hybrid nanocomposite materials with organic and inorganic components for opto-electronic devices
TRANSCRIPT
FEATURE ARTICLE www.rsc.org/materials | Journal of Materials Chemistry
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Hybrid nanocomposite materials with organic and inorganiccomponents for opto-electronic devices
Elisabeth Holder,*a Nir Tesslerb and Andrey L. Rogachc
Received 7th August 2007, Accepted 15th November 2007
First published as an Advance Article on the web 10th January 2008
DOI: 10.1039/b712176h
Hybrid structures consisting of semiconducting organic polymers and strongly luminescent
semiconductor nanocrystals offer favorable perspectives through highly saturated, tunable emission
and tunable absorption, in combination with an easy processability from solution and low materials
cost, which is of importance for several high-tech applications such as hybrid organic–inorganic
light-emitting diodes and solar cells. This Feature Article describes selected examples of the design and
synthesis of polymer compounds and inorganic semiconductor nanocrystals, followed by operation
principles and material choices for devices that are based on combinations of polymers with
semiconductor nanocrystals.
Elisabeth Holder
Elisabeth Holder studied
chemistry at the Eberhard-Karls
Universitat in Tubingen,
Germany and received her
Ph.D. in 2001 in the laboratory
of Prof. E. Lindner. Thereafter,
she had the benefit of a postdoc-
toral stay in Baltimore, USA at
the University of Maryland in
the Center for Fluorescence
Spectroscopy with Prof. J. R.
Lakowicz. Subsequently, she
pursued a postdoctoral stay at
the Technischen Universiteit
Eindhoven in the Netherlands in
the laboratory of Prof. U. S. Schubert. Since April 2006 she has
led the ‘‘Functional Polymers Group’’ at the University of Wupper-
tal in Germany and there she belongs also to the directorial board of
the Institute of Polymer Technology. From 2006–2007 she was
a visiting scientist at the Technischen Universiteit Eindhoven in
the Netherlands. Her research interests are in the synthesis and
characterization of new functional and macromolecular materials
involving metal–ligand complexes, organic–inorganic hybrid mate-
rials and composites for applications in light-emitting devices, solar
cells and sensors, with a focus on materials development for
engineering energy and electron transfer processes.
aFunctional Polymers Group and Institute of Polymer Technology,University of Wuppertal, Gaußstraße 20, D-42097 Wuppertal, Germany.E-mail: [email protected]; Fax: 0049-202-439-3880bOrganic Materials & Devices Laboratory, Nanoelectronic Center,Department of Electrical Engineering, Technion - Israel Institute ofTechnology, Haifa 32000, IsraelcPhotonics and Optoelectronics Group, Department of Physics and Centerfor Nanoscience (CeNS), Ludwig-Maximilians-Universitat Munchen,Amalienstr. 54, D-80799 Munich, Germany
1064 | J. Mater. Chem., 2008, 18, 1064–1078
Introduction
The motivation to control interfacial interactions on the
nanoscale leads to a new class of materials known as nanocom-
posites.1–4 The idea is to co-assemble organic and inorganic pre-
cursors into a nanocomposite material with molecular level
control over interfaces, structure, and morphology.5,6 The
designed structures may exhibit properties and functions
unattainable in the individual components. Harnessing the
advantages of organic–inorganic nanocomposite materials
Nir Tessler
Nir Tessler received his B.Sc.,
M.Sc., and Ph.D. from the Elec-
trical Engineering department at
the Technion Israel Institute of
Technology, Haifa, Israel. In
1995 he joined, as a postdoctoral
fellow, Prof. Sir Richard Friend’s
group at the Cavendish Labora-
tory, Cambridge, UK and in
1996 he demonstrated the world’s
first optically pumped conjugated
polymer laser. In 1999 he left his
advanced EPSRC fellow position
at the Cavendish to head the
Organic Materials & Devices Laboratory at the Electrical Engineer-
ing Department, Technion, Haifa, Israel. He is a member of the
Microelectronic and Nanoelectronic Centers as well as the Russel
Berry Nanotechnology Institute at the Technion. His research inter-
ests are in the field of conducting, semiconducting and light emitting
organic materials. This includes photophysical processes (including
laser action and microcavities), transport of charges and of electron–
hole pairs (executions), processing of devices and circuits (diodes,
transistors, detectors), and also the combination between synthetic
and natural (biological) polymers as a tool to extend the understand-
ing and scope of each separate system. He is furthermore interested
in new device structures and processing procedures.
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requires fine-tuning of the sizes, topologies, and spatial assembly
of individual domains and their interfaces. Furthermore, in order
to exploit the full potential of the technological applications of
the nanomaterials, it is very important to endow them with
good processability,7–20 which has ultimately guided research
towards using polymers as one of the components resulting in
a special class of hybrid materials: polymer nanocomposites.
Depending upon the nature of association between the
inorganic and polymeric components, nanocomposites can be
classified into two categories: one in which the inorganic material
(nanocrystals, colloids, polyoxometalates) is embedded in a
polymeric matrix,21 and the other where the organic polymer is
confined into an inorganic template.22 In the first case,
inorganic-in-organic composites, the good processability and
low density of the polymer component, in combination with
the high mechanical durability and well-defined optoelectronic
properties of the inorganic component, are harnessed. This
allows the combinations of the advantages of the rapidly
developing field in opto-electronic technology23 with attractive
properties of semiconductor nanocrystals (NCs). Optical proper-
ties of this class of lumophores are determined by the quantum
confinement effect, so that their emission color and the electron
affinity can be finely controlled, not only by the material choice,
but also by size within a single synthetic route. State of the art
syntheses, which can be carried out either in organic solvents
or in water, provide a broad palette of II–VI, III–V and IV–VI
NCs with variable size and a narrow size distribution leading
to narrow emission spectra—25–35 nm full width at half maxi-
mum in solution—tuneable from the UV to the near-infrared
spectral region.24,25 Proper surface passivation leads to improved
chemical stability and high photoluminescence (PL) quantum
yields of >50% for so-called core–shell NCs like CdSe/ZnS26 or
CdSe/CdS,27 where the large bandgap semiconductors (ZnS or
CdS) epitaxially overgrow the core material (CdSe) and the
band edges of the core material lie inside the bandgap of the
outer material (type I structures). Variable surface chemistry of
NCs allows for the ease of their processability from different
solvents and for their incorporation into different organic matri-
ces. The basic idea behind NC based organic light-emitting
diodes (OLEDs) is to achieve full color tuneability in a single
host material. Organic semiconductors such as conjugated
Andrey L: Rogach
Andrey Rogach received his PhD in p
in 1995 from the Belarusian State Un
at the Institute of Physical Chemistr
he also worked in 1997–2002 as a
a staff scientist. Since 2002 he has b
turing Labs at the Photonics & Optoe
Universitat (LMU) in Munich, Germ
a Principal Investigator of the Exce
was holder of the Walton Award of t
in 2005–2006. His research interest
materials, with an emphasis on the s
of colloidal semiconductor nanocryst
nanocrystal structures, energy transf
voltaics, and the use of water-soluble
systems.
