Synthesis and purification of long copper nanowires ... Res 1 Synthesis and purification of long...
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Nano Res
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Synthesis and purification of long copper nanowires.
Application to high performance flexible transparent
electrodes with and without PEDOT:PSS Céline Mayousse, Caroline Celle, Alexandre Carella, and Jean-Pierre Simonato () Nano Res., Just Accepted Manuscript • DOI: 10.1007/s12274-013-0397-4
http://www.thenanoresearch.com on December 12, 2013
© Tsinghua University Press 2013
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Nano Research DOI 10.1007/s12274‐013‐0397‐4
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TABLE OF CONTENTS (TOC)
Synthesis and purification of long copper nanowires.
Application to high performance flexible transparent
electrodes with and without PEDOT:PSS.
Céline Mayousse, Caroline Celle, Alexandre Carella, and
Jean-Pierre Simonato*
CEA, LITEN / DTNM / LCRE, 17 rue des Martyrs, 38054
Grenoble, France
High performance flexible transparent electrodes based on random
networks of copper nanowires are reported. A crucial chemical
cleaning of copper nanowires with glacial acetic acid after the
hydrothermal synthesis is revealed, giving access to transparent
conductive films with excellent performances, typically 55 Ω/sq at
94% transmittance, without need of post-treatment. Encapsulation of
Cu nanowire networks with PEDOT:PSS also provides an efficient
route to very good transparent electrodes. Furthermore integration of
these electrodes into flexible touch sensors is reported.
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Synthesis and purification of long copper nanowires. Application to high performance flexible transparent electrodes with and without PEDOT:PSS.
Céline Mayousse, Caroline Celle, Alexandre Carella, and Jean-Pierre Simonato ()
CEA, LITEN / DTNM / LCRE, 17 rue des Martyrs, 38054 Grenoble, France
Received: day month year / Revised: day month year / Accepted: day month year (automatically inserted by the publisher) © Tsinghua University Press and Springer-Verlag Berlin Heidelberg 2011
ABSTRACT We demonstrate the hydrothermal synthesis of long copper nanowires based on a simple protocol. We show
that the purification of the nanowires is very important and can be achieved easily by wet treatment with
glacial acetic acid. Fabrication of random networks of purified copper nanowires leads to flexible transparent
electrodes with excellent optoelectronic performances (eg 55 Ω/sq at 94 % transparency). The process is
carried out at room temperature and no post‐treatment was necessary. Hybrid materials with the conductive
polymer PEDOT:PSS show similar properties (eg 46 Ω/sq at 93 % transparency), with improved mechanical
properties. Both electrodes were integrated in capacitive touch sensors.
KEYWORDS
Copper nanowires, Transparent electrodes, PEDOT:PSS, touch sensor, metallic nanowires
1. Introduction
Transparent conductive thin films are essential
components for touch screens, solar cells, organic
light‐emitting diodes and many other
optoelectronic devices. The fabrication of
transparent electrodes is currently realized with
transparent conductive oxides (TCOs), and notably
indium tin oxide (ITO) due to its high conductivity
(~ 10‐30 Ω/sq) at high optical transparency (90 %).
However, ITO is not able to meet the future
demands for transparent conductive films because
of the rising and volatile cost of indium, the
intrinsic brittleness of ITO and the necessary high
temperature processing for production. Therefore,
great efforts have been devoted to develop new
materials produced at low cost, low temperature
and processable over large areas. Several materials
have led to encouraging results so far, such as
carbon nanotubes (CNTs) [1–4], graphene [5],
conductive polymers and metallic nanowires [2,6,7].
Among those candidates, metallic nanowires are
especially promising. Indeed, transparent
electrodes based on silver nanowires (Ag NWs)
have been reported to compete well with TCOs
Nano Res DOI (automatically inserted by the publisher) Research Article
———————————— Address correspondence to: Caroline Celle, [email protected]; Jean-Pierre Simonato, [email protected]
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[8–14]. Up to now, mainly silver has been used.
