Thin-film metal oxides are among the key materials used in organic semiconductor devices. As there are no intrinsic charge carriers in a typical organic semiconductor, all charges in the device must be injected from electrode/organic interfaces, whose energetic structure consequentially dictates the performance of devices. The energy barrier at the interface depends critically on the work function of the electrode. For this reason, various types of thin-film metal oxides can be used as a buffer layer to modify the electrode work function. This paper provides a review on recent progress in metal oxide/organic interface energetics, oxide valence structure and work function, as well as the impact of defects and interfacial reactions on oxide work functions. This review provides a rational guide to process engineers in selecting the best suitable electrode/oxide structures for a targeted applications.
Introduction to organic electronics
The past three decades have seen major improvements in organic semiconductor devices. Technologies such as organic light-emitting diodes (OLEDs), organic photovoltaics (OPVs) and organic field-effect transistors (OFETs) have been steadily evolving and have begun to penetrate the mainstream consumer electronics market.
OLED displays are arguably the most mature of the organic semiconductor technologies. Ultra-high-resolution OLED displays—with high brightness, extreme contrast ratios, rich color reproduction and extended operating lifetimes—are already available in the consumer electronics market. The next major developments in OLED technology will likely be in the sector of high-efficiency illumination products, where improvements are still needed in terms of color-rendering index, high efficiency at high brightness and operating lifetime.
OPVs have also seen great progress in recent years, with power-conversion efficiencies increasing from 2.5% in 2001 to 9.2% in 2012.1, 2 Commercial products are beginning to emerge in the consumer electronics market, and as operational lifetimes and power-conversion efficiencies continue to improve, there is good reason to believe that OPVs will continue to increase their share of the market in coming years.
Major developments have also been seen with OFETs—a technology that enables computer processors and display devices to take the form of flexible plastic sheets, using inexpensive production techniques.3, 4 There is even the possibility of light-emitting OFETs that allow display devices to be designed without the need for independent display drivers.5 With recent improvements in driving voltages, switching speeds, on–off ratios, power consumption and operating lifetimes, these devices will likely show up soon in niche, mobile communication markets.6, 7, 8, 9, 10
The rapid development of organic electronics over the past few decades is a result of a large-scale, concerted effort from the science and engineering research community. One of the major areas of development has been in the field of interfacial engineering.
Organic electronic devices are generally composed of multiple layers of various materials. During device operation, charge carriers must pass through these materials, and therefore electrons must cross several interfaces along their paths. The interfaces often possess an energetic barrier that hinders the passage of charge carriers. Such ‘interfacial charge-injection barriers’ give rise to high driving voltages and low power efficiencies in organic electronic devices, thereby reducing device lifetime and negating the possibility of lightweight high-efficiency portable electronic devices.
One of the most important types of interface in an organic device is the interface between an electrode material and an organic semiconductor. These interfaces must allow charge carriers (either electrons or holes) to easily pass across the material boundary with minimal resistance.
Low-resistance electrode/organic interfaces are not as easy to achieve as one might think. The need to solve this problem gave rise to the field of interfacial engineering in organic electronics.11, 12 Interfacial engineering often involves tailoring the electron energy levels of the materials that are in contact with one another, in order to minimize or eliminate the charge-injection barrier.
The magnitude of a charge-injection barrier depends on the relative positions of donor and acceptor energy levels on either side of an interface.11, 13, 14, 15 The alignment between donor and acceptor levels is often referred to as energy-level alignment (ELA). For an organic semiconductor, the donor level is the highest-occupied molecular orbital (HOMO) and acceptor level is the lowest unoccupied molecular orbital (LUMO). For conductive electrodes, the Fermi level (EF) serves as both the donor and acceptor level.
The ELA criteria vary slightly for different types of organic devices, as illustrated in Figure 1. In OLEDs, there are two types of charge-injection contacts; electron-injecting and hole-injecting contacts. Low-resistance electron-injecting contacts require that the donor level of the electrode (that is, the cathode) be closely aligned with the LUMO level of the organic semiconductor. Conversely, low-resistance hole-injecting electrodes (that is, anodes) require that the electrode’s acceptor level (that is, Fermi level) is closely matched with the organic’s HOMO level.
In p-OFETs, there are hole-injecting contacts (Figure 1c), where the Fermi level of the source electrode should align with the HOMO of the organic semiconductor to minimize the hole-injection barrier. In n-OFETs, there are electron-injecting contacts (Figure 1d), where the Fermi level of the source electrode should align with the LUMO of the organic semiconductor to minimize the electron-injection barrier.
With OPV’s, the scenario is slightly different (Figure 1b). One often refers to hole-collecting and electron-collecting electrodes, rather than hole-injecting and electron-injecting electrodes. A hole-collecting electrode should have its donor level closely aligned with the organic’s HOMO level, and an electron-collecting electrode should have its acceptor level closely aligned with the organic’s LUMO level to minimize energy losses.