This journal is ª The Royal Society of Chemistry 2008
polymers represent large polymer chains that are soft and flexi-
ble. On the other hand, semiconductor NCs as inorganic species
are robust. Inorganic semiconductors are well known to change
their emission color over a very wide spectral range, while in
organic semiconductors this effect is less pronounced and often
goes in hand with changed electrical properties. Although
organic molecules span the entire visible spectrum in terms of
emission wavelength, a change of material required to tune the
color of emission can result in a dramatic modification of the
charge transport properties and thus of the device characteri-
stics. A key goal of research into hybrid NC-based OLEDs is
therefore a separate optimization of charge transport and emis-
sion properties, which can be achieved in certain hybrid devices.6
Whereas organic semiconductors are typically hole transporting
materials, NC solids generally display strongly n-type beha-
vior,28 i.e. in most cases preferentially conduct electrons, which
make the two classes of materials a natural choice of partners.
Therefore, combination of both components within nanocompo-
sites enhances the range of potential optoelectronic applications.
Photodiodes based on organic polymers rely on the presence
of a second component facilitating charge separation, with
fullerenes being a typical example.29 An alternative way to
achieve efficient charge separation is to combine polymers with
inorganic semiconductor NCs (i.e. based on cadmium chalcoge-
nides or on lead chalcogenides). Size- and material-dependent
energy levels of a semiconductor NC allow for an elegant
solution in adjustment of their electron affinity, favoring charge
separation at the interface with polymers. The charge transfer
rate can be remarkably fast in the case of polymers chemically
bound to NCs, allowing a high percentage of excitons generated
in polymers and/or NCs to dissociate at the interface. Chemical
bonding of the NCs and polymers naturally overcomes problems
related to purely defined morphological issues of hybrid photo-
diodes. Furthermore, quantum confinement leads to an enhance-
ment of the absorption coefficients of NCs compared to the
respective bulk materials, making them efficient absorbers even
in relatively thin devices.30 The performance in such devices is
strongly dependent on the local and long-range film morpho-
logies. Such molecular and mesoscale structural features can in
many cases be modified by incorporation into a suitable polymer
host matrix to form a composite material.
hysical chemistry on synthesis and properties of silver nanoparticles
iversity in Minsk. From 1995 to 1996 he was a postdoctoral fellow
y, University of Hamburg (Germany) with Prof. H. Weller, where
visiting scientist, Alexander-von-Humboldt Fellow, and finally as
een a senior staff scientist heading the Chemistry and Microstruc-
lectronics group of Prof. J. Feldmann at the Ludwig-Maximilians-
any. He is a member of the Center for NanoScience (CeNS) and
llence Cluster ‘‘Nanosystems Initiative Munich’’ at the LMU. He
he Science Foundation Ireland at Trinity College Dublin (Ireland)
s are in the areas of chemistry and physics of nanometer-sized
ynthesis, supramolecular chemistry, spectroscopy and applications
als. His recent research activities address the formation of hybrid
er in composite nanocrystal-based systems, nanocrystals for photo-
semiconductor nanocrystals as luminescent markers in biological
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In this Feature Article, we describe examples of general
principles of device operation, followed by selected examples
on the design and synthesis of conjugated polymers and organic
compounds and inorganic semiconductor NCs, and material
choices for devices based on combinations of polymers with
NCs.
Organic LEDs
OLEDs based on charge-transporting and light-emitting organic
molecules or polymers31–33 have been gaining much interest in
both academic and applied research. In organic optoelectronic
devices there is much room to tailor both the devices and the
materials designs.
The first conjugated polymer LEDs appeared in their simplest
form and consisted of �100 nm of a PPV polymer film sand-
wiched between two electrodes: indium tin oxide, ITO (for hole
injection and transparency), and a lower work function metal
(for electron injection)34,35 (Fig. 1).
Even in these single-layer and single-material LEDs one can
consider all the basic processes which have to be optimized in
any LED. The processes leading to electroluminescence (EL) in
OLEDs, when a positive bias is applied, can be divided as
follows: charge injection and charge transport followed by
charge recombination to form excitons (singlets and triplets)
and subsequent radiative recombination of some of the singlet
excitons leading to light emission. The enormous improvement
of the performance of OLEDs over the last two decades has
been achieved by the optimization of the introduced processes
leading to light emission. The hole injection can be improved
by introduction of conducting polymers (such as PEDOT)36 as
well as by engineering the interface using monolayers that
introduce a graded bandgap or electric dipole.37,38 The electron
injection and the balancing of electron and hole injection was
largely done through systematic modifications of the polymer
structure and the resulting electronic properties.39,40 The exciton
recombination and the maximum quantum efficiency seemed to
be elusive for some time as it was believed that the maximum EL
efficiency was limited to 25% due to the formation of non-
emissive triplets. However, in recent years the use of triplet
emitters41,42 paved the way to significantly higher efficiencies by
placing the theoretical limit at 100%.14,43 At the same time it
Fig. 1 Schematic energy band representation of an ITO/PEDOT : PSS/
PPV/Ca LED, showing the basic processes leading to electroluminescence.