However, copper appears as an interesting
alternative since it is almost as conductive as silver,
with a bulk resistivity of 1.59 nΩ.m (vs 1.67 nΩ.m
for silver). Moreover, copper is much more
abundant and far less expensive than silver (about
100 times cheaper). Based on these facts, there has
been recently a growing interest in the development
of one‐dimensional copper nanostructures,
especially copper nanowires (Cu NWs). Several
methods for preparing Cu NWs have been reported
such as chemical vapor deposition [15], template
assisted electrochemical synthesis [16,17] or
membrane processes [18]. All these routes have
usually complex reaction processes and often
require the use of toxic reducing agents such as
hydrazine [19–25]. Surprisingly, fabrication of
flexible transparent electrodes based on random
networks of Cu NWs has been scarcely studied up
to now. Wiley and co‐workers have pioneered Cu
NW based electrodes by preparing flexible films
exhibiting sheet resistance of 30 Ω/sq at 85%
transmittance [26,27]. Recently, Lu et al. [28] and
Peng et al. [29] have also reported very good
performances on glass or flexible substrates down
to 30 Ω/sq at 85 % and 51 Ω/sq at 93 %, respectively.
Transparent electrodes with remarkable
optoelectronic performances were also obtained
with the deposition of electrospun copper
nanofibers or nanotrough networks as reported by
Cui’s group [30,31]. However most of these
processes encompass significant drawbacks such as
high temperature, use of physical deposition
methods or use of toxic reducing agents, and
generally hard post‐processing treatments. Thus
there is still a need to develop processes compatible
with the fabrication of low‐cost large area devices
using Cu NWs and to integrate them into functional
devices. To our knowledge very few functional
devices using CuNWs have been reported to date
[29,32,33]. Hybrid materials with graphene
derivatives have also been reported recently,
showing interesting properties and ability to be
used in electrochromic devices or CdTe solar cells
[34,35].
Herein we report an environmentally friendly
synthesis to produce ultralong well‐dispersed
CuNWs. Electrode fabrication was realized at room
temperature without need of post‐treatment. We
show that after the synthesis of Cu NWs, a simple
cleaning with glacial acid acetic (GAA) in solution
improves dramatically the performances, typically a
sheet resistance of 55 Ω/sq at 94 % transparency
which compares well with ITO electrodes. Further
improvement of the electrodes was performed by
making composite thin films of Cu NWs and
poly(3,4‐ethylenedioxythiophene)poly(styrenesulfo
nate) also named PEDOT:PSS. To demonstrate the
practical use of Cu NW transparent conductive
films in functional devices, we also report herein
the fabrication of a capacitive touch sensor.
2. Experimental
Synthesis of Cu NWs
Cu NWs were synthetized according to a modified
published procedure. In a typical protocol, 0.53 g of
octadecylamine (ODA, Aldrich) and 0.13 g of
anhydrous copper chloride (CuCl2, Aldrich) were
added to 80 mL of deionized water. After 5 min of
stirring, the round bottom flask was sonicated for 45
min forming a blue emulsion. Subsequently, the
solution was transferred into a Teflon‐lined
autoclave and sealed for 140 h at 165°C. The reactor
was then cooled down to room temperature. The
supernatant was removed and the reddish settled
product was dispersed in deionized water. The
solution was then transferred into a separatory
funnel and washed successively with deionized
water, n‐hexane and ethanol. The final product was
kept under degased isopropanol to avoid oxidation
of the nanowires.
Before electrode fabrication, GAA treatment was
realized. The solution was centrifuged at 9000 rpm to
remove the solvent, and a large excess of glacial
acetic acid was added. After 10 min, GAA was
removed and the product was washed once with
isopropanol. Eventually, GAA treatment can also be
realized after deposition, by immersing the electrode
into a GAA bath for 10 min, and then drying on a
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hotplate at 80°C.
Fabrication of electrodes
Electrodes were realized on
poly‐ethylenenaphthalate (PEN) substrates obtained
from Dupont Teijin (Teonex, 125 μm thickness).
Transparent conductive films were formed at room
temperature by filtration of a dispersion of Cu NWs
on a Teflon filter (Sartorius, 0.45 μm). The deposited
film was then transferred to the substrate by
applying uniform pressure. The Teflon filter was
peeled off to leave the Cu NW network on the
substrate. The fabrication process of the electrodes is
detailed in supplementary information (Fig. S‐1).
This method does not require heat or substrate
functionalization. In a parallel study, a solution of
PEDOT:PSS (Clevios, PH1000) in isopropanol was
spin‐coated at 1500 rpm for 50 s onto the nanowire
network. No GAA purification of the solution was
carried out in this case. The thin film was annealed
for 2 min at 100 °C in order to remove the solvent.
