Energetics of molecular interfaces
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Transcript of Energetics of molecular interfaces
With organic electronics rapidly maturing, interest in
molecular electronics growing, and prospects of
single-molecule electronics improving, there is an
increasing need to understand the interactions and
electronic structure at interfaces between molecular
and nonmolecular phases1-3. The level of activity in
new materials for organic light-emitting diodes,
organic field-effect transistors, and organic solar
cells; optical or transport characterization of organic
thin films; and fabrication of other organic electronic
devices has risen dramatically over the past decade4-
6. This work has demonstrated that interfaces play a
critical role because they determine, to a large
extent, the properties and performance of materials
and devices. Interfaces become even more important
as device dimensions decrease in nanoelectronics and
single-molecule electronics.
While the properties of conventional metal,
semiconductor, or insulator interfaces are fairly well
understood, many fundamental aspects of molecular
interfaces are not. The influence of basic aspects on charge
carrier injection and transport, such as the molecule-
substrate bond, molecular orientation, geometric structure,
energy levels, and the very nature of the molecule, e.g.
conjugated/aromatic (π) bonds versus saturated (σ) bonds,
remain to be investigated systematically. Our lack of
understanding of the complete picture limits our ability to
model and control the properties of devices comprising single
molecules, molecular monolayers, or multilayered bulk films.
by David Cahen1,*, Antoine Kahn2, and Eberhard Umbach3
Energetics of molecular interfaces
1Department of Materials and Interfaces,
Weizmann Institute of Science,
Rehovoth, Israel 76100
*E-mail: [email protected]
2Department of Electrical Engineering,
Princeton University,
Engineering Quadrangle, Olden Street
Princeton, NJ 08544, USA
3Experimental Physics II,
University of Würzburg,
97074 Würzburg, Germany
July/August 200532 ISSN:1369 7021 © Elsevier Ltd 2005
Transport of charge carriers through interfaces is
crucial to all electronic and optoelectronic devices, in
particular devices based on organic molecular films
and, especially, monomolecular layers and single
molecules. The energetics of molecular interfaces are
exceedingly important, therefore, and must be
understood in detail so that we can model and
control their behavior. This knowledge, however, is
not always sufficient, as the very physics of charge
carrier transport through molecular interfaces
remains, at times, unclear. This article provides an
overview of the main issues being researched actively
in the field of interfaces involving organic molecules,
and points out areas where progress has been made
and where basic questions remain unanswered.
REVIEW FEATURE
Key issuesUnderstanding carrier transport between an electrode and a
molecule or molecular film implies an understanding of:
• The electronic energy level(s) of the molecule that are
relevant to injection into and transport through the
molecule or film, and their relative position(s) with respect
to the energy levels of the electrode;
• The chemical and electronic interaction between the
molecule and the surface, e.g. chemical bonding7, overlap
of substrate and molecular wavefunctions, and local
structural and potential modification of the surface; and
• The role of molecular structure, e.g. orientation and
conformation.
Other issues relevant to the behavior of interfaces are:
• The effects of neighboring molecules on the energy levels
and electronic structure of the molecule on which the
injected charge is localized, e.g. (de)polarization or
relaxation effects;
• The bonding and ordering of molecules at the interface,
which strongly determine the growth, morphology, and
order of the layers, and hence the film properties; and
• The nature of the second (top) contact, which depends
critically on the way it is deposited and can affect the
original molecules/substrate interface.
Several features are often directly correlated to the
properties of the interface and, as a result, determine the
optical and transport properties. These are:
• The molecular orientation, and local and long-range order;
• The size and orientation of domains; and
• The density of defects, including centers for trapping of
charges and nonradiative decay.
In the following sections, we review some of these issues,
assess our general understanding, and mention outstanding
problems that need to be addressed in order to make tangible
progress in the field of molecular electronics.
Investigation methodsMethods of choice for determining the electronic structure of
molecular interfaces are surface/interface techniques that
have a proven track record with ‘classical’ inorganic electronic
materials. Of course, the methods mentioned can only be
exemplary and reflect, to some extent, the authors’ expertise.