1066 | J. Mater. Chem., 2008, 18, 1064–1078
also became apparent that the 25 : 75 singlet to triplet ratio
is not so general and ratios closer to 50 : 50 were reported for
polymers.44,45
This field has been rapidly progressing23,46 so that the currently
available OLEDs for color application are highly advanced in
terms of lifetime (100 000 h), operation voltage (below 5 V)
and efficiency (above 20 lm W�1), and most of these record
performances are being reported by commercial companies.47–49
Organic photovoltaics
The constraints in the use of organic semiconductors in photo-
voltaic applications are very much determined by the fact that
the excited states produced by photon absorption are usually
excitons that have relatively high binding energies and do not
dissociate to give electrons and holes.32 Exciton ionization in
the bulk is therefore not a promising method to follow. However,
it is known that exciton dissociation is efficient at interfaces
formed between materials with different electron affinities and
ionization potentials, where the electron is accepted by the mate-
rial with larger electron affinity and the hole by the material with
lower ionization potential.50 The built-in potential in a single-
layer organic photodiode, which results from the difference in
work function of the cathode and anode, is usually insufficient
to induce efficient charge separation. Therefore, in order to
obtain free charges in a conjugated polymer, a more effective
exciton dissociation mechanism is required and is typically
manifested in the form of a junction. The simplest structure is
that of a bilayer heterojunction, formed by a layer of a hole-
accepting material and a second layer of an electron-accepting
material. It has been shown that if the energy discontinuity at
the junction is sufficiently large exciton dissociation (charge
generation) is efficient.51,52 The intensively studied bilayer device
is fabricated with a layer of conjugated polymer and a layer of
buckminsterfullerene, C60, where the achieved external mono-
chromatic quantum efficiency values are about 9%.53,54
Fig. 2 schematically illustrates how exciton dissociation and
charge collection can be improved by using a polymer blend as
the active layer in photodiodes. In this way, when an exciton is
created in the film after light absorption it is easier for it to
find an interface where dissociation may occur. The free charges
obtained are afterwards transferred to the appropriate phase of
electron acceptor or hole acceptor. Subsequently, they are driven
by the electrical field to the electrodes. Very recently, such
devices have been reported to top 5% power conversion
efficiency.55–57
Synthesis of conjugated polymers
Since the discovery of electroluminescence from conjugated
polymers by Burroughes, Friend, Holmes and coworkers,58 there
has been considerable industrial and academic interest in semi-
conducting polymers as the active material for EL applications.
There is a passionate pursuit of the design and development of
materials that meet application criteria such as desired emission
colors with high emission intensity and efficiency, and good
environmental stability. In particular the control of the emission
color, of charge-accepting and -transporting properties, which
are important for optimizing device efficiency, and of electrical
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Fig. 3 Some main representatives of poly(arylene vinylene)s: poly
(phenylene vinylene) (PPV), methyl ethylhexyl poly(phenylene vinylene)
(MEH-PPV), dihexyl cyano poly(phenylene vinylene) (CN-PPV).
Fig. 4 Main structure of poly(arylene ethynylene): poly(phenylene
ethynylene). R represents some oxyalkyl chains.
Fig. 2 Cross section of a hetero-junction photovoltaic device with a
conjugated polymer for hole transport and C60 fullerene for electron
transport (redrawn according to ref. 17). Phase separation increases the
number of active interfaces in the device, improving exciton dissociation.
Optimized phase separation may also improve charge transport in the
device. Holes are collected at the anode and electrons are collected at
the cathode.
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and optical stability, which are vital factors in determining device
lifetimes, must be addressed. In light absorbing applications
there is a stronger focus on a broad spectral response to the
absorbed light, the charge transport and the morphological
behavior of the conjugated polymers such as phase separation
and charge transport within the respective domains on a meso-
scopic level (nm–mm). Some of the most common methods to
address the above-mentioned issues will be briefly discussed in
the following sections.
Methods of synthesis
A large variety of homo-,59–62 co-,59,60,62–65 block co-,66–71
dendritic72–83 and end-group functionalized semiconducting
polymers84–87 has been synthesized, mainly stimulated by the
developments in the late 1980s and early 1990s. This becomes
obvious when looking at the enormous amount of scientific pub-
lications coming close to 15 000 and in the numerous review
articles dealing with these classes of polymers.59,60,62,88–108 Most
of the articles describing synthetic procedures deal with deriva-
tives of semiconducting polymers of the poly(arylene vinylene)
(PAV),58 poly(arylene ethynylene) (PAE),109 and polyarylene
(PA)40,60,62,94 families. Large numbers of derivatives have been
synthesized to optimize absorbing and emitting behavior, charge
accepting or transporting properties as well as the long-range
assembly phenomena.
Main synthetic procedures for poly(arylene vinylene)s
Widely used in the poly(arylene vinylene) (PAV) (for some
representatives see Fig. 3) synthesis are the quinodimethane
polymerization reactions such as the Wessling–Zimmerman
route,110 and modifications like the Vanderzande route,111 the
Gilch route112 or the Horhold route.113 PAVs are also available
via polycondensation reactions such as the Witting–Horner
reaction.114 Furthermore, there are transition-metal-mediated
reaction methods to obtain PAVs. Prominent is the Heck cou-
pling reaction,115 and the Stille coupling reaction.116 Metathesis
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polymerization procedures also lead to PAVs. Famous are the
Csanyi route117 and the ring-opening metathesis polymerization
(ROMP) reaction118 by Grubbs.
The structure–property relationship in PAVs regarding the
emission color is mainly affected by two structural elements:
the effects of the substituents and the degree of conjugation
along the backbone.
In EL devices balanced charge injection is a fundamental
prerequisite for high EL quantum efficiencies. PAVs represent
the most promising class of polymers with respect to the fabrica-
tion of such EL devices and consequently the optimization of the
structure–property relationship is mandatory. Hole and electron
transporting moieties can be connected to the polymer backbone
inducing improved charge transport. On the other hand, the
presence of meta-linkages or silicon atoms119 effectively reduces
the p-conjugation length of the polymer main chain. As a direct
result the emission wavelength is shifted to the blue region.97
Main synthetic procedures for poly(arylene ethynylene)s
The poly(arylene ethynylene) (PAE) (for a representative struc-
ture see Fig. 4) synthesis15,109,120,121 has been mainly developed
based on procedures of the so-called Hagihara–Sonogashira
coupling122 and by a metathesis procedure developed by
Bunz.109 The structure–property relationship of PAEs is given
by their more rigid backbone than that of PAVs, so that they
show a greater tendency to strongly aggregate which leads to
a strong red-shift of their emission in the solid state.