Interface engineering, in the context of organic electronics, involves tailoring the ELA between the electrode and the organic material, often via some sort of surface treatment to the electrode material, or by incorporating a thin buffer layer between the electrode and the organic. Common surface treatments include halogenation,16, 17, 18, 19, 20 plasma reactions,21, 22, 23, 24, 25, 26, 27 UV-ozone28, 29, 30 and controlled air exposure.31, 32, 33, 34, 35, 36 Buffer layers include vapor-deposited small molecules,37, 38, 39 spin-cast polymers,40, 41, 42, 43, 44, 45, 46 inorganic salts,12, 47, 48, 49, 50, 51, 52 covalently bound self-assembled monolayers53, 54, 55, 56, 57, 58 and thin metal oxide layers.59, 60, 61, 62, 63, 64, 65, 66, 67, 68, 69, 70, 71, 72, 73, 74, 75, 76, 77, 78, 79, 80, 81, 82, 83, 84, 85, 86, 87, 88, 89, 90, 91 This review concentrates on the use of transition metal oxides as buffer layers in organic electronics.
Transition metal-oxide buffer layers
Transition metal oxides are particularly versatile materials for use as buffer layers, as they can be used to achieve efficient charge injection for nearly any type of electrode. The first reported use of oxide buffer layers in OLEDs was by Tokito et al.61 in 1996. Now, transition metal oxides are heavily utilized in OLEDs,60 OPVs,92, 93, 94, 95, 96, 97 and OFETs,98, 99, 100, 101, 102, 103, 104 and are components in many of the current record-breaking devices reported in the literature.2, 105
Transition metal oxides can possess a wide range of work functions, spanning from extreme low of 3.5 eV for defective ZrO2 to the extreme high of 7.0 eV for stoichiometric V2O5.106 High-work-function metal oxides are often used as hole-injecting buffer layers for anodes,60, 61 including MoO3,61, 62, 63, 64, 65, 66, 67, 68, 69, 70, 71 WO3,72, 73, 107 NiO,74, 75, 76, 77, 78, 79, 80, 81, 108 CuO,82, 83 RuO2,61 V2O5,61, 84, 85, 86 Fe3O487 and Ag2O.88, 109 The low-work-function transition metal oxides—such as TiO2,89 ZnO90, 104, 110 and ZrO291, 111—are used as electron-injection buffer layers for cathodes. Some oxides can be evaporated at relatively mild temperatures—such as MoO3, WO3 and V2O5—and are used for devices that are fabricated in vacuum. Other oxides can be solution deposited—such as NiO,80, 112 V2O5,96, 113 TiO2,89, 114 WO3,95 ZnO,115, 116 MoO3117 and sub-stoichiometric MoOx118—making them convenient to use as buffer layers in solution-processed organic devices.117 There has also been some use of sub-stoichiometric oxides, such as WO3−x,119, 120 and MoO3−x,118, 121, 122, 123, 124 which tend to be metallic and can provide low-resistance buffer layers.
ELA and the importance of electrode work function
It has been known since the early studies on organic interfaces that electrode work function is an important parameter for ELA.11, 125, 126, 127, 128, 129 However, because of the complexity of interfaces, it has taken decades for the picture of interfacial ELA to become clear.
Electrode/organic interfaces appear to fall into three classifications: (1) chemically reactive/strongly interacting interfaces, (2) moderately interacting interfaces and (3) nonreactive/weakly interacting interfaces. One cannot draw a distinct dividing line that separates one class from another, but rather the classes likely span a continual range from strong chemical interactions to weak chemical interactions. Yet, there are some features that distinguish the three classes; in particular, their ELA behavior.
Chemically reactive or strongly interacting interfaces give rise to either breaking and reforming of chemical bonds in the organic or the formation of localized chemical bonds by strong hybridization between electrode surface electronic states and molecular orbitals (MOs).130, 131, 132, 133, 134, 135, 136 There are numerous examples from adsorption studies that demonstrate interfaces in which hybridization between adsorbate and substrate electronic states gives rise to distinct interface states. Work done between the 1970s and present day has provided many examples of such interfaces, involving small organic molecules on metals,131, 132, 134, 136, 137, 138, 139, 140, 141, 142, 143, 144, 145, 146, 147, 148, 149, 150 noble gas atoms on metals,151, 152, 153, 154, 155, 156, 157 small inorganic molecules (such as CO,158, 159, 160, 161, 162, 163, 164 NO165 and H2O166, 167) on metals and oxides,160, 161 and various organic semiconductors on metals and inorganic semiconductors.131, 132, 134, 136, 139, 140, 145, 146, 147, 148, 149, 150 These interfaces usually involve reactive metals, or planar molecules that can come in very close contact with metal electrodes. The ELA behavior of these interfaces is complex, involving many considerations such as molecular adsorption geometry and the overlap integrals between molecule and substrate electron wave functions. No simple relationship is known that can generalize the ELA behavior at such interfaces.
Moderately interacting interfaces also involve hybridization between substrate and molecular wave functions, except the hybridization gives rise to interface states and broadening of MOs, rather than localized chemical bonds.127, 128, 168, 169, 170, 171, 172 These types of interfaces are common for nonreactive metal electrodes, and can result in a wide range of interaction strengths. This type of interface has been thoroughly examined both theoretically and experimentally. ELA behavior is governed by both electrode work function and interaction strength.