Direct and inverse photoemission spectroscopies
Ultraviolet photoemission spectroscopy (UPS) has been used
very successfully for mapping filled ‘frontier’ orbital states8,9,
in particular the highest occupied molecular orbital (HOMO)
of the molecule at the interface (Fig. 1). Inverse
photoemission spectroscopy (IPES), while not as widely used,
gives the most straightforward measurement of empty
‘frontier’ orbital states, in particular the lowest unoccupied
molecular orbital (LUMO) of the molecule at the
interface10-12. The combination of UPS measurement of the
HOMO and IPES measurement of the LUMO of an organic
monolayer or film is used to determine the single particle
gap, or transport gap, Et of the molecular materials. By
determining the position of the Fermi level of the metal
contact on the same energy scale (with respect to a common
reference level), the energy barrier for electron and hole
injection across the interface, i.e. the band offset, can be
derived directly (Fig. 2). Using this information, one can
achieve one of the most important goals of these interface
studies, namely the correlation of the interface barrier with
experimental electrical characteristics obtained from current-
voltage, capacitance-voltage, or internal photoemission
measurements13,14. For contacts to ‘thick’ (tens of
nanometers) molecular films, relatively good agreement is
obtained between results from photoemission experiments
and barrier heights derived from electrical characteristics15. In
these ‘thick’ systems, the current corresponds to carrier
injection into ‘relaxed’ electron or hole polaron states, and
charge transport is well described by carrier hopping. Yet,
precise determination of the energy of the transport states
62 64 66 68 70 72 74 76 78 80 82
4Å α-NPD on Au
clean Au
Kinetic energy (ev)
10Å α-NPD on Au
20Å α-NPD on Au
α-NPD on Au
hν= 82 eV
EF
HOMO
13579111315 -1 -3 -5
Binding Energy w.r.t. EF (eV)
Inte
nsit
y (a
.u.)
62 64 66 68 70 72 74 76 78 80 82
4Å α-NPD on Au
clean Au
Kinetic energy (ev)
10Å α-NPD on Au
20Å α-NPD on Au
α-NPD on Au
hν= 82 eV
EF
HOMO
13579111315 -1 -3 -5
Binding energy with respect to EF (eV)
Inte
nsit
y (a
.u.)SubstrateSubstrate
hνe-
θ
(a)
(b)
(c)
Fig. 1 (a) Deposition of a molecular film on a metallic substrate. (b) Schematic of a
photoemission spectroscopy experiment. (c) UPS as a function of film thickness for a film
of N,N’-bis-(1-naphthyl)-N,N’-diphenyl1-1,1-biphenyl1-4,4’-diamine (α-NPD)
deposited on Au. The bottom spectrum corresponds to the clean Au substrate and
provides the position of the Fermi level (EF). The two vertical lines show the position of EF
and the onset of the HOMO. Their energy separation gives the barrier for hole injection
from the metal into the molecular film φh (shown schematically in Fig. 2). The photon
energy is 82 eV (synchrotron radiation source).
July/August 2005 33
generally remains difficult because of multiple contributions
to the width of the spectroscopic peaks of the frontier orbital
states, i.e. the HOMO and LUMO, from static and dynamic
disorder, incomplete screening on the time scale of the
photoemission process, the evaluation techniques, and
experimental resolution. Thus, in spite of the considerable
progress achieved so far, there is still a need to improve
measurement methodology and data analyses. The
comparison of experimental spectra with theoretical
calculations of filled and empty states16 remains a valuable
method to achieve a better understanding and a more
accurate determination of state energies.
In contrast to the case of ‘thick’ film systems, there is still
considerable uncertainty in correlating transport across
junctions involving single molecules or molecular monolayers
with the electronic structure of the molecule and interfaces.
While it is often assumed that tunneling is the dominant
mechanism, this is not obvious in all cases17. The type of
tunneling that should be used to describe the transport,
e.g. ‘through-bond’ or ‘through-space’, also remains to be
determined for many systems3. Evidence is accumulating that
these crucial details depend not only on the specific system,
but also on the way the contacts are prepared18-21,
cleanliness of the substrate surface, purity of the molecular
materials, and, in the case of monolayers, on the quality of
the layer. It is becoming clear that the interaction between
the molecule(s) and the substrate (be it metal or
semiconductor) can be a dominant factor and control
transport across the interface22-24. Fig. 3 illustrates this for a
metal/molecules/semiconductor system. It shows
schematically how breaking a chemical bond between
molecule and electrode changes the potential profile across
the molecule. This acute sensitivity to the nature of the bond
has been used to prepare molecule-controlled, room-
temperature negative differential resistance devices25,26.
Because widespread awareness of the importance of
molecule-electrode bonds is relatively recent, comparisons
between early transport data and those transport data with
photoemission data is often problematic.