Fabrication of flexible capacitive sensors
Capacitive sensors were realized according to a
published procedure using Ag NWs [9]. Cu NWs
were transferred on a 3x3 cm² PEN substrate, and
eventually coated with PEDOT:PSS. Contacts with
external electronics were realized with silver paste
(Ag L200 from Ferro) and the conductive layer was
encapsulated through lamination of PSA film from
3MTM to prevent damaging of the Cu NW networks
and to avoid direct contact of the operators with
nanomaterials for safety precautions.
Characterization
Scanning electron microscopy (SEM) images were
obtained on a FEG‐LEO XL30 operating at 5kV. The
X‐ray diffraction (XRD) analysis was performed
using Siemens‐D5000 X‐ray diffractometer with a
grazing incidence angle of 1.0°. Silicon <100> 1‐10
Ω‐cm, 4 in. wafers were used as substrates for the
copper oxide removal experiments. Cu NWs were
dropped off on cleaned silicon surfaces. Experiments
were conducted on 1 cm² samples cleaved from the
substrate. X‐ray photoelectron spectroscopy (XPS)
measurements were conducted on a NOVA‐KRATOS
model equipped with Al Kα radiation source (1486.7
eV). Transmittance values were measured on a
Varian Cary 5000 spectrophotometer using the
substrate as reference. For haze determination, total
transmittance and diffuse transmittance were
determined using an integrating sphere. The sheet
resistance was measured using a four pin probe with
a Loresta EP resistivity meter. Adhesion test was
performed with scotch tape Crystal from 3M.
3. Results and discussion
The synthesis of Cu NWs was realized according to a
modified reported procedure [21,36]. This process is
extremely simple since it only requires copper
chloride, ODA and water. We found that long
experiments afford better results. After a reaction
time of 140 h, well‐dispersed long Cu NWs were
obtained. The morphology of the nanostructures was
studied by SEM. Figure 1 shows representative
images of the nanowires at different magnifications.
The diameters of the nanowires were in the range
50–400 nm. The nanowires were very long with
lengths up to hundreds of microns. Bar charts
showing distributions of Cu NW lengths and
diameters are presented in Fig. S‐2. Possibly, some
short NWs may originate from broken long NWs
during the purification process. Interestingly, the
nanowires were not straight but showed some
curvatures as observed in Fig. 1(a).
The XRD pattern of the Cu NWs is presented in
Fig. 1(c). The peaks measured at 2θ = 43.2, 50.3 and
74.1° can be indexed to face‐centered cubic (fcc), they
are consistent with those reported elsewhere
[20,29,36]. No peaks attributed to copper oxides such
as CuO and Cu2O could be detected.
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Figure 1 (a) and (b) SEM images of purified Cu NWs (c) XRD pattern of Cu NWs
We realized electrodes using as‐synthesised
NWs, but we found that the electrical measurements
varied over a wide range and were hardly
reproducible. This problem was not observed with
Ag NWs and was thus ascribed to the propension of
copper to oxidize readily with oxygen or to form
stable bonds with amine groups of ODA. We thus
decided to use a room temperature chemical
treatment which was claimed to remove copper
oxide from a copper surface while not affecting
underlying copper [37]. We indeed observed a large
improvement in terms of performances and
reproducibility by treating the nanowires with GAA
before or after the fabrication of random networks of
Cu NWs.
As observed on the SEM images in Fig. 2(a) after
many washes, remaining organics were present on
the substrate and the nanowires, leading to a highly
resistive transparent thin film. We assume that these
organics were ODA residues. After GAA treatment
for 3 min, the substrate was cleaned and the network
became conductive despite the presence of residual
traces on the nanowires (Fig. 2(b)). After 5 min of the
same treatment, a very smooth and cleaned surface
was observed (Fig. 2(c)). The electrical properties
were also considerably improved as reported in
Table 1. It can be noticed that even after 30 min of
immersion, Cu nanowires were not damaged and the
electrical properties almost unchanged.
Figure 2 SEM images of CuNWs (a) before GAA treatment, and after treatment for (b) 3 min (c) 5 min and (d) 30 min
Table 1 Influence of GAA time treatment on electrode sheet
resistance
The effect of GAA treatment is probably twofold.