Nonreactive or weakly interacting interfaces have essentially no hybridization between the electrode bands and the organic orbitals. Consequently, there are no localized bonds and likely also no gap states at these interfaces. ELA behavior in these cases is mainly governed by electrode work function and organic donor/acceptor levels.173, 174
Many metal-oxide/organic interfaces are weakly interacting interfaces.174 Weakly interacting interfaces give rise to perhaps the simplest ELA trend, which is illustrated in Figure 2b. The blue dashed line represents the electron-injection barrier (Δe) and the orange line represents the hole-injection barrier, according to Figure 2a. The horizontal axis in Figure 2b is electrode work function. Figure 2c shows experimental measurements of the trend.
The trend shows that, within a certain range, the hole-injection and electron-injection barriers are linearly dependent on an electrode’s work function. This linear region is referred to as the ‘vacuum-level alignment’ regime (although the vacuum levels of electrodes and organics do not always align perfectly here). In this region, increasing an electrode’s work function decreases the hole-injection barrier and increases the electron-injection barrier. Conversely, decreasing an electrode’s work function will increase the hole-injection barrier and decrease the electron-injection barrier.
The linear relationship between HOMO binding energy and electrode work function occurs because the surface potential of the electrode is proportional to the work function. In the absence of charge transfer, the position of an adsorbed molecule’s frontier orbitals relative to the Fermi level depends on the electrode’s surface potential.
If the electrode’s work function exceeds a certain threshold value—a value that depends on the organic molecule—then the HOMO level becomes ‘pinned’ to the Fermi level. Note that ‘pinning’ means that the alignment between the HOMO and the Fermi level stays constant with further increases in electrode work function. Conversely, if an electrode’s work function is lower than another threshold value, the Fermi level becomes ‘pinned’ to the LUMO level, and the alignment between the Fermi and LUMO level does not change with further decreases in electrode work function.
The onset of pinning is believed to occur as a result of molecular ionization at the electrode/organic interface and capacitive effects in the electrode.173, 174, 175 Because of coupling between the molecular ionization processes and the electrode’s Fermi energy, ionized molecules become thermodynamically stable at the electrode surface once the Fermi level crosses the threshold to the ‘pinning’ regime. The electric potential—caused by the combined effects of ionized molecules at the interface and capacitive charge redistribution in the substrate—counteracts the surface potential that is related to work function.174, 175
This ELA trend was first observed by Tengstedt et al.173 using polymer/polymer interfaces. The trend has now been confirmed by several other groups, using both photoemission spectroscopy and Kelvin probe methods.174, 176, 177, 178, 179 Greiner et al.174 demonstrated that the trend also holds for small-molecule organic semiconductors on a wide range of transition metal oxides.
As mentioned earlier, the threshold values that govern the onset of pinning depend on the characteristics of the organic molecule. Although Tengstedt et al.’s173 study showed that the threshold to pinning occurs when the electrode’s work function is greater than the polymer’s positive polaronic level and less than its negative polaronic level, Greiner et al.’s study found that the threshold to pinning occurs when the electrode’s work function exceeds the organic molecule’s ionization energy and electron affinity. The discrepancy may be because Tengstedt et al.’s study used solution-cast conducting polymers, whereas Greiner’s study used vapor-deposited small-molecule organic semiconductors.
Polaronic levels are related to ionization energy and electron affinity, but polaronic levels contain an additional energy term that results from the electron-density distortions that occur when highly polarizable molecules become charged.173 The positive polaronic level represents the sum of the polymer’s ionization energy and the relaxation energy caused by molecular polarization. Likewise, the negative polaronic level represents the sum of the electron affinity and a relaxation energy.
Thus, it appears that for large and highly polarizable polymeric molecules, in which relaxation effects are large, one must consider the polaronic levels for the pinning thresholds. Although for small molecular semiconductors, in which polarization effects are considerably smaller, the relaxation term can be neglected and one needs to only consider a molecule’s ionization energy/electron affinity to determine the pinning thresholds.
Experimentally, the pinning trend has been shown very extensively for the hole-injection side of the plot, as shown in Figure 2c by measuring the HOMO level of organics on high-work-function electrodes using photoemission spectroscopy. The low-work-function end of the plot has had less experimental confirmation, likely due to the scarcity of materials with low-enough work function to pin the LUMO levels of common organic semiconductors, while simultaneously being nonreactive. Furthermore, occupied levels are more straightforward to measure than unoccupied levels. Ultraviolet photoemission spectroscopy is commonly used to measure the HOMO level. To date, there have been no studies that use inverse photoemission to observe the pinning trend by measuring the LUMO level.
Implications of ELA behavior
The ELA behavior of weakly interacting interfaces has important implications for organic device design. For instance in OLEDs and OTFTs, when choosing an electrode material (or buffer layer) to give an Ohmic hole-injection contact between the anode and a given organic semiconductor, one must ensure that the electrode’s work function is greater than the organic’s ionization energy/positive polaronic level. Conversely, when choosing an appropriate cathode material to have an Ohmic electron-injection contact, one must ensure that the cathode’s work function is lower than the organic’s electron affinity/negative polaronic level.