As mentioned above, the combination of UPS and IPES
provides a measure of Et for a material. Et is the minimum
energy of formation of a separated, uncorrelated free
electron and hole, and is associated with the transport of
single particles in the solid (Fig. 4). The optical gap Eopt, on
the other hand, corresponds to the onset of optical
absorption and formation of a bound electron-hole pair, or
exciton (Fig. 4). Because of the strong localization of carriers
in molecular solids (see below), the exciton is generally an
on-molecule excitation (Frenkel exciton) or an excitation
shared by neighboring molecules (charge-transfer exciton).
The Coulomb attraction between the paired electron and hole
is large, and the binding energy of the exciton EB is
significantly larger than in inorganic semiconductors such as
Si, GaAs, or ZnO. The consensus from experimental results
obtained over the past few years with various techniques, as
well as from theory10,11,27,28, is that EB = 0.5-1.5 eV in
molecular solids and 0.2-0.5 eV in polymers29,30. It is
typically ~10 meV in inorganic solids. As EB is the energy
REVIEW FEATURE
July/August 200534
Molecular film
Metal
IE
Evac
HOMO
LUMO
∆
EF
EA
φe
φh
Evac
Et
φM
Interfacialdipole
Fig. 2 Energy diagram of an interface between a molecular film and a metal surface. The
ionization energy IE, electron affinity EA, and transport gap Et of the organic film are
defined. The electron and hole injection barriers φe and φh correspond to the energy
difference between EF and LUMO and HOMO, respectively. The effect of an interfacial
dipole layer with energy offset ∆ is shown as well.
Ev
Ec
HOMO
LUMO
Evac
EF
metal
semi-conductor
metalEv
Ec
HOMO
LUMO
Evac
EF
semi-conductor
-1 -0.5 0 0.5 1-1 -0.5 0 0.5 1
Cu
rren
t (a
.u.)
Cu
rren
t (a
.u.)
Voltage[V]
Chemicallybound
Physical contactonly
EAφM
φMEA
Fig. 3 Current-voltage characteristics (left) showing the impact of a chemical bond at the
contact between molecule and electrode. The band diagrams on the right correspond to
(top) a molecule chemically bound to the metal electrode, and (bottom) a molecule with
physical contact only. The current-voltage curves refer to systems described in25,26.
REVIEW FEATURE
necessary to break the pair to create an uncorrelated electron
and hole on separate molecules, Et is larger than Eopt by a
significant amount. The difference between transport and
optical gaps could be similar for molecular monolayers and
single molecules, although the proximity of the substrate and
the absence of neighboring molecules in the latter case are
expected to affect polarization and the transport gap31.
Especially in the case of chemical bonding, the monolayer
molecules may have considerably different electronic
properties than those in the ‘thick’ molecular film. Moreover,
an optical gap may be difficult to determine in the first or
second molecular layer as a result of very effective optical
quenching32. At this point, however, there are insufficient
reliable data to draw definite conclusions on this issue.
Throughout this overview and in all contemporary
descriptions of molecule/contact interfaces, it is assumed
that electronic equilibrium is achieved – an assumption that
is questionable for thicker molecular films. The issue of
electronic equilibrium between molecules and electrodes is
especially relevant when doing electron spectroscopy, e.g.
UPS, IPES, or related techniques mentioned below, on
molecular monolayers and films. Electron spectroscopies
involve charge flow that may lead, under some conditions, to
significant charging on the time scale of the experiment33-35,
particularly on fairly insulating materials like nonconjugated
organic molecules and in thick films. These conditions must
be recognized to prevent significant errors in the evaluation
of the interface energetics. Recent work on dipolar layers
shows that equilibrium is generally achieved when doing
electron spectroscopy on single layers of conjugated
(π-bonded) molecules36, but the situation may well be
different for layers of saturated (σ-bonded) molecules.
Other spectroscopic techniques
Further techniques include two-photon photoemission
(2PPE)37,38 and near-edge X-ray absorption fine structure
(NEXAFS or XANES), which have proven to be powerful tools
for investigating energetics of organic molecular interfaces.
2PPE provides information on Et or Eopt of the molecular
material, depending on whether the first of the two
excitations is inter- or intramolecular, respectively39,40. In the
former case, the hole state is measured by a direct two-
photon excitation of an electron from the HOMO to the
vacuum, while the electron state is measured by first
populating the LUMO with an external electron, e.g. from the
metal substrate, followed by photoemission from the LUMO.
Very good agreement with Et measured by UPS/IPES has been
demonstrated41. In the latter case, the first photon excites an
electron from the HOMO to the LUMO, forming an exciton
on the neutral molecule and populating the empty state
across Eopt, and the second photon breaks the electron-hole
pair. 2PPE is therefore a very powerful and versatile tool for
investigating the energetics of metal/molecule systems. If
performed in the time-resolved mode, 2PPE becomes a
powerful tool for probing the dynamics of charge exchange
and excitation in organic systems40.