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Due to their rigid nature the PAEs are applied in nanotech-
nology as ‘‘molecular wires’’ or as ‘‘molecular alligator clips’’
in between two gold electrodes. Another use of these polymers
resulting from their structure–property relationship is in sensing
applications104 basically due to their high PL quantum efficien-
cies that can be efficiently quenched.97
Main synthetic procedures for poly(arylene)s
Polyarylenes (PAs) (for some structures see Fig. 5) are accessible
via the oxidative coupling of arenes,123 but also via the reductive
coupling of arenes which is namely the coupling according
to Yamamoto.124 Transition-metal-mediated cross-coupling
reactions are also paving the way to PAs: namely the Suzuki
polycondensation,125 McCullough126 and Rieke routes,127 as well
as the Grignard metathesis (GRIM) method.128 The structure–
property relationship of PAs is largely structure dependent. The
nature of the arene units strongly affects the emission. Therefore
a facile copolymer design allows tuning of the emission color of
PA polymers. Furthermore, the planarity of the PA system does
affect the emission color additionally: the more planar the system
is, the better the conjugation and thus the smaller the bandgaps.
Substituents also affect the color as steric interactions can produce
out-of-plane twisting of the polymer backbone leading to blue-
shifted emission. Since aggregation can lead to red-shifts in
emission, or enhance non-radiative pathways, attaching bulky
side groups to increase interchain separation can be used to
control the emission color and to enhance the PL efficiency. The
charge accepting and transport properties can be influenced by
introducing suitable units in the main chain, or in the side chain.
The regular alternation of electron-rich and electron-deficient
repeat units induces a high planarity of the conjugated backbone
with intramolecular charge transfer, resulting in low bandgaps.97
meta-Linkages129 or the presence of silicon atoms,119,130 amongst
others,131–133 are known to effectively reduce the p-conjugation
length of the polymer main chain, also for PAs. As a direct result
the emission wavelength is shifted to the blue region97 making
them attractive matrices for triplet emitters14 or semiconductor
NCs.61 In particular polyfluorenes40,62,94 became very prominent
as host polymers in light-emitting diodes, because of their wide
bandgap and good conducting properties. Through their
Fig. 5 Some representative structures of poly(arylene)s. Shown are
poly(phenylene) (PP), poly(3-hexyl thiophene) (P3HT), poly(fluorene)
(PF) and poly(carbazole) (PC), where R represents an alkyl chain.
1068 | J. Mater. Chem., 2008, 18, 1064–1078
modification with hole- or electron-conducting moieties, efficient
charge transport materials hosting other fluorophores can be
designed.14,43,61,134 Introducing a silicon atom in the 9-position130
allows them to be made stable against oxidation in the 9-position
that causes an undesired green emission band.130 For photo-
diodes and sensor applications on the other hand, poly(thio-
phene)s emerged to become a very important class of polymers.60
PAs are basically applied in all fields of polymer (opto)electronic
research.
Conjugated polymers used in light-emitting devices
The use of semiconducting, conjugated polymers has a long
tradition in light-emitting diodes.16,58,135 All UV-Vis colors could
be achieved.60,65,97 Furthermore, low bandgap polymers64 have
been designed for emission in the NIR region.90,136 To achieve
such low bandgap semiconducting polymers,90,92,137–140 potential
excited state electron donor and potential excited state electron
acceptor units are copolymerized (for the excited state electron
donor–excited state electron acceptor principle in order to
achieve low bandgap polymers see Fig. 6).
Electron and hole transporting functionalities have been intro-
duced into semiconducting polymers as well as emissive units
tuning the respective emission color. Recent development to
enhance the device efficiency involves the use of triplet emitters
for enhanced efficiency (theoretically 100%, 25% singlet and
75% triplet excitons that combine for the internal light emission
efficiency).43 Such systems usually consist of a fluorescent donor
and a phosphorescent acceptor. Possible triplet emitters making
all emission colors possible are mostly metal complexes of
platinum141 and iridium.14,43,142 Such phosphorescent small-
molecule OLEDs reveal external efficiencies of about 22%,14,43
while internal efficiencies of organic only polymer LEDs are
about 15–20%.143
Conjugated polymers used in photovoltaic devices
In bulk heterojunction solar cells102,144–146 traditionally two types
of conjugated polymers102 are widely used, namely derivatives of
Fig. 6 Principle of lowering the optical bandgap in low bandgap
polymer composites. Absorption takes place from the donor’s highest
occupied molecule orbital (HOMO) to the lowest unoccupied molecule
orbital (LUMO) of the excited state electron acceptor moiety. Typical
excited state electron donor moieties are thienyl derivatives and typical
excited state electron acceptor moieties are quinoxalines, benzothiadia-
zoles or thienylpyrazines.
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Fig. 7 (a) High-resolution transmission electron microscopy image of
a CdSe NC demonstrating the quality of a single crystal semiconductor
core. (b) Schematic representation of a NC consisting of a semiconductor
core coated by trioctylphosphine oxide (TOPO) molecules (c) which is
one of the organic molecules typically used as a ligand. (d) Schematic rep-
resentation of a water-soluble CdTe NC coated by short-chain mercapto-
acid molecules, another typical organic ligand.
