electrochemical properties of poly(4,4′-diaminodiphenyl sulfone) as a cathode material of lithium...
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ORI GIN AL PA PER
Electrochemical properties of poly(4,40-diaminodiphenyl sulfone) as a cathode materialof lithium secondary batteries
Su-Ryeon Yun • Kwang Man Kim • Jang Myoun Ko •
Yongku Kang • Kwang Sun Ryu
Received: 4 September 2012 / Revised: 3 March 2013 / Accepted: 21 July 2013 /
Published online: 10 August 2013
� Springer-Verlag Berlin Heidelberg 2013
Abstract Doped poly(4,40-diaminodiphenyl sulfone) (pDDS) is prepared for use
as a cathode-active material of lithium secondary batteries by chemical oxidation
method using ammonium persulfate initiator. The synthesized pDDS and doped
pDDS are characterized by chemical structure analysis using Fourier-transform
infrared spectroscopy and X-ray photoelectron spectroscopy. Cyclic voltammetry
shows that the doped pDDS has a typical pair of redox peaks at 3.75/3.15 V vs. Li/
Li?, corresponding to charging/discharging of the lithium ion. The discharge
capacity at low current rate (0.05 C-rate) achieves 31.5 and 24.3 mA h g-1 in the
initial and 50th cycles, respectively. The doped pDDS also shows good cycle per-
formance and high-rate capability, making it appropriate as a cathode material of
lithium secondary batteries.
Keywords Poly(4,40-diaminodiphenyl sulfone) � Cathode material �Electrochemical property � Lithium secondary battery
S.-R. Yun � K. S. Ryu (&)
Department of Chemistry, University of Ulsan, Ulsan 680-749, Republic of Korea
e-mail: [email protected]
K. M. Kim
Power Control Devices Team, Electronics and Telecommunications Research Institute (ETRI),
Daejeon 305-700, Republic of Korea
J. M. Ko
Division of Applied Chemistry and Biotechnology, Hanbat National University, Daejeon 305-719,
Republic of Korea
Y. Kang
Advanced Materials Division, Korea Research Institute of Chemical Technology, Daejeon 305-600,
Republic of Korea
123
Polym. Bull. (2013) 70:3011–3018
DOI 10.1007/s00289-013-1003-3
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Introduction
Since the emergence of conducting polymers, their practical use as active electrode
materials in energy storage devices has been the goal. Conventional conducting
polymers such as polyaniline, polypyrrole, and polythiophene partly succeed in
coin-type Li polyaniline cells, but eventually fail during use due to lower energy
densities (gravimetric and volumetric). This result is expected based on the low
doping ratio of lithium salt and the need for enlarged electrolyte solution [1]. The
study of conducting polymers is focused on conducting polymer derivatives to serve
as optimal electrode materials.
Newly developed conducting polymers, such as polymer of diphenyl sulfone
derivatives, have been studied due to their excellent electronic and mechanical
properties, solution or melt processability, and high environmental stability for
applications such as antibiology [2], electrochromicity and creating compatible
joints with mechanical strength. Of these, 4,40-diaminodiphenyl sulfone (DDS)
monomer and poly(DDS) (pDDS) have been synthesized and structurally analyzed
[3–9]. The pDDS appears particularly promising as a material in electrochromicity
with enhanced adherent characteristics [4], as an energy storage device such as a
capacitor [10] and a promotion agent for photocatalytic reactions [11], due to its
higher conductivity and good solubility in organic compounds such as N,N-dimethyl
formamide and dimethyl sulfoxide. In this respect, it is expected that the pDDS can
be adopted as an electroactive materials by utilizing its high conductivity.
Therefore, it is of interest to examine the electrochemical properties of pDDS as
a cathode-active material of lithium secondary batteries.
In this work, pDDS is prepared by polymerization during a chemical oxidation
process from DDS. The pDDS is applied for the first time to a cathode-active
material in lithium secondary batteries. The resulting pDDS is expected to contain
aniline bonds divided by –S– bonds that are confined along the polymer chains.
Chemical analysis of pDDS is compared with a polyaniline structure to identify the
incorporation of –N–N– links in the chain backbone. Finally, the pDDS electrode
containing aniline and O=S=O groups is fabricated, and its electrochemical
properties including redox behavior and charge/discharge profiles for repeated
cycles are investigated for use as a cathode material of lithium secondary batteries.
Experimental
The 4,40-diaminodiphenyl sulfone monomer (C12H10O2N2S, 99 %) was dissolved in
1 M HCl solution at 80 �C in a N2 atmosphere. Ammonium persulfate ((NH4)2S2O8,
98 %) was used as a redox initiator. The initiator solution was slowly added using a
dropping funnel to the reactant solution while stirring vigorously. The reaction
mixture was then agitated continuously for 24 h under N2 atmosphere at 80 �C. The
precipitated particles were filtered and washed with hot distilled water to remove
any impurities. The filtered product containing HCl-doped pDDS was dried under
vacuum for 48 h to yield a dry powder. The powder was then reduced by excess
solution of 1 M NH4OH to give dedoped pDDS (or pDDS). The pDDS was treated
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again for doping in 1 M HCl solution and finally dried under vacuum for 12 h to
produce HCl-doped pDDS (or doped pDDS).