NEXAFS involves the excitation of an electron from a core
level into unoccupied orbitals. Hence, it not only provides
information about the chemical state of the molecule and the
participation of previously unoccupied orbitals in the
intermolecular or interface bonding42, but also enables the
exact determination of the LUMO energy. Moreover, it allows
determination of the molecular orientation43,44. It is also a
local probe that yields information about the spatial
distribution of unoccupied orbitals within the molecule. The
availability of third-generation synchrotron sources has
improved the energy resolution to 20-50 meV for the edges
of light elements. This now allows the study of electron-
vibronic coupling45, intermolecular interaction, and potential
anharmonicities46. Because NEXAFS has much higher
resolution (one order of magnitude) and much higher
sensitivity (two to four orders of magnitude; also causing less
July/August 2005 35
Gas phase
I
A
P-
P+
−pE
+pE
vacuumE
Condensed phase
Molecular ion
LUMO
HOMO
Et = I - A – (P+ + P-) Eopt
Neutralmolecule
Optical absorption
+ + -
-+
+
-
-
-
-
--
--
+
+
+
+
+
+
-+ Optical absorption
Single electron
Single hole
(a)
(b) (c)
Fig. 4 (a) Schematic of a molecular film with a single hole (upper left) and a single
electron (lower right) surrounded by the polarization they induce in neighboring
molecules. Also shown is an optically excited on-molecule exciton (upper right).
(b) Energy levels of the single electron and single hole in the isolated gas-phase molecule
and the condensed-phase molecule. The energy levels of the latter are shifted with
respect to those of the former by the polarization (P-, P+) induced by the charge. The
electron and hole levels define the transport gap Et. (c) Optical gap Eopt of the organic
material, defined as the energy necessary to create an on-molecule exciton.
radiation damage) than IPES, NEXAFS seems preferable for
the determination of unoccupied orbitals. Yet, the unclear
influence of the core hole makes it difficult to reach
unambiguous conclusions on the energetics.
Contact potential difference measurements
This method, which uses a Kelvin probe, provides a totally
noninvasive means of investigating energetics of surfaces and
incipient interfaces47. The technique gives a precise measure
of the work function of the surface under investigation,
relative to the work function of the probe. For a given
surface, changes in work function and, in the case of
semiconductors, of electron affinity, ionization potential, and
band bending, can be followed as a function of surface
treatment, e.g. molecule adsorption, in various ambient
atmospheres or ultrahigh vacuum (UHV). The latter provides
the necessary link with photoemission data, which, by the
nature of the method, reflects the situation in vacuum.
Comparison between measurements in ambient and UHV
leads to an assessment of the effects of ambient exposure on
the contacts. This is of considerable importance for two
critical issues of molecular devices, i.e. their fabrication
environment and stability.
Spectroscopies based on scanning probe techniques
Methods like scanning tunneling spectroscopy (STS)31,48,49
add considerable insight by measuring filled and empty
transport levels with molecular spatial resolution. The
techniques can be seen as the energy spectroscopy
complement to contact-mode atomic force or scanning
tunneling microscopy for measuring current transport
through single (or small numbers of) molecules50,51. Because
other methods provide an average over large ensembles of
molecules, comparing the results with STS measurements
provides crucial information on inhomogeneities at interfaces
(see below). An alternative approach to gauge the
homogeneity of the interface relies only on scanning probe
measurements by collecting and comparing many single-
molecule or small-domain experimental results22.
A difficulty inherent to scanning tunneling techniques,
especially STS, is in understanding the degree to which the
high electric field developed between the tip and the surface
(or molecule) drops mostly in the physical gap or modifies
the energy levels of the molecule or molecular film. This issue
is not restricted to molecular solids, and band dragging is a
well known phenomenon when performing STS to measure
inorganic semiconductor band gaps48. STS has been
performed on single molecular layers and has produced
results in good agreement with UPS/IPES techniques31. For
thicker films, STS with penetration of the tip into the film has
been performed successfully for molecular materials and
polymers29,49, although the invasive tip-molecule contact
raises some questions about the chemical interaction
between tip and molecules and the specific energy levels
probed by the technique.
Finally, a frequent difficulty with these and most other
types of measurements, especially for thicker films, is that
the interface relevant for current transport is buried below a
layer that is thicker than the probing depth of the technique.