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poly(phenylene vinylene) PPV147–150 and polythiophenes. With
poly[2-methoxy-5-(3,7-dimethyloctyloxy)-1,4-phenyleneviny-
lene] (MDMO PPV) and [6,6]-phenyl-C61-butyric acid methyl
ester (C60-PCBM) or [6,6]-phenyl-C71-butyric acid methyl ester
(C70-PCBM) efficiencies of around 3% could be achieved.151
With poly(3-hexyl-thiophene) (P3HT)152 as hole transporter
and C60-PCBM as electron transporter 5% efficiency has been
reported for optimized cells.153 Many other conjugated polymers
have been tested, but none of them could thus far (used solely)
top the 5% of P3HT, a regio-regular polythiophene with good
stacking behavior. To date, many efforts have been focused on
the design of conjugated polymers utilizing the donor–acceptor
approach90,137 (Fig. 6) in order to achieve low bandgap polymers
for tuning the absorption over the 300–1500 nm spectral range;
2.4% efficiency has been reported combining a low bandgap
polymer with PCBM,154 and it is currently an active matter of
research to reach the targeted 6–8% efficiency of this kind of
materials being announced.155 By an elegant blending approach
utilizing alkanedithiols, introduced by Heeger and coworkers,55
the efficiency of such solar cells using low bandgap polymers
can be dramatically increased to 5.5% through altering the film
morphology. The Heeger team furthermore showed an improve-
ment by changing the solar cell architecture to a tandem cell
achieving 6% efficiency.56 To the best of our knowledge, this is
the highest efficiency to date reported for organic polymer
photovoltaics. These recent and very promising developments
give realistic hope that the targeted efficiencies will be achieved
by further tailoring the low bandgap polymers and by optimizing
the morphologies of the polymer solar cells.
Fig. 8 Schematic representation of a core–shell NC and the band struc-
tures for typical type I core–shell materials CdSe/ZnS and CdSe/CdS
(reproduced with permission from ref. 24, Copyright 2004 Wiley).
Inorganic semiconductor nanocrystals
The availability of reliable colloidal syntheses leading to semi-
conductor NCs being uniform in composition, size, shape,
and surface chemistry is crucial both for the study of their size-
dependent properties and for further use in different applica-
tions. Briefly describing the state of the art in the semiconductor
NC area we outline the challenges as well as the flexibility in
defining the NC structures (organic passivation, core-only
NCs, type I and type II core–shell NCs) and hence their proper-
ties (tuneable energy levels and emission spectral range). A
typical semiconductor NC, which can also be thought of as a
colloidal quantum dot, consists of an inorganic core, which is
comparable to or smaller in size than the Bohr exciton diameter
of the corresponding bulk material, surrounded (‘‘passivated’’)
by an organic shell of ligands (Fig. 7). The choice of a suitable
capping ligand (‘‘stabilizer’’) can be considered as a key point
in an advanced colloidal synthesis of semiconductor NCs. Stabi-
lizers regulate the growth rate and the size of NCs, prevent them
(to a greater or lesser extent) from (photo-)oxidation and provide
a dielectric barrier at the surface thus eliminating (partially)
surface traps. Importantly, stabilizers, being organic molecules
with free functional groups, make NCs stable as colloidal disper-
sions in different solvents and allow their further handling
(attachment to different surfaces, covalent coupling with each
other and with other molecules, etc.). A very convenient and
generally applicable liquid–solid–solution (LSS) synthesis
approach was recently introduced allowing the synthesis of
This journal is ª The Royal Society of Chemistry 2008
numerous NCs, including TiO2, CuO, ZrO2, SnO2, CdS, Ag2S,
ZnS, PbS, MnS, ZnSe and CdSe.156
Nanocrystals for applications at visible wavelengths
The synthesis of CdSe NCs by the reaction of dimethylcadmium
with trioctylphosphine selenide in a trioctylphosphine oxide–
trioctylphosphine (TOPO–TOP)157 or TOPO–TOP–hexadecyl-
amine (HDA)158 mixtures of coordinating solvents at 250–300�C allows the preparation of NCs with sizes from �1.7 to
15 nm soluble in a variety of organic solvents like toluene,
n-hexane, chloroform, etc.
Type I core–shell nanocrystals
A large step towards the preparation of robust highly lumines-
cent NCs was the passivation of their surface with an inorganic
shell of a semiconductor with wider bandgap (usually ZnS or
CdS)26,27 in analogy with the well developed techniques for the
growth of type I quantum wells (Fig. 8). The lattice mismatch
between the CdSe core and the ZnS or CdS shell is small enough
to allow epitaxial growth, if the shell thickness is low.159 In type I
core–shell NCs the large bandgap semiconductor forms a closed
outer shell and the band edges of the core material lie inside the
bandgap of the outer material. The outer inorganic shell
J. Mater. Chem., 2008, 18, 1064–1078 | 1069
Fig. 9 Size-dependent change of the emission color of colloidal
solutions of CdSe/ZnS core–shell nanocrystals. The particles with the
smallest (�1.7 nm) CdSe core emit blue, the particles with the largest
(�5 nm) core emit red (reproduced with permission from ref. 24, Copy-
right 2004 Wiley).
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efficiently passivates core surface states and considerably
improves the chemical stability and photostability of the NCs,
resulting in high PL efficiency. Using CdSe core NCs of different
sizes for growing the core–shell particles, a series of colloidal
solutions emitting from blue to red with the emission band as
narrow as 25–35 nm (FWHM) and room temperature PL quan-
tum yield as high as 50–80% can be synthesized (Fig. 9).
Type II core–shell nanocrystals
A type II colloidal heterostructure consists of semiconductor
materials where both the valence and conduction bands in the
core are lower (or higher) than in the shell. As a result, one
charge carrier is mostly confined to the core, and the other to
the shell (Fig. 10). For CdTe/CdSe NCs, the hole wave function
is predominantly located in CdTe core, and the electron wave
Fig. 10 Schematic representation of a cross section of CdTe/CdSe NC
(left) and CdSe/ZnTe NC (right), with corresponding potential diagrams.
A 20 A core radius and a 4 A shell thickness were used in the modeling
(redrawn according to ref. 160).