First, the carboxylic acid species are prone to react
with basic amine groups of remaining ODA used
during the hydrothermal synthesis. Indeed ODA
plays both the role of reducing agent and capping
agent [36]. Thus a very thin layer could still partly
encapsulates the surface of nanowires, preventing
good conductivity notably through prevention of
ohmic contacts at nanowires’ junctions. By
protonating the amine, GAA certainly destabilizes
copper‐amine interaction, making easier the ODA
solubilization into the liquid phase. As mentioned
hereinbefore, GAA also removes traces of copper
oxides that could limit the overall conductivity.
Electrical resistance of Cu NW based electrodes
was observed to be stable after few days, however it
significantly increased after weeks. After 4 months,
the sheet resistance was around 20 kΩ/sq, which was
much higher than the initial value. Fortunately, by
applying GAA treatment to these electrodes, it was
possible to recover the initial conductivity,
highlighting the role of GAA through the
solubilization of superficially grown copper oxides.
GAA treatment
(min) none 3 5 30
Sheet Resistance
at T=94%
(Ω/sq)
> 106 128±90 15±4 17±7
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To further investigate the influence of GAA
treatment, XPS analysis was performed to
demonstrate the copper oxide layer removal.
Comparative experiments were realized on
air‐stored and freshly treated GAA samples. Figure
S‐4 shows XPS spectra in the region of Cu 2p3/2 for
both samples. Prior to GAA treatment, typical native
copper oxide is observed. The two peaks at 933.7 and
935.1 eV, correspond respectively to CuO and
Cu(OH)2 binding energies. The third main peak
contains contributions from both Cu(0) and Cu2O
(932.6 eV). From the O 1s peak, not shown here,
deconvolution allows to distinguish between
Cu(OH)2 (531.0 eV), Cu2O (530.3 eV), and CuO (529.7
eV). No significant amount of Cu(0) is detected on
the surface of the air‐stored sample, meaning that the
oxide layer is larger than the XPS analysis depth (few
nm). After GAA treatment, the peak centered at 932.6
eV corresponding to contribution of Cu(0) and Cu2O
dominates the Cu 2p3/2 spectrum. The pronounced
shoulder due to the presence of copper oxides ( CuO
and Cu(OH)2 ) is no more visible. According to the O
1s peak analysis, peaks assigned to Cu(OH)2 and
CuO are not detected, and a slight contribution of
Cu2O peak (~ 1.4 atom %) can probably be ascribed
to undesired oxidation during air transfer to the XPS
chamber. Our XPS results are in good agreement
with those reported with similar treatment on copper
film [37], they confirm that GAA treatment removes
a thin layer of insulating copper oxides, leading to
enhanced electrical conductivity of the electrodes.
The main characteristics of CuNW based
transparent electrodes are presented in Fig. 3. The
transmittance at 550 nm as a function of the sheet
resistance is plotted in Fig. 3(a). An excellent
trade‐off between transparency and conductivity
was obtained, particularly below 90 % transparency.
For instance, the electrodes exhibited sheet
resistances of 9, 17 and 55 Ω/sq at 88, 92 and 94 %
transparencies respectively. Above 97% transparency,
electrodes were not conductive indicating that
percolation threshold was exceeded. The nanowire
density is approximately 0.021 CuNW g.m‐2 at 94 %
transmittance (see Fig S‐3 for details). It is important
to note that from a processing point of view, our
protocol does not require the use of physical
processes like high temperature (≥170°C) thermal
annealing [29] usually combined with forming gas
post‐treatment [27,28,34]. This procedure gives direct
access to functional electrodes at low temperature, it
is thereby compatible with full solution process
fabrication of heat sensitive multilayered devices.
Figure 3(b) shows a comparison of the
transmittance of a Cu NW based electrode with other
transparent thin films of conductive materials. While
ITO or PEDOT:PSS electrodes absorb light in the
near‐infrared (NIR) region, electrodes made of Cu
NWs demonstrate almost constant transmittance
over a large wavelength range. This might be of
interest for devices such as solar cells with wide
absorption spectrum [38]. The relationship between
transmittance and haze factor is plotted in Fig. 3(c).