A recent study52 of a metal/polymer interface via ballistic
electron emission microscopy (BEEM) is a first attempt to
probe the buried interface with spatial resolution. So far,
however, methodologies involving measurements as a
function of increasing film thickness have proven to be the
most practical way to circumvent the problem. While the
buried interface is less of a problem for monolayers, making
measurements as a function of partial monolayer coverage
can yield important information on the evolution from the
free contact surface to the interface of interest53.
Theory and experimentThe comparison between experimental and theoretical results
on interface electronic structures plays a crucial role in the
process of understanding contact/molecule interfaces. The
fundamental difficulty here is that electrons in molecules are
described using localized electron models, while electrons in
the metal or semiconductor contact are described using a
delocalized picture with periodic boundary conditions.
Combining these two approaches poses a challenge for
achieving a consistent, unified energy level model for
interfaces. Current methods use one of the two descriptions:
the localized54 or delocalized approach55. The latter is
problematic for single molecule work because of the periodic
boundary condition. The former requires the use of large
clusters to obtain an electron density at the Fermi level and
describe the metal contact correctly. In both cases, the
problem is one that can be overcome with enough
computational power or the development of fast algorithms.
Relevant energy levelsOne of the most important, and so far unresolved, issues in
single-molecule transport is to identify the specific energy
REVIEW FEATURE
July/August 200536
REVIEW FEATURE
levels that are involved in the process. All the research efforts
described above are aimed at providing the ‘right’ energy
levels/bands for defining barriers to electronic charge carrier
injection and transport. This task is easiest if the molecules
are inert toward the contacting material, i.e. the only
interactions are of the van der Waals type. The problem is
more complex when stronger chemical interactions take
place, even if electronic equilibrium (see above) is assumed.
The choice of relevant energy levels for injection and
transport in a macroscopic inorganic metal/semiconductor
system is clear. These levels include the metal Fermi level and
the top of the valence band (for holes) or bottom of the
conduction band (for electrons) of the semiconductor. For a
thick organic semiconductor layer, injection and transport
involve carriers (polarons) that thermalize to the lowest-
energy transport states. The valence and conduction band
edges of the inorganic semiconductor are replaced by the
transport states, i.e. the HOMO and LUMO levels of the
molecule, measured as described above. Good correlation
between interface energetics and injection and transport data
is generally obtained in these cases15. In metal/single
molecule or molecular monolayer/metal systems, however,
questions remain concerning the transport mechanism(s), the
electron-molecule interaction, and the time scale involved in
the process. The nature and energy of the molecular orbitals
involved in injection and transport are not known a priori. In
the Au-S-alkyl chain-S-Au system, the highest occupied alkyl
orbital is more than 3 eV below the Au Fermi level. If the
transport experiments are interpreted in terms of carrier
tunneling through a square symmetric barrier, the height of
the barrier is, at most, 1.5-2 eV (assuming an effective
electron mass of 1)56. The only occupied level that might
fit this picture is the one localized on the S at the very
interface with Au57,58. However, if the tunneling barrier is
determined by this molecular level, the mode of transport of
the electron through the rest of the molecules remains
unclear.
This very important example shows the fundamental
problem faced in predicting the barrier for charge carrier
transport between molecules and contacts. Resolving these
basic issues also requires a consistent understanding of both
the occupied and unoccupied energy levels at the interface,
as well as variations in electrical potential across the
interface. Without this, distinguishing between nonresonant
(through-space) and resonant (through-bond) tunneling
becomes very difficult. Finally, thermionic emission can also
become important with semiconducting contacts13,59.
Interacting versus noninteractingcontacts The contacts that are easiest to describe, and whose
properties are most reliably predicted, are those between a
substrate and a noninteracting molecule. In metal/organic
film interfaces, where the metal-molecule interaction is not
dominated by a strong chemical reaction, progress toward
predicting interface energetics and injection barriers has used
models related to interface induced density of states60. The
physical proximity of the metal and organic semiconductor
broadens the molecular energy levels and results in a quasi-
continuum of states in the band gap of the organic film in
the first molecular layer or two, i.e. the induced density of
interface states. The relative position of the contact Fermi
level and charge neutrality level of this induced density of
states defines charge transfer across the interface and the
interface energetics. These models, in accord with
experimental results61,62, clearly point out that metal/organic
interfaces generally do not follow the Mott-Schottky model63
and that, as is found for their inorganic counterparts, their
electronic structure is dominated by charge exchange
between the contact material and interface states. Exceptions
to the departure from the Mott-Schottky model have been
seen with polymer/metal interfaces. However, these systems
are generally fabricated ex situ from a liquid phase, where the
metal surface is fundamentally changed with respect to the
intrinsic surfaces considered above.