In designing OPVs, the ELA trend has implications not only for contact resistance but also for maximizing open-circuit voltage (VOC). The maximum VOC that an organic solar cell can achieve depends on the offset between a donor molecule’s HOMO and an acceptor molecule’s LUMO.6 However, the maximum VOC can only be achieved by appropriately tuning the ELA at the electrode/organic interfaces.
As shown in Figure 3, the maximum VOC is achieved by tuning the electrode work functions, such that the donor’s HOMO level and acceptor’s LUMO level are pinned to their respective electrodes. If this is the case, the maximum VOC will depend on the energy offset between the donor’s HOMO level and the acceptor’s LUMO level. However, if HOMO and LUMO levels are not pinned to their respective electrodes, then the VOC will be less than ideal and will scale with the electrode work-function difference.
General electronic structure of metal oxides
Although transition metal oxides have been found to follow a general ELA behavior, their diverse set of electronic structures affects their conductivity properties. Transition metal oxides can be dielectric insulators, defective semiconductors (p- and n-type), Mott–Hubbard insulators and metallic conductors. These properties are established from a combination geometrical, quantum chemical and electrostatic characteristics. For example, crystal symmetry, metal-oxygen bond length, valence electron population, degree of ionic or covalent bond character and electron correlation effects, all influence a metal oxide’s electronic properties. Although a quantitatively accurate description of an oxide’s electronic structure often requires most of these factors to be considered, many of the qualitative features can be understood from rather simple models—such as crystal field theory or ligand field theory—and by simply considering d-band occupancy.180
In crystal field theory, one treats oxygen atoms as negative point charges. Conceptually, these point charges are positioned in a particular geometry around a metal atom, as illustrated in Figure 4 for the octahedral case. One then considers how the electric field—which is formed by the negative point charges—affects the energy of the metal atom’s d electrons. Although a metal atom’s d orbitals are degenerate when they are surrounded by a spherically symmetric electric field (or zero electric field), they lose their degeneracy when surrounded by an electric field of lower symmetry than a sphere.
In crystal field theory (that is, in the ionic approximation), oxides are treated as though the metal atom has transferred all of its valence electrons to the oxygen atom. Thus, the oxygen atom is treated as an O2− ion and the metal as an Mx+ ion, where x is the formal oxidation state of the transition metal. This model represents the hypothetical scenario where there is zero hybridization between O 2p and metal d orbitals.
In most metal oxides, the oxygen anions are arranged in an octahedral or tetrahedral geometry around the metal cation. In an electric field of octahedral symmetry, two of the five d orbitals are destabilized (pushed up in energy) and the other three d orbitals are stabilized (pulled down in energy), as illustrated in Figure 4. This splitting of d-orbital energies creates an energy gap. The two orbitals that are destabilized are assigned the point-symmetry label eg, and the three stabilized orbitals are assigned the point-symmetry label t2g.
In contrast to the ionic approach of crystal field theory, ligand field theory is a MO approach, in which oxide energy levels are calculated from the linear combinations of atomic orbitals—mainly the metal d and oxygen 2p orbitals. For octahedrally and tetrahedrally coordinated metals, the computed MOs from ligand field theory yield similar structures as crystal field theory—that is, the d orbitals are split into MO’s of eg and t2g symmetry. An example of the electronic structure of TiO2, from MO overlap calculations, is shown in Figure 5.
The ligand field picture is often an adequate description of oxides—except when electron correlation effects are strong, in which case coulomb repulsion between electrons must be considered.
In extended solids, the energy levels from ligand field theory are broadened into bands in the same way that atomic orbitals of metals and semiconductors are broadened into bands in solids. Both O 2p states and metal d states contribute to the total density of states (DOS). Overlap integrals between oxygen 2p states and metal d states are usually nonzero, thus bands generally consist of a hybridized mixture of oxygen and metal states.
The total DOS can be divided into projected DOS plots, which show what portion of the total DOS is contributed from O 2p states and metal d states, as shown for anatase TiO2 in Figure 5b. Often a certain band can be said to be majority O 2p character, or majority metal d character, giving rise to the labeling of the O 2p band or metal d band. In the example of anatase TiO2, one can see that the occupied valence band is majority oxygen 2p character, and the unoccupied conduction band is majority Ti 3d character.
Although the finer details of transition metal-oxide electronic structures require computation, some of the most important qualitative features can be understood from the above-described models and considerations of the d-band occupancy.34 Figure 6 shows some transition metal-oxide valence spectra, which have been grouped into classes according to their d occupancy. The top row of the Figure 6 presents each class’s schematic energy-level diagram, and the bottom row presents their valence photoemission spectra. For simplicity, the different cation coordination geometries are not distinguished, but it is sufficient to say that, whatever the anion geometry, there is an energy gap in the d band.
