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A smart surface prepared using the switchable superhydrophobicity of neatelectrospun intrinsically electroactive polyimide fiber mats
Chang-Jian Weng,a Yu-Sian Jhuo,a Chi-Hao Chang,a Chun-Fang Feng,a Chi-Wei Peng,a Chung-Feng Dai,b
Jui-Ming Yeh*a and Yen Weic
Received 13th June 2011, Accepted 5th August 2011
DOI: 10.1039/c1sm06097j
An electroactive polyimide fiber (EPF) mat based on conjugated segments of electroactive amino-
capped aniline trimer (ACAT) as a diamine and 4,40-(4,40-sopropylidenediphenoxy)-bis(phthalicanhydride) (BSAA) as a dianhydride was successfully prepared by electro-spin technology with
electrochemical activity and dopable properties, which were similar to polyaniline. The degree of
electrochemical activity and dopable properties can be tuned by varying the content of ACAT existing
in the as-prepared electro-spun EPF mats. After doping with perfluorooctanesulfonic acid (PFOS), the
water contact angle of EPF surface is increased from hydrophobicity at 133� to superhydrophobicity at
155�. It is interesting that the EPF mat undergoes a switchable process from superhydrophobicity to
superhydrophilicity via doping with PFOS and de-doping with ammonium gas.
1. Introduction
Smart surfaces with reversibly switchable wettability, especially
switching between superhydrophobicity and super-
hydrophilicity, are of great importance due to their numerous
industrial applications.1–3 It is well know that surface free energy
and geometrical structure play key roles in the wettability of solid
substrates. The significant effect of the micro- (or nano-) surface
roughness of inorganic oxides or organic compounds is high-
lighted when fabricating superhydrophobic and super-
hydrophilic reversible switched surfaces.
A variety of stimulus tactics have therefore been developed for
controlling the wettability by way of light irradiation,4,5 thermal
treatment,6,7 treatment with acid solution,8–10 and other
approaches.11–14 With the development of smart materials, a dual
controllable wettability triggered by both temperature/pH, and
temperature/light irradiation has been demonstrated.15,16 Atten-
tion has also been paid to the wettability of conducting polymers,
which is a crucial parameter for controllable separation and
application of conducting polymers as sensors.17–21 For instance,
Berggren et al. 18 reported a wettability switch based on
a combination of a solid polymer electrolyte and a conducting
polymer, such as PANI, or poly(3-hexylthiophene), demon-
strating electrochemical control of wettability. Yan et al.
demonstrated19 that a polypyrrole film could be switched from
superhydrophobicity to superhydrophilicity by changing
aDepartment of Chemistry and Center for Nanotechnology, Chung-YuanChristian University, Chung Li, 32023, Taiwan, R. O. C. E-mail:[email protected]; Fax: +886-3-265-3399; Tel: +886-3-2653340bTaiwan Textile Research Institute, Tucheng, 23674, Taiwan, R. O. C.cThe Tsinghua Center for Frontier Polymer Research Department ofChemistry, Tsinghua University, Beijing, 100084, China
This journal is ª The Royal Society of Chemistry 2011
electrical potential. Jiang et al. reported22,23 that PANI fibers
could be tuned from superhydrophobicity to superhydrophilicity
with PFOS and PFSEA as a dopant, respectively.
However, to the best of our knowledge, the wettability tran-
sition between superhydrophobicity and superhydrophilicity for
a non-conductive polymer, such as polyimide, has remained
a challenging task. Recently, research activities in terms of oli-
goanilines with well-defined structures for modelling the elec-
tronic, magnetic and optical properties of polyaniline have
emerged.24 Moreover, oligoanilines-derived electroactive poly-
mers have also attracted considerable research interests.25–28
Herein, we envisioned that electroactive polyimide might
reveal reversibly switchable wettability because it exhibits
dopable properties similar to polyaniline. Electrochemical
activity and dopable properties of as-prepared electroactive
polyimide fiber mats can be tuned by varying the content of
amino-capped aniline trimer (ACAT) existed in the polyimide
main chain. Therefore, in this work, we present the first report of
the reversibly switchable superhydrophobicity of neat electro-
spun intrinsically electroactive polyimide fiber (EPF) mats. The
wettability of electroactive polyimide fiber mats could be tuned
by varying the content of the ACAT segment existing in the
polymer main chain. The reversible wettability of EPF mat from
superhydrophobicity to superhydrophilicity could be reversibly
switched by doping with perfluorooctanesulfonic acid (PFOS)
and dedoping with ammonia gas.