As is well known from ‘classical’ metal-semiconductor
contacts, reactive contacts deviate from behavior predicted
on the basis of standard models and energy levels/bands of
the isolated components. Electronic states resulting from the
interface chemistry generally dominate the energetics64. The
same is true for contacts to molecules65. In the latter case,
the energetics even depend on the chemical bonding, the
molecular orientation, and co-adsorbates. The resulting
interface dipole, which essentially determines the band
offsets, may vary between -1 eV and +1 eV or more, even for
the same molecule and substrate in different adsorbate
bonds66. In molecular electronics involving nonconjugated
molecules, the issue is complicated by the finding that
considerably more efficient charge transport is found if the
interface is reactive, i.e. if the molecule and substrate form a
July/August 2005 37
chemical bond, than if it is chemically nonreactive (see
Fig. 3)3. This means that the most attractive molecular
electronics systems might be those whose behavior cannot
be predicted from knowledge of the isolated components,
emphasizing the crucial importance of interface studies.
If the polar character of the substrate-molecule bond can
be estimated, then a model of interface dipoles67 that
reproduces the behavior of a wide range of ‘classical’ metal-
semiconductor contacts is likely to be another useful step.
These dipoles are important for the energy level alignment at
the interface (see Fig. 2). Another factor that needs to be
considered in constructing an energy level diagram is that
bonding at the interface leads to the formation of new
molecule/substrate states. This has been well known in
surface science for decades, and can be described in the
simplest way by the Andersen-Newns (molecular orbital
interactions) model, yielding energy levels different from
those of the components. The occurrence of such states is
quite common for π-bonded aromatic molecules with
functional groups, even though bonding may preferentially
involve frontier orbitals located on the aromatic part68. The
new interface orbitals may insert gap states that facilitate
charge carrier tunneling by introducing a chemisorbed
molecular monolayer between the substrate and the
transport layer21. Thus, one can argue that only knowledge of
the exact chemistry and structure (molecular orientation and,
for monolayers, lateral order) of the interface will allow a
true description of its electronic structure.
Single molecule versus monolayerIn addition to the interface mechanisms mentioned above,
the energetics of the contact between a given substrate and a
molecule will be affected in two major ways by the presence
of neighboring molecules surrounding the central molecule.
The first effect is the stabilization (lowering) of the energy
level of the injected charge because of electronic polarization
of the metallic contact (i.e. by the image charge) and of
adjacent molecules, especially if they are π-bonded69. The
electron density in the metal and the molecular layer
responds very rapidly to the presence of the excess charge
and ‘screens’ it to some extent. In the bulk of the molecular
film, this screening, or polarization, accounts for the >1 eV
difference between the ionization energy (or electron
affinity) of a single gas-phase molecule and the molecule in
the condensed phase. The screening by the image charge is
even larger70. On the metal surface, the difference in
polarization between a single molecule and a molecule in a
saturated, packed monolayer can be as large as a few
hundred millielectronvolts31,71-73, depending on the molecule
polarizability and packing structure. In the case of
chemisorption, there may be an effective charge exchange
between metal and molecule after creation of a charge in the
chemisorbed molecule. This exchange leads to charge
delocalization and, as a result, the difference between an
ionized molecule in the gas and chemisorbed phases may
amount to a few electronvolts. The second effect, which is
crucial in layers of intrinsically dipolar molecules or
chemisorbates involving considerable charge transfer, is
depolarization. When dipolar molecules pack closely on a
surface, dipole-dipole repulsion causes a change in charge
distribution within the molecules or between the molecules
and the substrate. The former is well known and has been
described by Topping74,75. Molecular depolarization, brought
about by molecular distortion, has been observed for dipolar
silanes on SiOx/Si76,77. Depolarization via charge transfer
between molecules and a metal substrate was invoked to
explain unusual giant magnetism in normally diamagnetic
molecules of a normally diamagnetic substrate78.
Another effect altogether has been suggested to explain
the much higher current densities obtained with single
molecules than with monolayers of identical molecules. The
lower energies of vibrational modes of single molecules
versus a molecular ensemble, presumably because of steric
hindrance, make these modes more readily accessible for
charge transport via hopping79. It is likely that the strength of
bonding to the substrate plays an important role in both the
ability to have hopping transport and molecular distortion, an
issue that remains to be explored.
Interface polarization and equilibriumThe importance of molecular and interface dipoles has
already been noted. Here, we briefly dwell on the issue of
interface polarization and how it affects interface energetics.
The concept of interface dipoles can explain how molecules
equilibrate electronically with the contacting material.