The class 1 oxides have totally empty d bands (d0 oxides). When completely stoichiometric, these oxides are insulators. However, they have a natural tendency to form oxygen vacancy defects, and consequently they are n-type materials.34, 40 The bottom of their conduction bands are composed primarily of empty metal d states, and valence-band maxima are composed primarily of O 2p states, as shown in Figure 6 (i). Examples of these oxides are: MoO3, TiO2, HfO2, WO3, ZrO2, Ta2O5, V2O5 and CrO3.
A subset of the class 1 oxides is the oxygen-deficient d0 oxides. With high a degree of oxygen deficiency, a significantly high density of occupied states form within the band gap. These defect states arise from the filling of empty metal d states, and can be seen in the valence spectra of Figure 6 (ii). As a result of the small energy gap between the defect states and the conduction band minima, these oxides tend to be n-type semiconductors.
The class 2 oxides are oxides whose d bands are partially occupied, but with a low number of electrons (for example, d1, d2 and d3). These oxides tend to form when d0 oxides are chemically reduced. They are often metallic, as evident by the finite DOS at the Fermi level in the valence spectra level in Figure 6 (iii).
The oxides whose d bands are partially occupied with a high number of electrons (for example, d7, d8 and d9) constitute class 3 oxides. These oxides represent a very important class of materials, called Mott–Hubbard or charge-transfer insulators. Their electronic properties are dominated by electron–electron correlations. The valence photoemission spectra of these oxides are not as simple to interpret as the d0 oxides, because there is often a significant amount of hybridization between metal d and oxygen p states, thus one cannot easily divide the valence DOS into metal d regions and oxygen p regions. Furthermore, the strong electron correlation gives rise to several final-state photoemission features. Nonetheless, the valence photoemission spectra of the class 3 oxides share similar qualitative features, as seen in Figure 6 (iv).
Because of the strong electron correlation, the electronic properties of these oxides are not correctly predicted using the simple independent-electron model that is often used to describe band structures of solids. According to the independent-electron description, class 3 oxides should have a partially filled d band and should therefore be metallic conductors. Contrary to this prediction, these oxides are electrical insulators. The electrical conductivity of these oxides can be explained by considering on-site Coulomb repulsion and electron exchange interactions, in the models developed by Mott183 and Hubbard.184, 185, 186
In the Mott–Hubbard model, d electrons are localized on metal cations because there exists a strong repulsion energy between electrons in narrow d bands.187 In this model, conduction is envisioned as d electrons hopping from one metal site to another (that is, din djn→din−1 djn+1, where the i and j indices indicate different metal sites). Coulomb repulsion and exchange interactions between electrons introduce an energetic penalty to placing two d electrons on the same site.
A material is metallic if there exists vacant states at an energy infinitesimally higher than the highest-occupied state. The Coulomb repulsion energy increases the energy of the lowest unoccupied state, such that it no longer is infinitesimally higher in energy than the highest-occupied state. In the band picture, this scenario can be viewed as the formation of an energy gap in the d band, as illustrated in Figure 7. The splitting of the d band gives rise to the so-called lower Hubbard band and the upper Hubbard band. The bands are separated by the Hubbard parameter (U).
Strong electron correlation can also give rise to so-called ‘charge-transfer’ insulators.188 In these materials, the lowest-energy excitation is not a d–d excitation, but rather a transition from a ligand site to a metal site (that is, din Lm→din+1 Lm−1, where L indicates a ligand, or in the case of oxides, oxygen). The energy required to excite an electron from the highest-occupied oxygen state to the lowest unoccupied metal d state is represented by the charge-transfer term, Δ. If the Hubbard term (U) is much greater than the charge-transfer term (Δ), as illustrated in Figure 7b, then the material is described as a charge-transfer insulator, rather than a Mott–Hubbard. The oxides NiO, CuO and CoO are believed to be charge-transfer insulators. Although electron correlation has a strong influence on the bulk electrical conductivity properties of these metal oxides, it is not yet clear to what degree electron correlation affects the charge-injection characteristics at metal-oxide/organic interfaces.
The final class of oxides discussed here (class 4) are the oxides with completely filled d bands (d10 oxides). They tend to be semiconductors owing to the gap between the d band and the next-highest energy band (usually derived from metal s orbitals). These oxides tend to behave as intrinsic p-type semiconductors, where the Fermi level resides closer to the valence band than the conduction band; however, the hole mobility for these materials is still rather low. The reason for the p-type nature of these oxides is commonly accepted to be due to the presence of cation vacancy defects.189, 190
Fermi-level position and importance of band structure
Hypothetically, the Fermi level of a perfectly stoichiometric semiconducting oxide would sit at midway between the valence-band maximum and the conduction band minimum. Realistically, a perfectly stoichiometric oxide (that is, an oxide without any defects) cannot exist, as entropy requires that there will always be some finite concentration of defects.
The common defects in oxides are oxygen vacancies (vO) and metal vacancies (vM), although other defects are also possible, such as metal or oxygen interstitials, an oxygen ion on a metal site and a metal ion on an oxygen site. In general, all of these defects give rise to either over-coordinated or under-coordinated metal centers, and result in new occupied or unoccupied states near the conduction band or valence-band edges. These defect states make an oxide behave as either a p- or n-type semiconductor.
