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Enhanced electrical stability of organic thin-film transistors with polymersemiconductor-insulator blended active layersJiyoul Lee, Ji Young Jung, Do Hwan Kim, Joo-Young Kim, Bang-Lin Lee, Jeong-Il Park, Jong Won Chung, JoonSeok Park, Bonwon Koo, Yong Wan Jin, and Sangyoon Lee Citation: Applied Physics Letters 100, 083302 (2012); doi: 10.1063/1.3688177 View online: http://dx.doi.org/10.1063/1.3688177 View Table of Contents: http://scitation.aip.org/content/aip/journal/apl/100/8?ver=pdfcov Published by the AIP Publishing Articles you may be interested in Phosphonic acid self-assembled monolayer and amorphous hafnium oxide hybrid dielectric for high performancepolymer thin film transistors on plastic substrates Appl. Phys. Lett. 95, 113305 (2009); 10.1063/1.3231445 Structural origin of the mobility enhancement in a pentacene thin-film transistor with a photocrosslinking insulator J. Appl. Phys. 102, 063508 (2007); 10.1063/1.2780869 Copper phthalocyanine buffer layer to enhance the charge injection in organic thin-film transistors Appl. Phys. Lett. 90, 073504 (2007); 10.1063/1.2535741 Blends of semiconductor polymer and small molecular crystals for improved-performance thin-film transistors Appl. Phys. Lett. 87, 222109 (2005); 10.1063/1.2136356 Humidity effect on electrical performance of organic thin-film transistors Appl. Phys. Lett. 86, 042105 (2005); 10.1063/1.1852708
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Enhanced electrical stability of organic thin-film transistors with polymersemiconductor-insulator blended active layers
Jiyoul Lee, Ji Young Jung, Do Hwan Kim, Joo-Young Kim, Bang-Lin Lee, Jeong-Il Park,Jong Won Chung, Joon Seok Park, Bonwon Koo, Yong Wan Jin,a) and Sangyoon LeeDisplay Device Laboratory, Samsung Advanced Institute of Technology, Yongin-si 446-712, South Korea
(Received 29 November 2011; accepted 6 February 2012; published online 22 February 2012)
We report on an enhanced electrical stability of organic thin-film transistors (OTFTs), where an
organic semiconductor (poly(didodecylquaterthiophene-alt-didodecylbithiazole) (PQTBTz-C12)) and
a polymer insulator (poly(methyl methacrylate) (PMMA)) blended film were used as the active layer,
in comparison with a single PQTBTz-C12 OTFT. While both devices exhibit similar electrical
performance in terms of mobility and ON/OFF ratios, the blended device is less susceptible to
OFF-bias stress. It is suggested that the carboxyl groups of PMMA in the blend may act as
suppressors with regards to hole accumulation in the channel, and thus, the PQTBTz-C12/PMMA
blend based OTFTs exhibit delayed threshold voltage shifts under OFF-bias stress. VC 2012 AmericanInstitute of Physics. [doi:10.1063/1.3688177]
As an alternative to conventional photolithographic
methods, the art of printing the electronic circuitry directly
on substrates, also known as “printed electronics,” has
attracted a lot of attention with regards to low-cost fabrica-
tion process.1,2 For the implementation of printed electron-
ics, polymer semiconductor that can be dissolved in various
organic solvents and functionalized in opto-electronic char-
acteristics is one of the best candidate materials. Polymer
semiconductor has, thus, been actively investigated to obtain
desired electrical properties, and many remarkable advances
in terms of charge carrier mobility have been achieved up to
date.3,4 However, despite these improvements, polymer
semiconductor based electronic devices still encounter seri-
ous issues such as electrical instability under bias stress.5,6
Such a phenomenon has been observed by many research
groups, and although it is still controversial, the associated
device degradation has been attributed to the effect of water,
oxygen, ionization potential, or structural defects. In general,
the degradation of organic thin-film transistors (OTFTs) is
manifested by shifts in the threshold voltage (VT) during
operation.5–8
In this letter, we demonstrate the realization of electri-
cally stable OTFTs by using an active layer that consists of a
blend of a polymer semiconductor and a polymer insulator.