Predicting interface dipoles requires understanding the cause
of their formation and origin. The simplest approach is
intuitive and based on chemistry and electronegativity
differences. Both atomic and group electronegativities can be
used. We can again consider the much-studied Au-thiol
REVIEW FEATURE
July/August 200538
REVIEW FEATURE
systems to see the main problem with this approach. Several
electronegativity scales are available and it is not obvious
a priori which one to use. On each side of the Au-S bond are
a molecular system (ending with the S atom) and a metallic
one (Au). If we use the Phillips-van Vechten scale80, derived
for nonmolecular systems, the bond is found to be quite
polar with S negative compared to Au. The same holds if we
use the Allred-Rochow scale81. However, if we use the
Pauling scale80,81, which was derived for isolated molecules,
the bond is nonpolar – more in line with the interpretation of
experimental data82,83. Alternatively, we can turn to
quantum mechanics, foregoing the convenience of intuition.
We can hope that, as theoretical descriptions of the
molecular (localized)/nonmolecular (delocalized electron)
interface develop, theory will provide easy-to-use predictive
tools beyond those based on electronegativity.
The critical role of interface polarization is driven home by
our recent results that show total inversion of free molecule
dipole moments as a result of molecule-metal contact
interaction (see Fig. 5)18,20. This phenomenon is most
remarkable, as it does not occur upon chemical binding of the
molecule to the substrate, but upon metal contact deposition
on the molecule, i.e. at a supposedly noninteracting interface.
Interface homogeneity There are generally two ways to approach this issue. One is
to start with ‘ideal conditions’, i.e. a highly ordered, single-
crystalline substrate surface; a highly ordered, well-
characterized interface layer; one or more epitaxially grown
homogeneous molecular layers; and a carefully prepared
second (top) contact, and then measure transport, optical, or
(opto)electronic properties. This approach is well-established
in inorganic semiconductor physics and surface science, but
very difficult to achieve in organic hybrid systems because of
the difficulties of preparing homogeneous epitaxial layers and
top contacts. Some of these steps have been achieved with
organic systems, i.e. the preparation of highly ordered
molecular interface (mono)layers on highly ordered substrate
surfaces84-87. Even the homogeneous and epitaxial growth of
an organic film on a metal substrate can be achieved in
specific cases88,89. The final step, i.e. deposition of
homogeneous top contacts onto the molecule(s) and
molecular films, without damaging the molecules for the
measurements of transport properties is still problematic. As
discussed elsewhere in this issue, several approaches are
being pursued19,90,91, but deposition on epitaxial films has, by
and large, not yet been realized. Nevertheless, studies of the
first steps have already shown how complicated, for instance,
interface preparation can be. For example, depending on
temperature, coverage, deposition rate, and co-adsorbate,
deposition of a molecule on a substrate can result in several
different geometric structures with significantly different
chemical bonding92 or molecular orientation93, resulting in
very different interface dipoles66.
The second approach starts from a ‘real’ system and
attempts to correlate its homogeneity with other properties.
Because most techniques for interface characterization
average over macroscopic dimensions, extracting information
on structural heterogeneity is problematic. Scanning probe
methods can alleviate the problem if the measurement does
not interfere with the molecular structure (e.g. if used in
noncontact mode). For inorganic metal/semiconductor
interfaces, the effect of inhomogeneity on electronic
transport across the interface has been studied thoroughly
and fairly accurate models have been developed94,95. For
molecular contacts, the problem is exacerbated by the
limited purity of many of the compounds normally used in
research96. The degree of homogeneity is likely influenced by
the strength of binding of the molecules to the surface. Thus,
Bias [V]0.2 0.3 0.4 0.5 0.6 0.7
0
100
200
300
400
500
Cu
rren
t [
Me H
CN
bare
CN > H > Me
Bias [V]0.2 0.3 0.4 0.5 0.6 0.70.2 0.3 0.4 0.5 0.6 0.7
0
100
200
300
400
500
0
100
200
300
400
500
Cu
rren
t [C
urr
ent [
Me H
CN
bare
CN > H > Me
Cu
rren
t (µ
A)
CO2HHO2C
OOCC OO
XX
n-GaAs
Au
OO OO
X X
0 0.1 0.2 0.3 0.4 0.5
0
2
4
6
8
10
CN
H
Me
bare
CN < H < Me
Cu
rren
t (µ
A)
Bias [V]0 0.1 0.2 0.3 0.4 0.50 0.1 0.2 0.3 0.4 0.5
0
2
4
6
8
10
0
2
4
6
8
10
CN
H
Me
bare
CN < H < Me
Cu
rren
t (µ
A)
Bias [V]
∆EA = EA - ∆φmol.dipole
∆EA = EA + ∆φmol.dipole
∆φb = M −∆EAsemiconductor
B
A
φ
Fig. 5 Effect of the nature of the molecule-metal electrode contact on current-voltage
characteristic of Au/molecules/n-GaAs diodes (molecule shown at top left; device
schematic at bottom left). The molecules, which are chemically bound to the GaAs, are
changed systematically. ∆φb is the change in Schottky diode barrier height. ∆φmol.dipole is
the change in electrostatic potential as a result of the interfacial molecular dipole layer.
