavior can be tailored by adjusting the number of ALD cycles. The Coulombic efficiency of
all samples is above 97 % at low rates and 100 % at high rates (Fig. 5C).
Cyclic voltammetry of TMC/vanadium oxide electrodes was further carried out in sodium containing
electrolyte (Fig. 5D). All CVs are found to exhibit a rather rectangular signal with a slightly increasing
current in the negative potential range during the cathodic scan. No major differences in shape or
magnitude are visible between all coated samples, except for a more pronounced resistive knee
during polarization change for higher vanadium oxide loadings, which is a consequence of higher
electrode resistivity. The absence of any distinct redox peak indicates exclusively pseudocapacitive
sodium intercalation in TMC/vanadium oxide hybrid electrodes, which aligns with previous reports
3
6, 39
on bi-layered V
2
O
5
.
This study demonstrates stable pseudocapacitive sodium intercalation
host lattice. The intercalation of sodium in the
behavior for the first time in an orthorhombic V
2
O
5
3
9
vanadium oxide structure is described by Eq. 3:
ꢒ
ꢔ
ꢊ ꢌ + ꢎꢏꢖꢗ + ꢎꢏꢓ ꢎ↔ ꢖꢗ ꢊ ꢌ ꢎ
(Eq. 3)
ꢋ
ꢍ
ꢕ ꢋ ꢍ
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The specific capacity of TMC/vanadium oxide electrodes is analyzed by galvanostatic cycling (Fig. 5E),
the associated coulombic efficiencies are well above 90 % and given in Fig. 5F. The maximum
capacity for all hybrid electrodes, independent of the vanadium oxide loading, is almost identical
with values between 102-107 mAh/g. This is in clear contrast to the behavior in lithium containing
electrolyte, where the maximum capacity scales with the vanadium oxide content of the hybrid
electrode. The observation can be attributed to two reasons: (1) To a small extent, there is a higher
double-layer contribution to the overall capacity of hybrid electrodes with smaller vanadium oxide
loadings, since they exhibit slightly higher specific surface areas. However, considering the rapid
decrease of micropore volume already seen for TMC+50VOx, this contribution is relatively low. (2) To
a larger extent, not the entire volume of the vanadium oxide coating contributes towards charge
storage: sodium appears not to reach all possible reactive sites but only intercalates to a certain
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extent into thicker orthorhombic V
2
O
5
structures. This can be understood by considering the larger
34
ionic radius of sodium with 1.02 Å compared to 0.76 Å for lithium. When cycling at higher rates, the
capacity decreases most rapidly for TMC+200VOx; the highest retention is observed for TMC+50VOx
with 51 mAh/g at 20 A/g (corresponds to 187C). Qualitatively, this is the same trend as in lithium
electrolyte and a consequence of increasing electrode resistivity with higher vanadium oxide loading.
It should be noted that the specific capacities in sodium electrolyte at high rates are on the same
+
level as in lithium electrolyte, despite the larger ionic radius of Na . The reason is the exclusively
pseudocapacitive intercalation mechanism of sodium, which is not limited by solid state diffusion.
To quantitatively separate pseudocapacitive and battery-like intercalation for both electrolyte
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systems, a kinetic analysis as proposed by Dunn et. al is carried out. Therefore, CVs of TMC+100VOx
samples are recorded in both lithium and sodium containing electrolytes at scanning rates between
1
0-500 mV/s (Supporting Information, Fig. S2A-B) and the cathodic current at a fixed potential
of -0.75 V vs. carbon is traced at every scan rate. By logarithmic plotting of the current over the
logarithmic scan rate, a linear relation is observed (Supporting Information, Fig. S2C). A slope of 0.5 is
typically associated with ideal battery-like, solid state diffusion limited charge transfer, whereas a
6
9-70
slope of 1.0 corresponds to an ideal capacitive behavior that is not diffusion limited.
In lithium
electrolyte, a slope of 0.62 is calculated, being in line with a mixed battery-like and pseudocapacitive
behavior. Contrarily, in sodium electrolyte, a slope of 0.92 corresponds to an almost ideal
(pseudo-)capacitive behavior, thereby underlining the reasoning for the good rate behavior of larger
+
Na .
Finally, TMC+100VOx hybrid electrodes will be subjected to C-rate and stability benchmarking to
provide a better comparability to state-of-the-art literature (Table 2). When considering the
performance with a lithium electrolyte, a maximum capacity of about 150 mAh/g at a rate of 0.5C is
observed (310 mAh/g when normalizing to the vanadium oxide content of the electrode) (Fig. 6A).