2. Experimental
Chemicals and instrumentations
Aniline (Sigma-Aldrich) was distilled prior to use. 2,2-Bis[4-
(4-aminophenoxy)phenyl]hexafluoropropane (BDAF); Fluka,
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Buchs, Switzerland), 4,40-diaminodiphenylamine sulfate (Sigma-
Aldrich), N,N-dimethylacetamide (DMAc; Riedel-deHa€en),
tetrahydrofuran (THF; Riedel-deHa€en), 4,40-(4,40-iso-propylidenediphenoxy)-bis(phthalic anhydride)(BSAA, Sigma-
Aldrich, 97%), sodium chloride (NaCl, Sigma-Aldrich), per-
fluorooctanesulfonic acid (PFOS; Fluka, 40%), ammonium
hydroxide (NH4OH; Riedel-deHa€en, 35%) and ammonium per-
sulfate (APS, Sigma-Aldrich, 97%) were used as received without
further purification. All the reagents were reagent grade unless
otherwise stated.
Mass spectra were run on a Bruker Daltonics IT mass spec-
trometer model Esquire 2000 (Leipzig, German) with an Agilent
ESI source (model G1607-6001). 1H NMR spectra were run on
a Bruker 300 spectrometer, referenced to internal standard of
tetramethylsilane (TMS), DMSO was used as the solvent.
Attenuated total reflectance FTIR spectra was obtained at
a resolution of 4.0 cm�1 with a FT/IR spectrometer (FT/IR-4100)
at room temperature ranged from 4000 cm�1 to 650 cm�1. The
surface morphology of materials was characterized by scanning
electron microscopy (SEM), (Hitachi S-2300). Contact angles of
samples were measured using a First Ten Angstroms FTA 125.
Synthesis of N,N0-bis(40-aminophenyl)-1,4-quinonenediimine
(ACAT)
4,40-Diaminodiphenylamine sulfate (23.65 g, 0.796 mol) and
aniline (7.40 g, 0.796 mol) were dissolved in aqueous HCl solu-
tion (1.0 M, 800 mL) containing 75 g of NaCl. A solution of
ammonium persulfate (18.00 g, 0.789 mol) in aqueous HCl
(1.0 M, 200 mL) was added via a dropping funnel into the above
solution at an operational temperature of �5 �C with a dropping
rate of approximately 60 drops min�1. The reaction mixture was
stirred for additional 1 h at �5 �C. The resulting precipitate was
collected by filtration and washed with aqueous HCl solution
(1.0 M, 400 mL) precooled to 0 �C. The solid product was
washed with 10%NH4OH solution (100 mL) and a large amount
of distilled water and then dried in a vacuum oven at 50 �Covernight. The ACAT was obtained as a bulk solid. 11.8 g
(51.5%). 1H NMR (300 MHz, DMSO-d6): d 6.95 (s, 4H), 6.80–
6.60 (dd, 8H), 5.42 (s, 4H). MS (ESI) calcd. for C18H16N4 [M]:
288.14. Found 289.1 [M + H]+.
Scheme 1 A schematic representation of the synthesis of electroactive
polyamic acid and electroactive polyimides.
Synthesis of electroactive polyamic acid (EPAA), electroactive
copolyamic acid (ECPAA) and non-electroactive polyamic acid
(NEPAA)
Electrospun process was performed by using electroactive pol-
yamic acid (EPAA), electroactive copolyamic acid (ECPAA) and
non-electroactive polyamic acid (NEPAA) solution (10 wt%) as
an electrospun solution. Three polyamic acid were prepared
using 2,2-bis[4-(4-aminophenoxy)phenyl]hexafluoropropane
(BDAF), N,N0-bis(40-aminophenyl)-l,4-quinonenediimine
(ACAT), and 4,40-(4,40-isopropylidenediphenoxy) bis(phthalic
anhydride) (BSAA) in different feeding ratios. The typical
procedure to prepare EPAA and NEPAA was using BSAA
(0.26 g, 0.5 mmole) and ACAT (0.14 g, 0.5 mmole) or BDAF
(0.26 g, 0.5 mmole) in 4 g of THF/DMAc (1 : 1) at room
temperature. The electroactive copolyamic acid (ECPAA) solu-
tion was synthesized by a well-developed procedure using BSAA
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(0.26 g, 0.5mmole), ACAT (0.072 g, 0.25 mmole) and BDAF
(0.13 g, 0.25 mmole) in 4 g THF/DMAc (1 : 1) at room
temperature. The as-prepared mixture was then stirred for an
additional 2 h at room temperature, as shown in Scheme 1.