1070 | J. Mater. Chem., 2008, 18, 1064–1078
function in the CdSe shell; for CdSe/ZnTe NCs the electron–
hole localization is vice versa.160 Emission from type II CdTe/
CdSe, or CdSe/ZnTe NCs originates from the radiative recombi-
nation of the electron–hole pairs across the core–shell interface,
and the emission energy is determined by the corresponding
band offset. As a result, typeII core–shell NCs emit at lower
energies than corresponding core-only materials, covering the
spectral range from 700 to 1000 nm depending on core size
and shell thickness.160
Nanocrystals for near-IR applications
In contrast to the cadmium chalcogenide NCs absorbing and
emitting in the visible spectral range, the fabrication of near-
IR nanocrystalline materials has only relatively recently been
explored.156,161–174 The use of IR emitting colloidal NCs for
telecommunications has been the subject of several reviews.175,176
In what follows, we provide some examples of IV–VI and III–V
IR active NCs; the interested reader is referred to a recent review
for details.177
PbS and PbSe nanocrystals
PbS178,179 and PbSe180 NCs are of great potential interest due to
their bulk unique properties. Bulk PbS and PbSe materials have
a cubic (rock salt) crystal structure, a narrow direct bandgap
(0.28–0.41 eV at 300 K) and a large exciton Bohr radius (for
PbSe 46 nm, about eight times larger than that of CdSe).167 As
a result, size quantization effects are more pronounced in PbSe
than in cadmium chalcogenides, and the value of the bandgap
energy makes the PbSe nanocrystals interesting as emitters in
the near-IR region.
Lead chalcogenide semiconductor NCs were first generated
inside polymer and oxide glass hosts over a decade ago.180,181 A
more versatile liquid-phase synthesis for PbSe colloidal NCs
was first reported by Murray et al. in 2001.161 In the following
year, the groups of Guyot-Sionnest164 and Krauss170 reported
simultaneously similar methods to prepare PbSe NCs. Very
small PbSe NCs (2–3 nm in diameter)162 as well as larger PbSe
quantum wires, rods, and cubes163 have also been successfully
synthesized. High quality PbSe NCs were synthesized from
lead oleate and trioctylphosphine selenide in the diphenyl
ether–TOP medium at 90–220 �C.161 The isolated monodisperse
PbSe NC fractions sized from �3 nm to 15 nm exhibit a
pronounced quantum size effect resulting in a shift of the first
absorption maximum from �1200 nm for 3 nm particles to
2200 nm for 9 nm NCs. The best reported values for PL
efficiency of PbSe nanocrystals were as high as �60%.182 The
passivation of the PbSe NC surface via the epitaxial growth of
a PbS shell resulted in an improvement of both PL efficiency
and NC stability.162
InP and InAs nanocrystals
A first step towards controllable synthesis of III–V NCs was
made by Micic et al. who adapted the Well’s dehalosylilation
reaction for the synthesis of nanocrystalline InP colloids.183
Alivisatos et al. have extended this approach to InAs.184 The
luminescence properties of as-prepared InP and InAs NCs are
rather poor as compared to those of II–VI compounds. The
This journal is ª The Royal Society of Chemistry 2008
Fig. 11 Structures of the non-interacting polymers used in blend systems for hybrid devices. Shown are the structures of MEH-PPV, MEH-CN-PPV,
P3HT, PF, F8BT, CN-PPP, PF-co-PPV, yellow-PPV and MeLPPP.
Fig. 12 Structures of PF-type polymers used in blend systems. Shown
are the structures of CP1 and CP2. CP1 represents a polycationic
semiconducting polymer, while CP2 is an end-capped PF.
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growth of an epitaxial shell of a higher bandgap II–VI or III–V
semiconductor on the core InAs NCs184 or photochemical etch-
ing of InP NCs185 increases their PL efficiency.
Semiconductor nanoparticles synthesized in aqueous medium
Various II–VI NCs have been prepared in aqueous solutions
using different thiols as stabilizing agents: CdS,186 CdSe,187
CdTe,188 CdxHg1�xTe,189 and HgTe.190 As in the non-aqueous
syntheses mentioned above, the entire spectral range from 500
nm to 2000 nm is available by varying the size and composition
of the nanoparticles. In particular, the luminescence spectra of
HgTe NCs of different sizes cover the spectral region between
1000 and 1800 nm. The luminescence quantum yields of CdTe,
CdxHg1�xTe and HgTe NCs as synthesized in water routinely
reach values of up to 40–50%.173,188
Design of conjugated polymers used inorganic–inorganic devices
The charge transport properties of NC-only films are poor,191
and it is difficult to achieve an electrical contact to single NCs
because of their small size. Taking these aspects together, these
particularities of NCs make them attractive materials for fabri-
cation of hybrid semiconductor NC/organic devices as described
below. The organic/inorganic compatibility depends on the
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Fig. 13 Structures of end-group functionalized oligomers: P3HT,86 OP-
PE(SH2)217 and PPV-SH87 as well as OPPV-PO.211 In the composites the
endgroups are connected to NCs.
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versatile chemistry of the host polymer. Hence, the polymers are
designed to attain both the optoelectronic properties desired for
the specific application in mind, and chemical compatibility
providing organic/inorganic homogeneous mixtures.
Fig. 14 Synthesis of polymer-modified
1072 | J. Mater. Chem., 2008, 18, 1064–1078
In analogy to the already very successful donor/acceptor
approach for phosphorescent systems,14 wide bandgap semi-
conducting polymers are used as donor hosts for semiconductor
NCs.61 In such blend systems, efficient energy transfer from host
(polymer) to guest (NCs) takes place when the donor and acceptor
moieties are in close spatial proximity and have a sufficient spec-
tral overlap.181,192,193 Energy and charge transfer from the polymer
to the NCs requires an energy band offset at the organic/inorganic
interface. To date, conjugated polymer hosts used in hybrid device
technology include mainly the commercially available p-type wide
bandgap polymers. MEH-PPV is the most common polymer
used as host in hybrid light-absorbing or -emitting devices.194–198
Some authors reported yellow-PPV,198 CN-PPV199,200 or methyl-
substituted ladder-type poly(para-phenylene) (MeLPPP)201 as
hosts (Fig. 11). Polyfluorene (PF) (n-type polymer),61 and several
PF copolymers such as PF-co-PPV202 and 9,9-dialkylfluorene-
benzothiadiazole (FxBT; x ¼ 6 or 8)203,204 were also recently
used as polymer matrices in hybrid LEDs (Fig. 11).