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This value is in the range of other state-of-the-art V O cathode materials. When increasing the
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cycling rate up to 100C, TMC+100VOx shows a capacity retention of 46 % compared to the initial
value. In the sodium electrolyte, a maximum specific capacity of 120 mAh/g is measured at 0.5C
(
250 mAh/g normalized to V
based cathodes in literature. In addition, an attractive 51 % capacity retention of the maximum
value is observed when cycling at 100C. The good rate behavior in both electrolytes is caused by the
homogenously distributed, nanoscopic V clusters and the consequential large interface to the
2 5
O content) (Fig. 6B), which is already among the highest reported for
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electrolyte, owing to the TMC substrate that additionally provides a superior electric conductivity.
The longevity of the electrodes is monitored by cycling TMC+100VOx electrodes in lithium and
sodium containing electrolytes at a rate of 10C (Fig. 6C). In lithium electrolyte, no capacity fading is
observed after 2,000 charge/discharge cycles. Contrarily, the capacity even increased slightly to
1
16 % of the initial value. A similar behavior was observed in a previous study on vanadium
oxide/activated carbon hybrid electrodes, where a rising capacity after several thousand cycles was
1
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linked to a partial clearance of previously blocked micropores, and the present study confirms this
trend for hybrid materials employing endohedral porous carbon. For sodium containing electrolyte,
very small, constant capacity fading is observed over 2,000 cycles to a retention of about 75 % of the
+
+
initial value, related to the higher lattice expansions upon intercalation of larger Na compared to Li .
This is, to the best of our knowledge, the most stable sodium intercalation behavior reported so far
for V
2
O
5
2 5
-based electrodes. Interestingly, orthorhombic V O was previously reported unsuitable for
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sodium intercalation because of rapid capacity fading. The reason for the enhanced stability of the
TMC/vanadium oxide electrodes appears to result from (1) the nanoscopic vanadium oxide layer size
and (2) the confinement of vanadium oxide in spherical mesopores. The nanometer-sized dimensions
of the ALD coating are enabled by the homogenous distribution of TMC pores and contribute
towards a significantly reduced strain formation in the vanadium oxide structure upon intercalation
of large sodium ions. Further, by locally confining vanadium oxide in the mesopore space,
disintegration and the consequential loss of contact with the conductive carbon matrix can be
effectively prevented.
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4. Conclusions
We demonstrated the synthesis of tailored mesoporous carbon / vanadium oxide hybrid electrodes
via atomic layer deposition with varying metal oxide loadings between 24-65 mass%, without
observing substantial pore blocking of the carbon substrate. The coating was identified as
orthorhombic V O , and an increasing crystalline ordering was detected for higher vanadium oxide
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loadings. When employing the hybrid electrodes as lithium and sodium hosts, intercalation was
found to be predominantly pseudocapacitive and maximum capacities of 200 mAh/g for lithium and
1
10 mAh/g for sodium were measured (per electrode mass). Kinetic analysis revealed that sodium
intercalation was less limited by solid state diffusion than lithium, what resulted in an impressive rate
+
behavior for Na , with 51 % retention of the maximum capacity at an ultra-high rate of 100C. Stability
testing showed superior longevity over more than 2,000 charge/discharge cycles, which was
attributed to reduced strain formation in the nanometer-sized ALD coating in the tailored mesopores
and an effective prevention of vanadium oxide disintegration in the confined pore space.
Acknowledgements
The work at INM was part of the Carbon Metal Oxide Nanohybrid project (CarMON) supported by the
Leibniz Association (SAW-2017). VP acknowledges funding from the German Federal Ministry for
Economic Affairs and Energy (BMWi) in support of the HyBaCap project (award number 03ET6113C).
We thank Prof. Arzt (INM) for his continuing support. Financial support from the German Federal
Ministry of Education and Research (BMBF) within the Mechanocarb project (award number
03SF0498) is gratefully acknowledged by LB and DL.
Supporting Information
Transmission electron micrographs and cyclic voltammograms.
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Fig. 1: Schematic illustration of the TMC/vanadium oxide synthesis process (A). Scanning and
transmission electron micrographs of uncoated TMC electrodes (B,C) and TMC/vanadium
oxide hybrid electrodes coated with 150 ALD cycles (D,E).