Preparation of electroactive PAA fiber membranes
The electrospun solution was synthesized upward and its corre-
sponding molecular weight: NEPAA (Mw¼ 29 814; PDI¼ 1.95),
ECPAA (Mw ¼ 66 501; PDI ¼ 3.275) and EPAA (Mw ¼ 92 097;
PDI ¼ 2.138) were measured by GPC (0.1 wt% in NMP
solution).
Fig.1 showed the general electrospin process, which consisted
of a high-voltage power supply and a collector plate. The
spraying solution was put into a syringe with a 13 mm inner
diameter and a distance of 14 cm from the tip of syringe (anode)
to the collector (cathode). The high-voltage DC electric field
strength controlled by a high-voltage DC power supply was fixed
at 20 kV. The typical ejection rate of solution from the syringe is
0.02 mL min�1 and the electrospinning was conducted in air.
Removal of solvent and imidization of EPAA, ECPAA and
NEPAA fiber mats were performed concurrently by heating
them under air flow at 250 �C for 2 h. After imidization, the EPF,
ECPF and NEPF can be obtained.
Wettability switching experiments
As-prepared EPF was immersed into a solution of PFOS (2 wt%
in water) for about 2 h and then followed by washing with water
and air-drying at room temperature. The superhydrophobic of
EPF mat obtained. Ammonia was added into a closed vessel
using syringe, and then ammonia vapor was filled into the
This journal is ª The Royal Society of Chemistry 2011
Fig. 1 A schematic of the electrospin setup with modified auxiliary
electrode and field-controllable target electrode.
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chamber. After the superhydrophobic EPF mat was exposed to
dry ammonia vapor in chamber for �1 min, the super-
hydrophobic of EPF was obtained.
Fig. 2 FTIR spectra of (a) NEPF, (b) ECPF, (c) EPF.
Fig. 3 SEM of (a) NEPAA, (b) ECPAA, (c
This journal is ª The Royal Society of Chemistry 2011
3. Results and discussion
For the studies on FTIR spectroscopy, the EPF mat prepared
from thermal imidization of ACAT and BSAA exhibited an
obvious carbonyl asymmetric stretching of nC]O located at 1850
and 1778 cm�1 and symmetric stretching of nC]O located at
1720 cm�1.
The characteristic peak near 738 cm�1 due to the imide ring
deformation of the EPF mat was also found in the IR spectra.
Moreover, the FTIR spectroscopy of the ECPF mat revealed
a decrease in the intensity ratio of nC]O (1850 cm�1)/nC]O
(1778 cm�1), indicating a decrease in the feed composition ratio
of ACAT/BDAF existing in the as-prepared ECPF mat and this
ratio permits us to estimate the extent of oxidation of the poly-
mer. However, the NEPF mats lack the characteristic asym-
metric stretching of nC]O (1850 cm�1) of ACAT, as shown in
Fig. 2.
As important aspects, effects of the electroactive polyamic acid
fibers and electroactive polyimide fibers with different ACAT
content on morphologies have been studied, and SEM is used to
characterize their morphologies. SEM micrographs of all speci-
mens as showed in Fig. 3. Average diameters of electroactive
polyamic acid fibers which with different ACAT contents ranged
from about 420 to 560 nm. However, the fibers didn’t shrank
obviously after thermal condensation process and them still
uniform and continuous after imidization.
According to the proposed mechanism for the electrochemical
redox reaction of aniline oligomers,29 the electrochemical
behavior of all obtained specimens was examined in a strongly
acidic electrolyte composed of 1.0 M H2SO4 aqueous solution.