The blending of polymer semiconducting materials is a
widely used technique in ambipolar OTFTs to transport elec-
trons and holes simultaneously by mixing n-type and p-type
semiconductors.9–11 In addition, the blending of organic
semiconductors and polymer insulators has also been used in
OTFTs for at least two purposes: reducing the environment
effects via self-encapsulation and increasing the areal uni-
formity of the device performance by controlling the self-
aggregation process.9,12–14 In such devices that involve the
blending of polymer semiconductors and insulator, the phase
separation direction (lateral or vertical with respect to the
substrate) of the blended polymer after solidification is of
fundamental importance. Generally, a lateral phase separa-
tion of blended polymer materials is suitable in order to con-
trol the crystal growth direction in the OTFT channels
(especially for soluble small-molecule semiconductor–-
polymer semiconductor or insulator) to obtain uniform per-
formance over a large area.9,15,16 On the other hand, vertical
phase separation is more desirable to lessen the susceptibility
of the OTFTs with respect to the environment. Having a
polymer insulator on top of an organic semiconductor would
passivate the latter, thus making it less prone to degradation
upon exposure to the ambient.9,14
In the present work, we rely on the vertical phase sepa-
ration of blended materials having a polymer insulator on
top of an organic semiconductor to enhance the OFF-bias
stability. Rather than by inhibiting the ambient effects, the
major improvement in device stability is based on the sup-
pression of hole accumulation at the channel region, as will
be described later on. In order to fabricate OTFT devices, a
liquid-crystalline copolymer, poly(didodecylquaterthio-
phene-alt-didodecylbithiazole) (PQTBTz-C12)17 was used
as the semiconductor, and poly(methyl methacrylate)
(PMMA) was used as the insulator. Semiconductor/insulator
blend solutions were prepared by mixing 1 wt. % of
PQTBTz-C12 (Synthesized in SAIT, Avg. Mw� 18 000)
and PMMA (Aldrich, Avg. Mw� 93 000) in chlorobenzene
(Aldrich). Thin films with various PQTBTz-C12 and PMMA
ratios were spun onto octadecyltrimethoxysilane (ODTS,
Aldrich) treated silicon oxide substrates by conventional
spin-coating. The thickness of all blended films was con-
firmed by a surface profiler to be approximately 120 nm. Co-
planar (bottom contact and bottom gate) TFT devices were
fabricated, and the electrical characteristics of devices with a
channel width of 1000 lm and a length of 100 lm were eval-
uated as shown in Figure 1. All blending ratios of PQTBTz-
C12 and PMMA (x: 1� x), where x ranges from 0.4 to 0.6,
result in devices that exhibit field-effect characteristics.
Since the transport of charge carriers within the solidified
blend film can occur only in the semiconducting PQTBTz-
C12 layer, it is anticipated that phase-separation of the two
organic components has occurred, with the insulating
PMMA layer forming on top of the stack. Figure 2(a) shows
a)Author to whom correspondence should be addressed. Electronic mail:
0003-6951/2012/100(8)/083302/5/$30.00 VC 2012 American Institute of Physics100, 083302-1
APPLIED PHYSICS LETTERS 100, 083302 (2012)
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time of flight (TOF) secondary ion mass spectrometry
(SIMS) results obtained from a spin-coated film prepared on
a SiO2/Si substrate, with a blend ratio of 4:6 by weight frac-
tion. Figure 2(a) shows that the first signal detected is oxy-
gen, which is highly likely to arise from the side chains of
PMMA. The sulfur signal is also detected at a depth of
approximately 50 nm from the top surface of the film. These
results indicate that vertical phase separation has indeed
occurred in the PQTBTz-C12/PMMA stack. It is suspected
that preferential adsorption of the relatively hydrophobic
PQTBTz-C12 onto the hydrophobic ODTS-treated SiO2 sub-
strate resulted in such phase separation.9 Grazing angle inci-
dent x-ray diffraction (GIXRD) measurements were also
carried out on the blend films to observe the crystalline struc-
ture and molecular orientation, as illustrated in Figure 2(b).
As was shown in former reports for single PQTBTz-C12
films, GIXRD patterns of a PQTBTz-C12/PMMA blend
show the presence of a well-ordered molecular structure with
a perfect edge-on orientation, indicated by narrow spots in
the out of plane direction.17 More evidence on the morphol-
ogy was obtained by tapping-mode atomic force microscopy
(AFM) as shown in Figure 2(c). The PQTBTz-C12/PMMA
blend exhibits a partially polycrystalline flake-like PQTBTz-
C12 (upper side in the AFM image) and a smooth PMMA
phase in the lower side of the AFM image.