The synthesized polymers (pDDS and doped pDDS) were characterized by surface
group analysis using a Fourier-transform infrared spectrometer (Varian 2000) in the
wavenumber range of 4,000–400 cm-1. X-ray photoelectron spectroscopy was
performed on the synthesized polymer powders using a VG ESCALAB Mk(II)
spectrometer (A1 Ka 1486.6 eV photons). The neutral peak of carbon 1s (C1s) at
284.6 eV was used as a reference to correct the shift by surface-charging effects.
A coin-type cell (2032) was fabricated in a dry box for investigation of the
electrochemical property. Lithium foil was used as a negative electrode. The doped
pDDS (90 wt%) as the positive electrode was mixed with carbon black (Super P,
Timcal, 5 wt%) as a conductive agent and poly(vinylidene fluoride) (Aldrich, 5 wt%)
as a polymer binder. The electrolyte solution used was 1.15 M LiPF6 dissolved in
ethylene carbonate/ethylmethyl carbonate/dimethyl carbonate (3/2/5 weight basis).
Cyclic voltammetry was performed on the Li pDDS cell using a potentiostat
(WBCS3000, WonA Tech) within the potential range of 2.0–4.5 V (vs. Li/Li?) at the
scan rate of 0.05 mV s-1. Galvanostatic charge and discharge were also carried out for
50 cycles using a cycler (WBCS3000, WonA Tech) in the voltage range of 2.5–4.0 V
at a constant current density of 8 mA g-1, practically corresponding to a 0.05 C-rate.
In addition, the rate-capability test was performed by varying the C-rate every seven
cycles to 0.1, 0.2, 0.5, 1.0, 2.0, 3.0, 5.0, and 0.1 C-rates.
Results and discussion
Figure 1 shows the Fourier-transform infrared spectra of the pDDS and doped
pDDS. Though slight deviations are appeared, the pDDS and doped pDDS exhibit
similar characteristic bands of stretching and bending vibrations for the surface
groups such as N–H, C=C, C–H, and S=O. Compared with the previous reports [4,
7, 10, 12], most of the bands observed for the present pDDS and doped pDDS are
shifted. Nonetheless, the band identifications for the doped pDDS in Fig. 1 may be
summarized as follows: N–H stretchings at 3,596 and 3,363 cm-1, N–H bending at
1,634 cm-1, C=C stretchings of quinoid and benzenoid rings at 1,588 and
1,503 cm-1, respectively, C=C bending vibration at 692 cm-1, S=O stretchings at
1,298 and 1,149 cm-1, S=O bending at 567 cm-1, C–H in-plane bending at
1,102 cm-1, and C–H out-of-plane bending at 832 cm-1. Particularly, the bands at
1,302 and 555 cm-1 [7] corresponding to S=O stretching and S=O bending modes,
respectively, shift their frequency and intensity in the present pDDS to 1,298 and
567 cm-1, respectively.
On the other hand, it is difficult to distinguish the pDDS and doped pDDs in the
Fourier-transform infrared spectra in Fig. 1 due to the similar intensities and
frequencies of each band peak. However, the effect of HCl- or H?-doping may be
observed by the decrease in the absorption intensity of N–H stretching vibrations at
3,596 and 3,363 cm-1 due to slight shrinkage by an attack of H? to a part of –N=,
resulting in the formation of an N? group in the main chain. The H?-doping can be
confirmed by the N1s X-ray photoelectron spectroscopy results (see Fig. 2). The
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pDDS possesses two peaks corresponding to –N= and –NH–, centered at 399.5 and
402.9 eV, respectively. The percentage of peak area ratio or Lorentzian-Gaussian is
estimated to be 53.2 and 46.8 % for the –N= and –NH–, respectively. Meanwhile,
the H?-doped pDDS includes three peaks corresponding to –N=, –NH–, and N?
centered at 398.7, 399.7, and 401.3 eV, respectively. The percentage of peak area
ratio due to the positive nitrogen (N?) is 46.0, 44.0, and 10.0 % for the –N=, –NH–,
and N?, respectively. This implies generation of charged nitrogen sites by H?-
doping with the decrease in the peak area ratio percentages of –N= and –NH–.
These results reflect the doping/dedoping structure of pDDS, as shown in Fig. 3a.
Also, the charging/discharging mechanism of pDDS (Fig. 3b) can be expected to
occur in association with the doping/dedoping process.