All samples were formed by electrospinning on the surface of a Pt
working electrode and followed by thermal conversion into
polyimide through imidization. Fig. 4 shows the cyclic voltam-
metry of EPF, ECPF and NEPF obtained using a saturated
calomel electrode (SCE) as the reference electrode with a scan
rate of 50 mV s�1. Under these conditions, cyclic voltammetry of
EPF showed a pair of reversible redox peaks, which were similar
to many longer oligomers that undergo a two-electron-transfer
process.30 For the studies of EPF, a single oxidation peak was
found to occur at a lower potential (582 mV) as compared to that
of polyaniline (800 mV). We considered that the oxidation peak
) EPAA, (d) NEPF, (e) ECPF, (f) EPF.
Soft Matter, 2011, 7, 10313–10318 | 10315
Fig. 4 Cyclic voltammetry of the polyimide, shown as (a) NEPF, (b)
ECPF and (c) EPF above, was measured in aqueous H2SO4 (1.0 M) with
a scan rate of 50 mV s�1. The proposed oxidation mechanism is shown
below.
Fig. 5 UV-vis spectra of EPF: (a) NH3 dedoped, (b) PFOS doped.
Fig. 6 SEM images of (a) ECPF, (b) EPF; SEM fluorine mapping
images of (c) ECPF, (d) EPF.
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located at �582 mV was assigned to the transition from the
reduced state to the oxidized state of EPF. It should be noted that
the EPF having higher content of ACAT exhibited a larger redox
current at 0.4 mA cm�2 (i.e., higher electroactivity) compared to
that of ECPF.
However, NEPF showed null zero redox current. This implied
that the incorporation of ACAT into polyimide may introduce
electroactivity into as-prepared EPF. Moreover, incorporation
of higher ACAT content may yield polyimide with higher elec-
tro-activity.
The EPF mat that has alternating conjugated segments
(ACAT) and non-conjugated segments (BSAA) in the main
chain still exhibits reversible dopable response properties. In this
study, perfluorooctanesulfonic acid (PFOS) was used as a dopant
to dope an EPF mat and examine its result in the UV-visible
spectrum. For an un-doped EPFmat, the quinoid (Q) absorption
peak located at ca. 509 nm and the benzenoid (B) peak located at
ca. 312 nm were assigned as the two characteristic peaks in the
emeraldine base (EB) form of ACAT, which were associated with
the transition ofpb–pq from a benzene unit to a quinone unit and
from a p–p* transition in a benzene unit, respectively.31 After
EPF was doped by perfluorooctanesulfonic acid (PFOS), the new
bands were observed at around 415 and 750–800 nm. The peak
appearing at 415 nm was probably due to the formation of
polarons (radical cations) caused by electron transition from
quinoid to benzoid units. The peak found at 800 nm with a long
tail was assigned to the polaron transition, which typically
characterizes protonation,22,23 and is identical to that of the
emeraldine salt (ES) form of the EPF mat. (Fig. 5)
In order to determine how the morphologies and elemental
distribution of the different ACAT contents in the polymer chain
can tune the contact angle (CA) by using PFOS as dopant, SEM
10316 | Soft Matter, 2011, 7, 10313–10318
imaging and SEM fluorine mapping imaging were performed.
SEM images of ECPI and EPI, which were doped with PFOS, are
illustrated in Fig. 6(a) and Fig. 6(b), respectively. EDX mapping
of an image in a SEM image of EPF and ECPF, which were
doped with a PFOS support, can provide information on the
distribution of fluorine from the PFOS dopant, as shown in
Fig. 6(c) and Fig. 6(d). It should be noted that more dense
fluorine distributions are observed for higher ACAT content
samples. Thus, these morphological studies demonstrated that
the EPF reveals a higher dopable degree than the EPCF because
of the more conjugated segment (ACAT) in the polyimide main
chain.
Since PFOS has dual doping and superhydrophobic functions,
reversible wettability of the surface of EPF may be realized
through a doping process. This prediction has been demon-
strated by measurements of the static CA of doped EPF and
ECPF. Fig. 7 gives the relationship between the content of
ACAT and CAs for all PFOS-doped specimens. It should be
noted that the CA of an electroactive polyimide fiber mat could
be tuned by varying the ACAT content while it was doped with
PFOS. Because the NEPF was without ACAT in the polymer
main chain, the CA of NEPF was only 106� and it cannot be
doped by PFOS. However, in ECPF and EPF, it is clear that the
CA increases from 117� and 131� to 133� and 155� with the
This journal is ª The Royal Society of Chemistry 2011
Fig. 7 The water contact angle of NEPF, ECPF and EPF.