Haze factor is a standard metric for quantifying a
film’s light scattering efficiency. It is thus a critical
parameter for optoelectronic devices [13,39,40], but it
is important to mention that there is no ideal value
for haze factor since expectations for haze values are
entirely application dependent [7]. The haze is
defined according to Eq. (1), were Tdiff is the
percentage of light diffusively scattered and Ttot the
total light transmitted.
%
100 (1)
Haze values appear to be strongly dependent on
network density. Indeed a 11% haze value was
measured at 86% transparency, whereas only 4%
were obtained at 97% transparency This is not
surprising since high density of nanowires is
expected to cause more light scattering.
To conclude about the first part of this study, it
appears that the reported chemical treatment of Cu
NWs is particularly efficient, and provides an easy
route to achieve high performance Cu NW based
electrodes, in particular when compared to other
works as shown in Fig. 4.
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Figure 3 (a) Plot of transmittance (at 550 nm) vs sheet resistance for Cu NW electrodes. Inset shows a flexible electrode on PEN
substrate (b) Plot of transmittance vs UV-Vis-NIR wavelengths (pink, blue and grey areas respectively) for several well-known
transparent conductive materials. (c) Haze value as a function of Cu NW electrode transmittance (at 550 nm) (d) Picture of a 3x3 cm²
Cu NW based electrode on PEN substrate over CEA logo
Figure 4 Comparison of the best performances of transparent electrodes based on solution synthesised Cu NWs and obtained with different post-treatments. P=Pressure; P*=Plasma cleaner; H2, N2= hydrogen and nitrogen atmosphere respectively, T= Annealing; Vac= Vacuum. [33]: Pressure (4 GPa) and hydrogen annealing at 175°C for 30 min. [27]: Plasma cleaner and hydrogen annealing at 175°C for 30 min. [29]: Vacuum annealing at 200°C during for 1 h. [28]: Forming gas annealing at 300°C
In a second part of the study, we were interested
in the fabrication of hybrid films based on CuNWs
and PEDOT:PSS, which is a commonly used solution
processable polymeric conductor. As discussed
hereinbefore, electrodes made with as‐synthetized
Cu NWs were hardly conductive without acidic
treatment. We tried to associate this polymer with
CuNWs to improve the properties of the Cu NW
based electrodes since combination of PEDOT:PSS
and Ag NWs has already proven efficient [41–44].
Thus PEDOT:PSS was spin‐coated as a thin layer (50
nm) on top of the random networks of Cu NWs. To
investigate the electrical conductivity of the Cu NWs
/ PEDOT:PSS thin films in comparison of GAA
treated Cu NW networks, sheet resistances were
measured and plotted as a function of the
transmittance (Fig. 5(a)). The 50 nm spin‐coated layer
of pristine PEDOT:PSS exhibited a sheet resistance of
3x105 Ω/sq at T=98 %. Composite electrodes
presented sheet resistances of 46 and 24 Ω/sq at 93
and 91 % transparency respectively, similar to those
obtained with Cu NWs after GAA treatment. Their
optical properties were investigated by UV‐Vis‐NIR
spectroscopy. Figure 5(b) shows a noticeable
decrease of transmittance after PEDOT:PSS
deposition in the NIR range, in accordance with the
known absorption properties of the conjugated
polymer (also presented in Fig. 3(b) at higher
thickness). However in the visible range, some
fringes appear due to the PEDOT:PSS layer and the
transmittance is slightly smaller when compared to
Cu NWs only.
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The significant modification of electrical conductivity
can be ascribed to several major phenomena. Firstly,
deposition of PEDOT:PSS could laminate the
nanowires, thus expanding the number of contacts
between NWs in the network. This was already
reported for Ag NWs [43,44]. The SEM images in
Figure 3(c) and 3(d) confirm that Cu NWs were
totally covered by PEDOT:PSS and the nanowires
were laid down on one another, ensuring improved
electrical connexions.