Figures 3(a) and 3(b) show representative drain current
(IDS) vs. drain voltage (VDS) plots at different gate voltages
(VGS) for a single-PQTBTz-C12 based TFT (as a reference
sample) and a PQTBTz-C12/PMMA (4:6 weight ratio) based
TFT, respectively. The output characteristics of both transis-
tors display reasonable saturation behavior and little hysteresis
between forward and reverse sweeps. They show well-
resolved linear behavior (ohmic region) in the low drain-
source voltage range (VDS<�1 V). The output current levels
(jIDSj) of both OTFTs are similar, being larger than
0.9� 10�5 A at VGS¼�40 V and VDS¼�40 V. The transfer
characteristics were evaluated by measuring the drain current
as a function of gate voltage for the PQTBTz-C12 based TFT,
and PQTBTz-C12/PMMA based TFT is also shown in Figures
3(c) and 3(d), respectively. From the slope of VGS vs.ffiffiffiffiffiffiIDS
p,
the saturation mobility is calculated to be �0.25 cm2/Vs and
�0.20 cm2/Vs for the PQTBTz-C12 and PQTBTz-C12/
PMMA based TFT, respectively. For both devices, the
ON/OFF ratio is typically over 106, and the turn-on voltage is
FIG. 1. (Color online) Schematic diagram
of bottom-contact OTFTs and chemical
structure of PQTBTz-C12 and PMMA
used in this study (left) and the optical
micrograph (channel length¼ 100lm)
(right).
FIG. 2. (Color online) (a) TOF-SIMS
depth profiles of oxygen and sulfur in
blended PQTBTz-C12 and PMMA. The
graph shows phase separation of PMMA
(upper)/PQTBTz-C12 (lower). (b) High-
resolution x-ray scattering patterns of
PQTBTz-C12 and PMMA blended films.
(c) AFM image of PQTBTz-C12 and
PMMA blended films.
083302-2 Lee et al. Appl. Phys. Lett. 100, 083302 (2012)
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less than a volt with a relatively low sub-threshold swing
(�0.85 V/dec.). The almost identical performance of both
devices may be interpreted in such a way that the lower poly-
mer semiconductor layer formed by the vertical phase separa-
tion in PQTBTz-C12/PMMA based TFT is thick enough to
conduct hole carriers and its crystalline quality also similar to
that of the single PQTBTz-C12 based TFT as supported in
Figure 2(b).
In order to examine the electrical stability of the single-
PQTBTz-C12 based TFT and PQTBTz-C12/PMMA based
TFT, prolonged gate bias experiments were done with
VGS¼þ20 V (OFF-bias) or VGS¼�20 V (ON-bias) at
VDS¼�10 V in air ambient with relative humidity (R.H.)
�40%. Each bias stress was applied for a total duration of 10
000 s, and the stress effects on the threshold voltage were
collected before and after the stress experiments. According
to Chua et al., electrons in p-type organic semiconductor
based devices can be injected under positive gate bias into
the semiconductor even from high-work-function electrodes
such as gold, because organic semiconductor has the intrinsic
ambipolar nature.18,19 Thus, as shown in Figures 4(a) and 4(b),
for both devices, the threshold voltage shifts in the direction
identical to that of the applied gate bias polarity. In the case
of negative bias stress (ON-bias), the amount of threshold
voltage shift (DVT) is relatively small (<5 V) and almost
identical for both devices. However, a relatively large DVT
(>15 V) is observed during positive bias stress (OFF-bias)
for the single PQTBTz-C12 based TFT while the PQTBTz-
C12/PMMA based TFT undergoes smaller shifts (<5 V) in
VT. These differences are more clearly observable when we
display the threshold voltage shifts as a function of time as
shown in Figure 4(c).
In Figure 4(c), experimental results under ON bias stress
(VG¼�20 V, VDS¼�10 V) and OFF bias stress
(VG¼ 20 V, VDS¼�10 V) for both devices are indicated as
scattered points, and these fit well (solid lines) to the
stretched exponential equation,
DVTðtÞ ¼ DV0
�1� exp � t
s
� �b� ��
;
where DV0 ¼ VGS � V0T , V0
T being the threshold voltage
before exerting the bias stress. The characteristic trapping
time (s) and dispersion parameter (b) describe the trapping
phenomenon of carriers and localized energy state distribu-
tion in the channel material, respectively. This equation is, in
general, well accepted to express the associated device deg-
radation upon bias stress.17,19–21 For the ON bias stress on
both devices, the fitted s value and b value are extracted to
be �1.4� 105 and �0.29, respectively. On the other hand,
the s value of the single PQTBTz-C12 based TFT under
OFF-bias stress is �9� 103 and the b value is �0.99, while
the s and b values of the PQTBTz-C12/PMMA blend based
TFT are �5� 104 and �0.89, respectively. For the stretched
exponential function, it should be noted that the parameter sindicates the time at which the function value has reached
63% of the saturation value expected for t!1, and the
time required to reach saturation is much longer when
b� 1.21
FIG. 3. (Color online) Output curve
(VGS: 0 V��40 V) of devices with
W¼ 1000 lm and L¼ 100 lm (a) based
on single PQTBTz-C12 and (b) based on
PQTBTz-C12/PMMA blended films.