Using the simplified ionic picture, one can say that coordination defects result in metal oxidation-state defects (that is, metal centers where the metal’s oxidation state differs from the value it would have in the stoichiometric oxide). An oxygen vacancy would give rise to metal cations with an extra electron. The extra electrons occupy states close to the conduction band minimum, and thus can act as n-type dopants. Conversely, a cation vacancy would result in unoccupied states close to the valence-band maximum, and can act as p-type dopants. In general, oxygen deficiency (or excess metal cations) makes an oxide behave as n-type, whereas metal deficiency (or excess oxygen) makes an oxide behave as p-type. Note that the actual position of a given occupied or unoccupied defect state, relative to the conduction and valence bands, differs from material to material, and in some oxides these states can act as traps.
Some metal oxides are described as ‘intrinsically’ p-type or ‘intrinsically’ n-type. This is simply because the formation energies of each type of defect are not equal.191 For most oxides, under normal conditions (that is, standard atmosphere, temperature and pressure), a given type of defect will tend to dominate. For instance, the most stable defect in MoO3 is the oxygen vacancy, and thus MoO3 will intrinsically behave as an n-type semiconductor. Conversely, the most stable defect in Cu2O is the Cu vacancy, and so intrinsically Cu2O behaves as a p-type semiconductor.192 In some oxides, the formation energies of various defects are similar in magnitude, so the oxide can change its behavior from p-type to n-type depending on the surrounding oxygen chemical potential.193, 194, 195 This behavior is rare, but is known to occur in the case of UO2.193, 194, 195
An oxide’s electronic structure is important to its use as a buffer layer. An oxide’s charge-injection properties in a device will depend on whether the oxide is p- or n-type, wide or narrow band gap, or a metallic conductor. Schematic energy-level diagrams of various transition metal oxides and several common organic semiconductors are shown in Figure 8.
As many of the oxides—due to intrinsic defects—are p- or n-type semiconductors, it is possible for certain oxides to be used as selective charge-injection layers. A selective charge-injection layer decreases the injection barrier for only one type of carrier—a property that is particularly important for OPVs, in which nonselective contacts result in high leakage currents.196
There are numerous reports of transition metal oxide buffer layers in OPVs, where the oxide provides charge selectivity.80, 196, 197, 198, 199, 200, 201, 202, 203 It is believed that the charge selectivity is a result of the p- or n-type nature of a particular buffer layer. For instance, consider the p-type oxide anode buffer layer, illustrated in Figure 9b. The Fermi level is closer to the oxide’s valence band than its conduction band. For a high-work-function oxide, as would be the case for anode buffer layers, the Fermi level is also pinned to the HOMO level of the organic layer. Holes can easily hop through the buffer layer via the buffer layer’s valence band. However, if the oxide’s band gap is larger than the organic’s HOMO–LUMO gap, then there will be a barrier to overcome for any electrons trying to hop from the LUMO to the electrode.
The reverse is true for n-type oxides and cathode buffer layers. An n-type oxide has its conduction band close to the Fermi level. Furthermore, a low-work-function cathode has its Fermi level pinned to the LUMO level. Excited electrons in the LUMO will be able to move to the electrode via the buffer layer’s conduction band. However, if the buffer’s band gap is larger than the organic’s HOMO–LUMO gap, then holes will have a barrier to overcome to move from the HOMO level to the electrode.
Consequently, the optimal buffer layer for the cathode of an OPV would be a low-work-function, n-type semiconductor with a large band gap, and the optimal buffer layer for an anode in an OPV would be a high-work-function, p-type semiconductor with a large band gap.
Similar rectifying behavior is believed to occur in OLEDs, as illustrated in Figure 9a. If the cathode has a wide band-gap p-type oxide as the buffer layer, then electrons can hop from the cathode to the organic LUMO level by overcoming the electron-injection barrier. However, the movement of electrons in the reverse direction requires electrons to overcome a much larger barrier (from the organic LUMO to the oxide-conduction band).
Conversely, on the anode side, if a wide band-gap n-type oxide is used for the buffer layer, then there will be a small hole-injection barrier for holes moving from the anode to the organic HOMO level, and a large barrier for holes moving from the organic HOMO level to the oxide valence band. Similar behavior is expected for contacts in OFETs as illustrated in Figures 9c and d.
Dependence of oxide work function on oxidation states and defects
Given the role of work function in governing ELA, tuning work function is an important capability. However, a material’s work function can be difficult to control. Work function values for a given material can span over 1 eV. For instance, reported work function values for MoO3 range from 5.3 to 6.9 eV.32, 64, 92
The large variation in reported work-function values is because work function is very sensitive to a number of factors. Work function represents the sum of electron chemical potential and surface dipole. Factors such as surface roughness,204, 205 exposed crystal face,206 radiation exposure207, 208 and adsorbate coverage209 affect the surface dipole component, whereas electron chemical potential is affected by the chemical identity of a material, the presence of impurities and the stoichiometry of a material.106
Although there are many factors that can alter work function, it is possible to gain control over many of these factors to tune work function. Under certain preparation conditions, one can obtain reproducible work-function values for a given material. For instance, sublimation-deposited MoO3 is routinely reported to have a work function of ca. 6.8–6.9 eV.