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Fig. 2: Mass retention of TMC/vanadium oxide hybrid electrode samples measured via
thermogravimetric analysis to 650 °C in synthetic air at a heating rate of 5 °C/min (A).
Relative mass gain of TMC electrodes coated with vanadium oxide via 50, 100, 150, and 200
ALD cycles (B).
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Fig. 3: Nitrogen gas sorption isotherms measured at standard temperature and pressure (A), and
cumulative pore volume of the TMC and TMC/vanadium oxide hybrid electrodes (B). STP:
standard temperature and pressure.
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Fig. 4: Raman spectra of TMC and TMC/vanadium oxide hybrid electrode samples with stars
indicating the ideal peak positions of V
positions of D- and G-peaks (A), as well as X-ray diffractograms of TMC/vanadium oxide
hybrid electrode samples including the ideal peak positions of V and PTFE (electrode
binder) according to PDF 41-1426 and PDF 54-1595, respectively (B).
2 5
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Fig. 5: Cyclic voltammograms of all samples measured at 1 mV/s in LiClO in ACN (A) and NaClO in
ACN (D). Specific capacity of all samples including the coulombic efficiency derived from the
cathodic scan of galvanostatic measurements with specific currents ranging from 0.05-
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Fig. 6: C-rate tests from 0.5C to 100C of sample TMC+100VOx in LiClO in ACN (A), NaClO in ACN
(B), and Cycling stability in both electrolytes at a rate of 10C (C). The rate of 1C was
equivalent to 167 mA/g for Li-containing electrolyte and to 107 mA/g for Na-containing
electrolyte.
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Tables
Table 1: Comparison of SSABET, SSADFT, and total pore volume of TMC and TMC/vanadium oxide
hybrid electrodes.
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SSABET
SSADFT
(m /g)
Pore volume
Material
2
2
3
(
m
/
g)
(cm /g)
TMC
999
421
290
164
186
856
367
247
133
162
1.30
0.74
0.54
0.30
0.21
TMC+50VOx
TMC+100VOx
TMC+150VOx
TMC+200VOx
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Table 2: Literature overview of V O based lithium and sodium intercalation electrodes. The specific
2
5
capacity values are normalized to the “active material”, that means, neglecting the addition
of CB as indicated with brackets. Abbreviations: Onion-like carbon (OLC), activated carbon
(
(
AC), carbon black (CB), acetonitrile (ACN), ethylene carbonate (EC), dimethyl carbonate
DMC), carbon nanotubes (CNT), propylene carbonate (PC).
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Electrode
material
Max. capacity Capacity (mAh/g)
Cycling
stability
Electrolyte
Reference
(mAh/g)
at maximum rate
1
M LiClO
in ACN
4
14
OLC/V
2
O
5
129
68 @ 5 A/g
4,000
8,000
50
1 M LiClO4
in ACN
1
7
4
2
AC/V O5
122
141
21 @ 5 A/g
2
V
2
O
5
nanosheets
+ 20 mass% CB)
Porous C/V
(+ 20 mass% CB)
Graphene/V
+ 15 mass% CB)
1 M LiPF
in EC/DMC
1M LiPF
in EC/DMC
1 M LiPF
in EC/DMC
6
80 @ 8C or
1.2 A/g
(
2
O
5
6
118 @ 64C or
9.4 A/g
31
1
2
40
80
800
2
O
5
6
210 @ 4C or
1.6 A/g
3
2
100
(
1 M LiClO
in ACN
4
60 @ 118C or
20 A/g
TMC/V
2
O
5
170
2,000
This work
CNT/V
(+ 10 mass% CB)
aerogel
+ 20 mass% CB)
V O nanobelts
O
2 5
1 M NaPF
in PC
6
6
No half-
cell data
3
9
1
1
2
10
50
31
67 @ 72C
V
2
O
5
1 M NaPF
in PC
50 @ 4C or
2.24 A/g
36
100
100
(
1 M NaPF6
EC/DMC
2
5
3
3
3
5
134 @ 0.64 A/g
(+ 20 mass% CB)
Amorphous
1 M NaPF
in PC
6
80 @ 5C or
1.17 A/g
170
107
100
2 5
V O
1
M NaClO
in ACN
4
51 @ 187C or
20 A/g
TMC/V
2
O
5
2,000
This work
2
5
ACS Paragon Plus Environment

Chemistry of Materials
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