Transfer characteristics of (c) the
PQTBTz-C12 based OTFT and (d) the
PQTBTz-C12/PMMA blend based
OTFT.
083302-3 Lee et al. Appl. Phys. Lett. 100, 083302 (2012)
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The bias stress results may lead us to suspect that while
the number of shallow hole traps is identical in both devices
(similar shift in VT during ON bias), the device with the
blended active layer has a smaller number of electron trap
sites at the semiconductor/dielectric interface (smaller shift
in VT during OFF bias). One possible origin of the different
electrical stabilities between the blend film transistor and the
control device involves the different degrees of unintentional
doping caused by ambient air. The blend thin film shows a
vertical phase separation that forms PMMA barriers (which
only covers part of the thin film as shown in the AFM image
of Figure 2(c)) against diffusion of dopants/extrinsic mole-
cules. On the other hand, the control device is vulnerable to
the interaction between the polymer semiconductor under
bias stress and the extrinsic molecules in ambient air. The
higher off-current in the control device may also imply the
presence of unintentional doping. Yet, if one considers the
similar device performance of both devices in terms of field-
effect mobility and the initial threshold voltage or turn-on
voltage, the electron trap density at the semiconductor/
dielectric interface in both devices should also be of the
same magnitude. Therefore, it is believed that for the OFF
bias stress, the difference in VT arises rather from the pres-
ence of the upper PMMA layer, which contains carboxyl
groups. The carboxyl groups in the upper PMMA layer gen-
erally contain strong negative dipoles because of the high
electronegative potential of oxygen atoms (Figure 4(d)). As
a gate field is applied, the negative dipoles would decelerate
the accumulation of majority hole carriers at the channel
region of the lower PQTBTz-C12 active layer. Hence, the
PQTBTz-C12/PMMA based TFT exhibits a somewhat
delayed turn-on behavior compared to the single- PQTBTz-
C12 based TFT, as the gate voltage is swept from positive to
negative values. Negligible changes in the field-effect mobil-
ity values indicate that no additional defect states are created
at the semiconductor/dielectric interface during the bias
stress experiments.
In summary, OTFT devices with enhanced stability
were fabricated by blending the organic semiconductor
(PQTBTz-C12) with a polymer insulator (PMMA), in com-
parison with a single semiconductor PQTBTz-C12 active
layer. While exhibiting similar electrical performance in
terms of field-effect mobility and ON/OFF ratios, the device
with the blended active layer is less susceptible to positive
(OFF) bias stress. Thus, we believe that the carboxyl groups
of PMMA in the blended active layer may act as suppressors
with regards to hole carrier accumulation in the channel
region and are accompanied by delayed turn-on in the trans-
fer characteristics.
The authors gratefully acknowledge helpful technical
support of atomic force microscopy by Ms. Y. Kwon in the
AE group at SAIT, and we also thank Professor Kilwon Cho
and his colleagues at POSTECH for helpful technical sup-
port of synchrotron x-ray diffraction.
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FIG. 4. (Color online) Threshold volt-
age shift (DVT) upon negative gate bias
stress and positive gate bias stress of (a)
the PQTBTz-C12 based OTFT and (b)
the PQTBTz-C12/PMMA blend based
OTFT after 10 000 s. (c) DVT as a
stretched exponential function of stress
time for negative (VGS¼�20 V) and pos-
itive (VGS¼ 20 V) gate bias condition
for the PQTBTz-C12 and the PQTBTz-
C12/PMMA blend based OTFT. (d)
Schematic cross-sections showing nega-
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PMMA, which prevent hole accumula-
tion at the channel.
083302-4 Lee et al. Appl. Phys. Lett. 100, 083302 (2012)
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