A compilation of work-function values for various metals and metal oxides (prepared by in-situ metal oxidation) is provided in Table 1. The work-function values in Table 1 represent the average of the most thermodynamically stable crystal faces of each oxide, as the oxides represented here were polycrystalline and prepared by in-situ metal oxidation. The oxides were not exposed to air, so adsorbates likely have a minimal effect on the work-function values shown here. Furthermore, as the oxides were prepared via in-situ oxidation (and vacuum annealing in the case of reduced oxides), they should all consist of stable oxygen-terminated surfaces. Consequently, the magnitude of the surface dipole in the work-function values listed in Table 1 can be considered similar in magnitude. Thus, the values allow an approximate comparison of relative electron chemical potential values.
A plot of metal-oxide (and metal) work functions versus average cation oxidation state shows that reducing the cation oxidation state of an oxide tends to decrease its work function, as shown in Figure 10a. This is likely a consequence of a decrease in electron chemical potential as the oxide becomes reduced (that is, as oxygen is removed). The reason for the decrease in electron chemical potential is that a cation’s electronegativity decreases as its oxidation state decreases.210
Electronegativity is closely related with the concept of electron chemical potential (or Fermi level). In Mulliken’s definition, electronegativity represents the midway point between the ionization energy and electron affinity—that is, midgap, as shown in Figure 11a.211 Likewise, the Fermi level in undoped semiconductors is midgap, as shown in Figure 11b.212 Thus, there is a direct relationship between electronegativity and Fermi level.213
Figure 10b shows a plot of the midgap position for various oxides—as calculated using electronegativity—versus the experimental midgap position—as determined by UPS (ultraviolet photoemission spectroscopy) measurements and literature band gaps.
The midgap positions were calculated using the concept of group electronegativity. In a compound, the overall electronegativity (that is, the group electronegativity) can be calculated using the geometric mean of the electronegativity values of the individual components in the compound:213
Where χAB is the group electronegativity of compound AmBn, where m and n represent stoichiometric coefficients. χA and χB are the electronegativities of components A and B, respectively. The concept of group electronegativity is illustrated in an energy-level diagram in Figure 11c.
Metal oxides can exhibit a continual range of stoichiometries because they are prone to many different types of defect, such as oxygen vacancies, oxygen interstitials, cation vacancies and cation interstitials. Metal-oxide work functions can also be tuned over a continual range by changing the concentration of defects—removing oxygen tends to decrease the work function, whereas adding oxygen tends to increase the work function. Removal of oxygen through the formation of O vacancies results in cation centers with reduced oxidation states. As the concentration of reduced cations increases, an oxide’s group electronegativity, and subsequently its work function, decreases. An example of the effect of O-vacancy defects on an oxide’s work function is illustrated with MoO3 in Figure 12.
In Figure 12, one can see that the increase in O vacancies gives rise to a decrease in work function (as seen by the shift of the secondary electron cut-off in Figure 12b). The O 2p band also shifts to higher binding energy because the Fermi level moves closer to the conduction band as O-vacancy concentration increases (as seen in Figure 12c). Furthermore, as defect state appears within the band gap and increases in intensity as O-vacancy concentration increases (as seen in Figure 12d).
In the presence of defects or dopants, the Fermi level is no longer positioned midway between the conduction band and the valence band, but rather it is shifted away from midgap position towards one of the band edges (depending on whether the defect/dopant is n- or p-type). The electronegativity contribution to the Fermi level is an electrostatic argument that positions the valence and conduction bands relative to the vacuum level. The presence of dopants and defects can form additional occupied or unoccupied states within the band gap. These states alter the carrier concentrations (that is, holes or electrons in the valence band or conduction band, respectively) and consequently shift the Fermi level within the band gap. Thus, the Fermi-level position is the net result of electronegativity and carrier-concentration contributions.
As shown in Figure 12, oxygen vacancies in MoO3 give rise to an occupied donor state (seen at a binding energy of ca. 1 eV in Figure 12d). There is a logarithmic relationship between donor concentration and Fermi-level position.215 Consequently, there is a rapid initial decrease in work function as oxygen vacancies are introduced, as seen in Figure 12e. The linear decrease in work function that occurs at higher O-vacancy concentrations is a consequence of electronegativity.
As mentioned in an earlier section, metal oxides exhibit doping asymmetry,191 meaning some oxides are prone to forming one type of defect over another. Because of their native defects, many oxides tend to have either n- or p-type character. For instance, native O vacancies in oxides like MoO3, TiO2, WO3 and V2O5 make them ‘intrinsic’ n-type materials, whereas native O interstitials in oxides like NiO make them ‘intrinsic’ p-type semiconductors.