Hybrid solar cells comprise mainly MEH-PPV195,197,205,206 or
p-type semiconducting polymers of the polythiophene family
such as P3HT205,207,208 or poly(3-octyl-thiophene) (P3OT).209 A
recent example of a red PF is also available.210
Mixing NCs into commercially available cationic PF-based
polyelectrolytes (Fig. 12) resulted in improved NC stability,
and reduced polymer interchain interactions.204 These effects
are both desirable in hybrid LEDs as they enhance the device
stability and device efficiency by reducing non-radiative losses.
A competitive approach to suppress polymer host interchain
interaction is the introduction of linear84,85,211,212 and side-func-
tional,87,213 or dendritic capping ligands.214–216 Blending the
NCs with polymers was also shown to result in enhanced energy
transfer from the polymer to the NCs.214 In Fig. 13, some of the
end-group functionalized oligomers are shown.86,217
In addition to the already shown polymer blends and surface
functional oligomers, functionalized semiconducting polymers
have also been designed in order to specifically modify the
NCs.85 A direct method is shown in Fig. 14.
Another approach for polymers uses the side chains, intro-
duced in thienyl monomers, in order to design materials that
can be grafted onto the surface of CdTe NCs (Fig. 15).218
Therefore 2,5-dibromo-3-[(tetrahydro-4H-thiopyran-4-ylidene)
methyl]thiophene has been prepared and was subsequently
copolymerized in a nickel-catalyzed C–C coupling procedure.
NCs (redrawn according to ref. 85).
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Fig. 16 NC modified with thiophene dendrons (redrawn according to
ref. 215).
Fig. 15 Polythiophene-modified CdTe NC(redrawn according toref. 218).
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The surface active side chains of the polymer were utilized in
order to trap the NCs via a ligand-exchange reaction. Further-
more, thiophene dendrimers synthesized in a convergent
approach were used in order to modify the NC surface with
polymeric organic materials as shown in Fig. 16.215,216
Visible LEDs based on nanocrystal–organiccompound composites
The first paper on hybrid NC/polymer LEDs from the Berkeley
group appeared in 1994219 and reported on a bi-layer device
comprising a thin (few tens of nm) layer of CdSe NCs deposited
on a conducting support with the help of a bifunctional linker
hexane dithiol, and a 100 nm thick layer of a soluble PPV deriva-
tive. The structure was sandwiched between an ITO-coated glass
and an Mg/Ag electrode, which functioned as anode and
cathode, respectively. The device with a hole transporting PPV
layer close to the ITO, with electrons injected into a layer of
NCs and holes injected into a layer of polymer (forward bias),
exhibited an emission characteristic of the CdSe NCs at an
operating voltage of only 4 V, with an EL band tunable from
yellow to red by changing the NC size.
A subsequent paper from two MIT groups220 reported on a
single-layer device where CdSe NCs were homogeneously
distributed within a polymer layer (70–120 nm thick) of poly-
vinylcarbazole as a hole conducting component, which addi-
tionally contained an oxadiazole derivative (butyl-PBD) as an
electron transporting molecular species. The resulting volume
fraction of CdSe NCs in a film sandwiched between ITO and
Al electrodes was 5–10%, below the percolation threshold for
charge transport to occur between the NCs. The PL and EL
spectra of the devices were reasonably narrow (<40 nm
FWHM) and nearly identical, and were tunable from 530 to
650 nm by varying the NC size. Subsequent papers reported
on bi-layer devices based on core–shell NCs221,222 and showed
This journal is ª The Royal Society of Chemistry 2008
sufficient improvements over the core-only CdSe-based devices,
namely a factor of 20 increase in efficiency and a factor of 100
in lifetime.
Tri-layer hybrid NC/organic molecule LEDs with a single
monolayer of CdSe/ZnS NCs sandwiched between two organic
thin films have been introduced recently by two MIT groups.223
In these devices the external quantum efficiency exceeded 0.4%
for a broad range of luminance. At 125 mA cm�2, the brightness
of the three layer device was 2 000 cd m�2 (i.e. 1.6 cd A�1), which
constitutes a 25-fold improvement over the best previously
reported visible NC-based LEDs.221
The first hybrid NC-based LED made by layer-by-layer
assembly was reported in ref. 224. It was built up from 20 alter-
nating double layers of a precursor of PPV (pre-PPV) and CdSe
NCs capped by thiolactic acid, followed by thermal conversion
of pre-PPV to PPV. The device emitted white light originating
mainly from recombination through NC trap sites, with
a turn-on voltage of 3.5–5 V and an external quantum
efficiency of 0.0015%.
EL of different colors (from green to red) was obtained from
layer-by-layer assembled LEDs based on thioglycolic acid cap-
ped CdTe NCs of different sizes and poly(diallyldimethylammo-
nium chloride) (PDDA).225 In spite of the use of an insulating
polymer, external quantum efficiencies of 0.1% were achieved.
Light emission was observed at current densities of 10 mA
cm�2 and at exceptionally low onset voltages of 2.5–3.5 V (i.e.
only just above the bandgap of the CdTe NCs).
Near-infrared LEDs based on nanocrystal–polymercomposites
Because of the limited choice of polymers and organic dyes emit-
ting in the range of telecommunications windows (1.3 and 1.55
micron), the use of the near-infrared emitting NCs in hybrid
organic–inorganic LEDs provides a particularly attractive alter-
native. The first paper on such LEDs appeared in 2002 and
reported on single-layer blend devices.203 The devices showed
broad emission in the range of 1.3 microns, which was attributed
to the inhomogeneously broadened spectrum of the ensemble of
differently sized NCs, with a rather high turn-on voltage of 15 V
and a remarkably high external quantum efficiency reaching
0.5% at high operating voltages.203,226
In subsequent reports, EL spectra of single-layer devices based
on mixtures of PbS NCs with MEH-PPV or poly(2-(6-cyano-60-
methylheptyloxy)-1,4-phenylene) (CN-PPP) were shown to be
potentially tunable across the range of 1000 to 1600 nm.181,227,228
Internal quantum efficiencies of 1.9% could be achieved in such
diodes with MEH-PPV and PbS nanocrystals.196 Other reports
on HgTe201 or PbSe198 based LEDs showed relatively poor EL
efficiency probably due to non matched properties of the NCs
and the organic molecules/polymers hosting them.