Figure 5 (a) Evolution of CuNWs electrode in function of wavelength before and after PEDOT:PSS coating. (b), Plot of
transmittance vs. sheet resistance for Cu NW electrode after acid treatment or PEDOT:PSS coating. (c), (d) SEM images of the
CuNWs covered by the PEDOT:PSS film at different magnification
However, to check this role of PEDOT:PSS, a
50 nm thick layer of insulating polymer
(polystyrene) was deposited on a thin film of
as‐synthetized Cu NWs. No improvement of
conductivity was observed. It can thus be deduced
that the lamination effect of spin‐coated
PEDOT:PSS layer is not sufficient on its own to
explain the large conductivity enhancement. This was also confirmed by coating GAA treated Cu
NW based electrodes with PEDOT:PSS: no
significant electrical conductivity improvement
was observed. The main reason can probably be
ascribed to the acidic character of PEDOT:PSS (pH
of the solution was measured at 2.5). It probably
acts like GAA through removal of some insulating
parts of native copper oxides and/or remaining
traces of ODA along the NWs, hence allowing
ohmic contacts at nanowire junctions. In order to
confirm the fact that PEDOT:PSS can remove native
copper oxide, we realized the following experiment.
We prepared a Cu NW based electrode and we
cleaned it with GAA (Rs=32 Ω/sq). After 60 days in
air, the sheet resistance increased up to 400 Ω/sq.
At this time the electrode was coated with a 50 nm
thick layer of PEDOT:PSS, and the initial
performances were recovered. This demonstrates
that PEDOT:PSS allows to regenerate electrodes
after a long oxidation time by removing insulating
copper oxides.
In addition to this point, the opening spaces of
the network were filled with an electrically
conductive polymer which contributes to the
overall conductivity by eventually building
conductive paths between non contacted
nanowires. Another significant advantage of the
hybrid material is the improvement of film
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adhesion on the substrate. To assess the adhesion
strength modification, scotch tape tests were
performed on Cu NW based electrodes with and
without PEDOT:PSS coating. Pictures taken before,
during, and after scotch peeling are presented in
Fig. S‐5. Like for other metallic one‐dimensional
nanostructures, Cu NW network by itself shows no
significant adhesion onto plastic substrates (Fig.
S‐5(a)). However, addition of a 50 nm thick layer of
PEDOT:PSS leads to a mechanically resistant
conductive film with strong adhesion to the
substrate (Fig. S‐5(b)).
The electrodes based on random networks of
Cu NWs, either treated with GAA or covered with
PEDOT:PSS, were used to fabricate transparent
flexible touch sensors. In both cases, protective
films were applied for safety reasons onto the
conductive layers to avoid any potential physical
contact of users with the nanomaterials. This
encapsulation has also the advantage to limit water
and oxygen diffusion to the Cu NWs, consequently
the touch sensors were found to be functional for
months. The details of the realization and
operating conditions of the touch sensor have been
described in a previous study [9]. Briefly, when a
conductive object such as a finger is approaching or
touching the electrode through the protective
coating, the local electric field is modified and
induces a capacitance change. This variation is
measured using the relaxation oscillator method
(integrated with a MSP430 microcontroller from
Texas Instrument) as illustrated in Fig. 6. To our
knowledge this is the first flexible touch sensor
realized with Cu NW based transparent electrodes.
Figure 6 Use of Cu NW based electrodes on a capacitive touch sensor. The capacitance change is operated by approaching a finger
close to the surface, which modifies oscillation values (right: 362; left: 273)
4. Conclusion
In summary, we have developed a new protocol to
fabricate high performance transparent flexible
electrodes based on copper nanowires. The
nanowires are synthesized according to a
straightforward hydrothermal hydrazine‐free
method using only CuCl2, ODA and water. In order
to obtain excellent performances (eg 55 Ω/sq at 94 %
transmittance), an acidic chemical treatment is
operated to clean up the nanowires. The
performances are among the best values reported
for Cu NWs up to now. The electrode fabrication
process is carried out at room temperature from
nanowires in solution and there is no need for
post‐treatments such as thermal annealing or
forming gas. We also demonstrate the fabrication of
hybrid materials using PEDOT:PSS with similar
optoelectrical performances and improved
adhesion property. Finally, to demonstrate the
potential of these electrodes, capacitive touch
sensors were successfully realized.
Acknowledgements
This work was funded by DGA (French Ministry of
Defense) through a PhD grant to CM.
10
Electronic Supplementary Material:
Supplementary material (scheme of transfer
process, statistic distribution of diameters and
length of Cu NWs synthetized, evolution of
transmittance as density of Cu NWs, XPS spectra,
scotch tape test picures) is available in the online
version of this article at
http://dx.doi.org/10.1007/s12274‐***‐****‐*
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