Based on these characteristics, one can develop strategies for tuning oxide properties for buffer layers. Decreasing an oxide’s work function by inducing O vacancies may be a useful strategy for obtaining low-work-function anode buffer layers, such as defective ZrO2. The opposite strategy (that is, inducing O interstitials) may be a useful strategy for obtaining high-work-function electrodes. Although, this may not work for MoO3, in which O interstitials are not stable, NiO supports O interstitials, and its work function has been reported to reach as high as 6.7 eV by treating it in atmospheres of high oxygen potential.216
Opportunities and challenges of metal oxides as ultrathin buffer layers
In general, oxide buffer layers are very thin (within a few nanometers) and must be in physical contact with a highly conductive electrode. The electrode is often a metal or transparent conducting oxide. The interface with the electrode may have a chemical interaction with the buffer layer that extends several nanometers from the electrode/buffer interface. These interactions can influence the buffer layer’s work function and electronic properties.
A number of studies have demonstrated the influence of oxide buffer-layer thickness on device performance.68, 69, 92, 217 In general, it is found that there is an optimal thickness for a buffer layer. If the buffer layer is too thin or too thick, then device performance suffers. The optimal thickness of MoO3 has been found to be in the range of 0.5–3 nm.
However, the optimal thickness of an oxide also depends on the nature of the electrode material. A number of studies have demonstrated chemical interactions between oxides and metal electrodes—within the first few nanometers of an interface—and also dependence of device performance on the electrode material.66, 70, 218, 219, 220, 221, 222
Chemically reactive interfaces can give rise to reduction of oxidation state in the oxide buffer layer near the electrode/buffer interface. For instance, MoO3 on metals with various reactivity gives rise to reduced MoO3 near the metal/metal-oxide interface, as illustrated in Figure 13.
If the magnitude of the first oxidation potential of the metal electrode is greater than the first reduction potential of the oxide buffer layer, then the metal electrode will sequester oxygen anions from the oxide buffer layer. Thereby, the metal becomes oxidized and the oxide reduced, within the first few nanometers of the electrode/buffer interface. The degree of oxidation/reduction is determined by the difference between the metal’s first oxidation potential and the oxide’s first reduction potential.
This results of such interfacial reactions causes changes to the oxide’s properties near the electrode interface, and a strong dependence of a buffer layer’s properties on its thickness. For instance, it has been demonstrated that interfacial reaction between MoO3 and various metal electrodes results in a decreased oxide work function and gap states close to the interface, as shown in Figure 14. Consequently, to ensure that an oxide buffer layer has the expected properties, one must ensure that there are no strong interfacial reaction at the electrode/buffer interface or at least account for the interfacial reaction zone.
The degree of MoO3 reduction and the thickness required before MoO3 reaches its bulk properties depend on the metal electrode. As shown here, the metals that have greater first oxidation potentials than the first reduction potential of MoO3 (that is, Ni, Mo and V) cause Mo6+ cations to be reduced to Mo5+ (and Mo4+ in the case of V) close to the metal/oxide interface. Copper is unique in that it forms an oxide alloy with MoO3. Interestingly, slight Mo6+ reduction is also observed at the Au/MoO3 interface; however, Au was not oxidized in the process. This suggests a charge-transfer interaction, possibly where Mo5+ cations are stabilized by screening from the Au Fermi level.
It has been shown on several occasions that organic ELA depends on buffer thickness.222, 223 Based on the observed correlation between interfacial oxide reduction and oxide thickness, it appears that too thin of an oxide does not provide sufficient work function for favorable ELA (only in the case of high-work-function hole-injection buffer layers), whereas too thick of an oxide becomes too insulating and causes a high-series resistance in a device. Thus, a clear understanding of interfacial reduction reaction will provide a rational guide to process engineers to select best suitable electrode/oxide structures for a targeted application.
There are many types of buffer-layer materials that can be used in organic electronic devices. Among the most versatile are transition metal oxides. These materials can be used in OLEDs, OPVs and OTFTs as both electron-injection and hole-injection contacts. Because of the weakly interacting nature of the metal-oxide/organic semiconductor interface, such interfaces follow a general ELA trend, in which hole-injection and electron-injection barriers are governed by an organic molecule’s HOMO/LUMO levels and an electrode’s work function. Transition metal oxides exhibit a wide range of work functions that can be altered by changing the concentration of defects and the cation oxidation states. Generally, decreasing the cation oxidation state gives a decrease in work function, due to the lower electronegativity of low-oxidation-state cations. Defects and changes to oxidation state also result in changes to an oxide’s electronic structure. An oxide’s electronic structure can influence the rectifying character of a buffer layer. Such layers can be designed such that they allow injection of one type of charge charier in one direction, but suppress movement of charge in the opposite direction. Although such buffer layers can be very useful, one must be mindful of the contact between the buffer layer and the electrode. Interfacial oxidation/reduction reactions can give rise to changes in an oxide buffer layer’s stoichiometry, electronic structure and work function nearby electrode/oxide interfaces. These changes can affect the oxide buffer layer’s ability to provide ELA and charge-selective contacts.
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Greiner, M., Lu, ZH. Thin-film metal oxides in organic semiconductor devices: their electronic structures, work functions and interfaces. NPG Asia Mater 5, e55 (2013). https://doi.org/10.1038/am.2013.29
- charge-injection layers
- metal oxides
- organic electronics
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