The cyclic voltammogram of the Li-doped pDDS cell is shown in Fig. 4, recorded
at a scan rate of 0.05 mV s-1. It may be confused by the fact that the potential range in
Fig. 4 is 2.0–4.5 V vs. Li/Li?, whereas the previous reports range from -0.2 V to 0.8
or 1.2 V in 0.1 M H2SO4 [4, 5] or 0–0.9 V vs. Ag/AgCl [8]. In this study, only redox
behavior within the doped pDDS electrode is considered for Li? transport, as shown in
Fig. 3b. Unlike a charge separation mechanism [13], the Li? transferred from the
lithium metal anode or the electrolyte solution interacts with the negative oxygen (O-)
on one side of the O=S=O group during the charging process, resulting in an oxidative
broad peak at 3.75 V in Fig. 4. During discharge process, the Li? dissociates with the
negative oxygen, transforming into the original O=S=O group to yield the reductive
peak at 3.15 V in Fig. 4. The charging/discharging process, which corresponds to a
typical pair of peaks at 3.75/3.15 V, is seen to be reversible. However, another
reductive peak at 2.4 V seems to be partially due to a charge separation mechanism,
i.e., the reduction in a small portion of positive N [13].
The charge and discharge profiles in Fig. 5a for doped pDDS may be an evidence
of the peak potentials described above. The charge profile of the doped pDDS shows
a breakpoint at 3.75 V, observed by a very small plateau, corresponding to the
oxidative peak at 3.75 V in the cyclic voltammogram. The oxidation peak at 3.75 V
reflects a physical interaction between Li? and O- in the main chain, which may be
formed temporarily. Thus, the charging profile looks like a smooth curve with a
3500 3000 2500 2000 1500 1000 500
1634
1588 1503
1298
33633596
1149
1102 832
692567
(b) Doped pDDS
Tra
nsm
ittan
ce (
a.u.
)
Wavenumber (cm-1)
(a) pDDS
Fig. 1 Fourier-transforminfrared spectra of the a pDDSand b doped pDDS
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small breakpoint at 3.75 V. A plateau can be clearly observed if a chemical and/or
an electrochemical reaction such as intercalation/deintercalation or alloying/
dealloying occurs. It may be similar with the description in the case of the
reduction peak at 3.15 V.
In terms of electrochemical performance, the specific discharge capacity of the
doped pDDS achieves 31.5 and 24.3 mA h g-1 at initial and 50th cycles,
respectively. A very large irreversible capacity between charge and discharge
during the initial cycle arises by initial absorption of large excess Li?, which is
overcharged even at the inactive sites. However, the cycle performance after the
first charging process is moderately stable by the fact that the capacity retention
ratio at the 50th cycle reaches about 77 % (see Fig. 5b). This may be due to the
stability of the charging/discharging process, which is supported by structural
stability of the doped pDDS connected with aniline and sulfone moieties in series.
As shown in Fig. 6, the high-rate capability result also shows a superior
performance. For instance, the recovery ratio at 0.1 C-rate after 50 cycles through
various severe current rates from 0.1 to 5.0 C-rates becomes almost 100 %. The
recovery ratio can also reflect the excellent cycle performance discussed above.
Such recovery is a characteristic feature of pDDS as a cathode-active material in
lithium secondary batteries with high-power requirements.
Fig. 2 N1s X-ray photoelectroncore spectra of the a pDDS andb doped pDDS
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Conclusions
This paper describes for the first time the characterization of doped pDDS for use as
a cathode-active material in lithium secondary batteries. The doped pDDS is
structurally identified by the polymer in which the aniline and sulfone moieties are
repeatedly connected in series in the main chain, providing sufficient structural
stability to endure many cycles of charge and discharge at high current rates. Even
Fig. 3 Reaction mechanisms of a doping/dedoping in the pDDS material and b charging/discharging inthe doped pDDS electrode
2.0 2.5 3.0 3.5 4.0 4.5-10
-5
0
5
10
15
ReductionCur
rent
den
sity
(m
A-1
g)
Potential (V)
1
2
1
2
Oxidation
Scan rate
0.05 mV s -1
Fig. 4 Cyclic voltammogramof the doped pDDS electrode,obtained at 0.05 mV s-1. Thenumber in the figure indicatescycle numbers
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though the specific discharge capacity is comparatively low (about 30 mA h g-1),
the doped pDDS can be considered as a promising candidate for cathode-active
material in lithium secondary batteries due to its cycle performance and high-rate
capability in applications.
0 10 20 30 40 50 60 70 802.5
3.0
3.5
4.0
Vol
tage
(V
)Specific capacity (mAh g-1)
@0.05 C-rate1
50
1030
(a)
0 10 20 30 40 500
10
20
30
40
Spe
cific
dis
char
ge c
apac
ity (
mA
h g-1
)
Cycle number
(b)
Fig. 5 a Charge and dischargecurves and b cyclic performanceof the doped pDDS electrode at0.05 C-rate. The number in thefigure indicates cycle numbers
0 10 20 30 40 500
5
10
15
20
25
30
0.1C
5.0C3.0C
2.0C
1.0C
0.5C
0.2C
Spe
cific
dis
char
ge c
apac
ity (
mA
h g-1
)
Cycle number
0.1C
Fig. 6 Rate-capability resultsof the doped pDDS electrode
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Acknowledgments This research was supported by a grant from the Fundamental R&D Program for
Core Technology of Materials funded by the Korean Ministry of Knowledge Economy and by the Priority
Research Centers Program through the National Research Foundation of Korea (NRF) funded by the
Ministry of Education, Science and Technology (2009-0093818).
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