Fig. 9 Reversible superhydrophobic–superhydrophilic conversion of
the EPF through doping with PFOS and de-doping by ammonia gas.
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increase in contents of ACAT, respectively. This implied that the
wettability and dopable degree of the electroactive polymer fiber
can be controlled by the ACAT content in the polymer main
chain.
The EPF mat presents superhydrophobicity with a static CA
as high as 155�. Obviously, superhydrophobicity is resulted from
the synergistic effects of the pore structure of the EPF mat and
a low surface energy of the PFOS dopant.
To give a surface revealing superhydrophobic properties, the
EPFmat was required to be doped with PFOS. As is well known,
the difference between advancing (qA) and receding contact
angles (qR) of a surface is used to understand contact angle
hysteresis.32 Fig. 8 shows the advancing and receding contact
angle for NEPI, ECPF and EPF mats doped with PFOS. The
ECPF doped with PFOS had advancing (qA) and receding (qR)
contact angles of 142� and 128�, respectively.After increasing the ACAT content in polyimide main chain
(EPF), both advancing and receding contacts angles increased up
to 158� and 150�. It is noteworthy that contact angle hysteresis
was reduced from 14� to 8�, respectively, which can be attributed
to the increase of doping degree due to the electroactive poly-
imide fiber mats doped with PFOS.
After the EPF mat was exposed to dry ammonia gas for 1 min,
interestingly, the water droplet on the surface of the mat spread
out, which results in a CA of about 0�. After the EPF mat was
immersed into a solution of PFOS (2 wt%) for about 2 h and then
Fig. 8 Advancing and receding water contact angles of the NEPF,
ECPF and EPF fiber mats.
This journal is ª The Royal Society of Chemistry 2011
dried in air, the EPF mat still gained superhydrophobic prop-
erties. These observations indicate that the doping/dedoping
process results in the reversible wettability changing from
superhydrophobicity to superhydrophilicity. The reversibility of
the surface wettability for the EPF mat can be repeated several
times without any change in wetting property as shown in Fig. 9.
The reversibility of the wettability observed for the EPF mat
can be explained as follows: The PFOS, composed of a hydro-
philic SO3H polar head and a hydrophobic perfluorinated
carbon tail, is not only reserved as a dopant, but also brings
about hydrophobic/hydrophilic function. However, the PFOS
molecules are then no longer locked to the ACAT backbone in
the polyimide main chain and it can move more freely.22,23
When EPF was doped with PFOS, the hydrophobic per-
fluorinated carbon tail was exposed at the outermost surface, the
superhydrophobic surface was obtained, as shown in Fig. 10(a).
After dedoping EPF with ammonia gas, the hydrophilic SO3�
groups can rotate and are exposed at the outmost surface, thus
resulting in conversion of the superhydrophobicity to super-
hydrophilicity. (Fig. 10(b))
Fig. 10 A proposed mechanism for the reversible wettability switching
by EPF (a) PFOS-doped and (b) NH3 de-doped.
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Conclusions
In summary, we have demonstrated an electrospin technique for
synthesizing an EPF mat, which has not only reversible response
properties but also has reversible wettablity that can be switched
from superhydrophobicity to superhydrophilicity by doping with
PFOS and dedoping with ammonia gas. Interestingly, the degree
of electrochemical activity and dopable properties can be
reversibly tuned by varying the content of ACAT existing in the
as-prepared electrospun polyimide fiber mats, based on SEM
fluorine element mapping results. Using NEPF, the CA of NEPF
was only 106� and it cannot be doped by PFOS. However, using
ECPF and EPF, the CA can be increased from 117� to and 155�
with the increase in the varying contents of ACAT. The revers-
ible wettability changing from superhydrophobicity to super-
hydrophilicity can be repeated several times by doping with
PFOS and de-doping with ammonia gas.
Acknowledgements
The financial support of this research by the Ministry of
Education, Taiwan, R. O. C., NSC 98-2113-M-033-001-MY3
and department of chemistry at CYCU., CYCU-98-CR-CH are
gratefully acknowledged.
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