All other symbols are as described in Fig. 2. In panel (A), the change in EA is determined by
the free dipole moment, as explained elsewhere33,103. In panel B, the effect is inverted
because of the interaction between the molecules and the metal spill-over electron
density18,90, which is the result of intimate contact between metal and molecules.
July/August 2005 39
very strong bonding (e.g. phosphates to oxides) can leave
many molecules in nonequilibrium binding configurations,
while some weakly binding molecules (sulfides to most noble
metals) may not bind at all or only intermittently97. In both
cases, a variety of substrate-molecule orientations may
result, rather than the preferred one. The strength of
intermolecular interaction is important as it can force even
weakly binding molecules to order on a surface53,98,99.
Most molecular films include structural inhomogeneities
that have an impact on their electronic structure. Interface
inhomogenities can be a result of evolution of orientation in
the first two or three molecular layers closest to a metal
surface. The change in molecular orientation, from flat on the
metal surface to more vertical in the bulk, can give rise to
shifts of the frontier electronic levels by 100-200 meV, as
demonstrated by UPS100. These shifts can affect the
interpretation of spectroscopic measurements used to
determine interface energetics, as well as the charge injection
characteristics of the interface, in ways that have not yet
been fully evaluated. Another example concerns structural
defects, which result from growth constraints and can be
found in highly ordered molecular films101. These defects
affect charge carrier transport through ordered molecular
films. They also give rise to new electronic states, which can
extend into the band gap of the pristine material102.
Conclusions and summary While our understanding of metal/bulk organic interfaces
with either strong or weak chemical interaction allows clear
correlation of charge injection and transport with measured
interface energetics, the same cannot be said for single-
molecule or monomolecular film junctions. For these
interfaces, the presence or absence of charge transfer and
chemical bond formation matters considerably when looking
at interface transport. At the same time, single-molecule and
monomolecular layer interfaces, in particular those involving
strong chemical bonds, also appear to be the most interesting
for molecular electronics. Understanding their properties and
behavior will require work in both theory and experiment,
preferably in a coordinated manner.
The most exciting directions for theoretical work are in the
extension of existing concepts from inorganic systems to the
molecule/conductor interfaces, and toward bridging the
localized/delocalized electronic structure calculation gap. The
stronger the interactions at these molecule/substrate
interfaces, the more likely it is that knowledge of the
chemistry and structure of the molecular interface will be
necessary for accurate description of the electronic structure.
Unfortunately, though, this will come at the expense of
generalizing results to wider classes of interfaces.
On the experimental side, more of the reproducible, high-
quality data that are starting to be produced are needed. The
data are necessary to allow controlled comparisons between
systems prepared and measured in UHV and in ambient, as
well as to compare spatially averaged with spatially resolved
results. The latter will become progressively more important
as dimensions shrink and the heterogeneous nature of these
interfaces are more strongly expressed in the results.
In all cases, the critical issues for molecular electronic
devices remain the understanding and prediction of the
energy barriers for charge carrier injection, the homogeneity
of the barriers across the systems, and the development of
accurate theoretical tools to investigate these barriers. MT
AcknowledgmentsThis article is based to a large degree on what we learned from organizing, participating in,
and summarizing the 306th W. E. Heraeus Seminar on ‘Energetics of Interfaces between
Organic Molecules and Conductors’, held in March 2003 in Bad Honnef, Germany. We
thank the W. E. Heraeus Foundation for making that seminar possible and all the
participants for their contributions. DC thanks the G. M. J. Schmidt Minerva Centre for
Supramolecular Chemistry and the Philip M. Klutznick Research Fund at the Weizmann
Institute, and the Israel Science Foundation (Jerusalem) for support. AK thanks the US
National Science Foundation (NSF), grant DMR-0408589, the New Jersey Center for
Organic Optoelectronics, and the Princeton MRSEC of the NSF.
REVIEW FEATURE
July/August 200540
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