Nanocrystal-based photovoltaic devices
Semiconductor NCs have recently been incorporated into conju-
gated polymers to create hybrid photovoltaic cells, aimed at
achieving ease of processing, low cost, substrate flexibility, large
area coverage and, from a longer term perspective, enhanced
efficiency. A particular noteworthy example is the hybrid NC/
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polymer photovoltaic device consisting of a blend of CdSe
nanorods (7 nm � 60 nm) with P3HT, which showed a solar
conversion efficiency of 1.7% (under air mass (AM) 1.5 global
solar conditions).30 The superior efficiency of this device over
net-polymer-based ones arises from the fast charge separation
at the NC/polymer interface and the enhanced electron transport
in the structure due to the relatively high intrinsic carrier mobili-
ties in inorganic semiconductor NCs. The performance of such
cells assembled from solution can attain external quantum
efficiencies of over 54% and a monochromatic power conversion
efficiency of 6.9% (under 0.1 mW per square centimeter illumina-
tion at 515 nm) in optimized devices tuning the composite mor-
phology by introducing large polymer/NC interfaces upon
thermal treatment.229 End-functionalized polymers in the hybrid
solar cells86 provided the power conversion efficiency (AM 1.5)
of 1.5%, being attached to CdSe nanorods of about 7 nm in
diameter and 30 nm in length.86
The first proof-of-principle photovoltaic device with dendritic
structures built from thienyl moieties79,82,83,215,216 appeared and
showed promise due to the favorable assembly behavior of the
thienyl dendrons used.215 Simple, not yet optimized devices
resulted in power conversion efficiencies of 0.29%. The impor-
tance of the morphology optimization in such devices in terms
of creating large interfaces becomes furthermore apparent
when looking at multi-armed CdS nanorods in MEH-PPV.230
After thermal treatment the reorganization of the inorganic
NC/polymer interface leads to an increase of exciton dissociation
efficiency in the system, providing photovoltaic devices with
power conversion efficiencies of up to 1.17% under AM 1.5
illumination (100 mW cm�2).
The use of metal–ligand complexes collecting the triplet
excitons from the conjugated polymers was also found to
enhance efficiencies in composite structures for solar cell applica-
tions.231 The system investigated was P3HT/CdSe doped with
10% of Ir(mppy)3. In such devices the short-circuit current was
found to increase by 100% revealing a much increased popula-
tion of triplet excitons.
A major drawback of the above mentioned devices utilizing
cadmium chalcogenides is that both the NCs and the introduced
polymers absorb light in the visible part of the solar spectrum
(below 800 nm), leaving a considerable amount of near infrared
solar energy (800–2800 nm) unused.
To generate photocurrent from low energy photons, narrow
bandgap NCs have been used in NC/polymer composites to
extend the photovoltaic response into the infrared.195 In this
study, PbS NCs were incorporated in the polymer matrix of
MEH-PPV, and NIR activity was demonstrated. Subsequently,
a single and double layer structure based on PbS or PbSe NCs
has been described and demonstrated spectral coverage up to
�1600 nm and power efficiencies up to 0.14%.232 The reason
for the relatively low efficiency at NIR wavelengths is directly
related to the low absorption cross section of the NCs that
becomes comparable to that of conjugated polymers only at
about double or triple the energy of the NC bandgap.198 Further-
more, it has to be mentioned that the mobility of holes and
electrons is equal in PbS NCs, which is different to typical elec-
tron acceptors such as fullerene or CdSe.233,234 Charge transport
in semiconducting polymer/PbS composite structures is still
a matter of active research.234 On the other hand, simply by
1074 | J. Mater. Chem., 2008, 18, 1064–1078
changing the hole conductor from MEH-PPV to P3OT sufficient
improvement in simple bilayer devices exceeding the external
quantum efficiency of 1% has been achieved.209 This may be
determined by rapid extraction of holes at the interface from
the NCs into the surrounding polymer, which is due to the favor-
able alignment of the heterostructure band offsets between the
polymer P3OT and the quantum-confined states of PbS
NCs.209 Introducing octylamine ligands to the PbS NCs
combined with the MEH-PPV hole transporting polymer may
be another reason for the drastic improvement of these devices.
PbS NCs used were either oleic acid or octylamine capped. The
octylamine-capped NCs allowed over two orders of magnitude
more photocurrent under �1 V bias; they also showed an infra-
red photovoltaic response, while devices using oleic acid-capped
NCs did not. Further improvement in the photovoltaic perfor-
mance of devices based on octylamine-capped PbS NCs occurred
upon thermal annealing: This simple procedure led to a 200-fold
increase in short circuit current, a 600-fold increase in maximum
power output, and an order of magnitude faster response time.
These already very promising developments in hybrid photo-
voltaic devices become apparent in many patent applications
filed recently.235–238 Novel approaches can further improve effi-
ciencies by e.g. taking advantage of multiphoton excitation239,240
in composite NC-based systems.
Conclusions
Hybrid structures consisting of semiconducting polymers and
strongly luminescent semiconductor NCs offer favorable
perspectives through highly saturated tunable emission as well
as tunable absorption features, which are of importance for
several high-tech applications such as hybrid organic–inorganic
light-emitting diodes and solar cells. The combination of organic
and inorganic components in hybrid materials offers advantages
that are not accessible with solely one of the materials classes.
Hybrid structures created by combination of inorganic and
organic components merge advantageous optical and conduct-
ing properties with robustness and flexibility. The field of
research, highlighted with selected examples in this publication,
will rapidly develop in the near future, ideally leading to a new
generation of organic–inorganic LEDs and photovoltaic devices.
Acknowledgements
EH and ALR gratefully acknowledge financial support from the
Deutsche Forschungsgemeinschaft (DFG). EH acknowledges
Prof. Ullrich Scherf supporting the Functional Polymers Group.
ALR gratefully acknowledges financial support of the German
Excellence Initiative of the DFG via the ‘‘Nanosystems Initiative
Munich (NIM)’’.
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