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Van Der Waals Heterostructures between Small Organic Molecules and Layered Substrates

Han Huang

^1,2,*,

Yingbao Huang

¹,

Shitan Wang

¹,

Menglong Zhu

¹,

Haipeng Xie

¹,

Lei Zhang

³,

Xiaoming Zheng

¹,

Qiliang Xie

¹,

Dongmei Niu

¹ and

Yongli Gao

^1,2,4,*

Hunan Key Laboratory of Super-microstructure and Ultrafast Process, School of Physics and Electronics, Central South University, Changsha 410083, China

State Key Laboratory of Powder Metallurgy, Central South University, Changsha 410083, China

Department of Physics, National University of Singapore, 2 Science Drive 3, Singapore 117542, Singapore

⁴

Department of Physics and Astronomy, University of Rochester, Rochester, NY 14627, USA

Authors to whom correspondence should be addressed.

Crystals 2016, 6(9), 113; https://doi.org/10.3390/cryst6090113

Submission received: 16 July 2016 / Revised: 27 August 2016 / Accepted: 30 August 2016 / Published: 9 September 2016

(This article belongs to the Special Issue Two-Dimensional Materials beyond Graphene and their Van der Waals Heterostructures)

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Abstract

Two dimensional atomic crystals, like grapheme (G) and molybdenum disulfide (MoS₂), exhibit great interest in electronic and optoelectronic applications. The excellent physical properties, such as transparency, semiconductivity, and flexibility, make them compatible with current organic electronics. Here, we review recent progress in the understanding of the interfaces of van der Waals (vdW) heterostructures between small organic molecules (pentacene, copper phthalocyanine (CuPc), perylene-3,4,9,10-tetracarboxylic dianhydride (PTCDA), and dioctylbenzothienobenzothiophene (C₈-BTBT)) and layered substrates (G, MoS₂ and hexagonal boron nitride (h-BN)). The influences of the underlying layered substrates on the molecular arrangement, electronic and vibrational properties will be addressed.

Keywords:

interface; self-assembly; growth behavior; vdW heterostructures; 2D organics; SPM; OFET; capping layer

Graphical Abstract

1. Introduction

Organic (opto-)electronics are attracting tremendous attention for their mechanical flexibility, light weight, low cost, and available large scale production in organic light emitting diodes (OLEDs), organic photovoltaics (OPVs), and organic field effect transistors (OFETs) [1,2,3,4,5]. The quality of organic semiconductor thin films is one of the key components for a better device performance. Figure 1a–d shows the molecular structures of four air-stable candidates for organic electronics, pentacene, copper phthalocyanine (CuPc), perylene-3,4,9,10-tetracarboxylic dianhydride (PTCDA) and dioctylbenzothienobenzothiophene (C₈-BTBT), respectively. The anisotropic structures suggest orientation-dependent electronic properties. For example, pentacene possesses a relatively higher mobility in its b-c plane than a-b plane, as shown in Figure 1e [6,7]. Thus, various substrates, metals [8,9,10], native oxide silica [11,12,13,14], and layered materials [6,7,15,16,17,18], have been chosen for the growth of high quality thin films. In order to optimize the devices performance, it is essential to clarify how the interactions between molecules and substrates affect the growth of organic thin films.

The two dimensional (2D) derivatives of layered materials, such as single- or few-layered (SL, FL) molybdenum disulfide (MoS₂), hexagonal boron nitride (h-BN), and graphene (G), whose structures are schematically shown in Figure 1f and exhibiting an atomically flat surfaces without dangling bonds, are thought to be perfect candidates to fundamental researches and practical applications. G has the advantages such as very high charge carrier mobility, good flexibility, and transparency to be used as a transparent electrode substituting indium−tin oxide (ITO) [19,20]. h-BN is an insulating isomorph of G with covalent bonding boron and nitrogen atoms occupying the inequivalent positions, possessing a low dielectric constant. MoS₂ is composed by one layer of Mo atoms stacked between two sulfide layers and used as channel materials in FETs because of its high on/off ratio, low sub-threshold swing value, and good carrier mobility [21,22,23,24]. G, MoS₂, and h-BN are all chemically inert, avoiding bonding strongly when integrating with different dimensional crystals at the interface and leading to 2D-2D and 0D-2D (organic molecules-2D) van der Waals (vdW) heterostructures [25,26,27]. For example, MoS₂-G vdW heterostructure shows that close to the Fermi level, no significant charge transfer doping is detected from MoS₂ to G [28,29]. Besides, organic molecules are able to grow into well-ordered thin film with a high degree of crystallinity on 2D substrates and form vdW heterostructures. Such vdW heterostructures possess potential applications in FET devices [30]. Moreover, the excellent physical properties, such as transparency and flexibility, make them compatible with current organic (opto-)electronics.

This review consists of following six sections: I tuning the orientation of pentacene, II pentacene on layered substrates, III CuPc on layered substrates, IV C₈-BTBT on layered substrates, V PTCDA on layered substrates, and VI conclusions.

2. Tuning the Orientation of Pentacene

As a well-known gate dielectric, SiO₂ is one of most usual substrates to study the properties of thin films of small organic molecules, for example, pentacene. The AFM image in Figure 2a shows the typical morphological features of ~3 ML (ML, monolayer, a full layer of molecules in the standing-up configuration) pentacene thin films on SiO₂ [12]. Such films are composed by dendritic grains with flat surfaces and well-ordered crystalline structures in size of few micrometers, indicating a kinetics-limited Volmer-Weber growth mode [31,32]. The corresponding inset shows the nucleation and extension of pentacene in the first monolayer into dendritic grains, indicating presence of plenty of grain boundaries in thicker films. The average step height of ~1.5 nm, close to the length of one pentacene molecule, suggests that pentacene molecules always stand up on SiO₂ (molecular a-b plane parallel to the substrate surface) as shown in Figure 2d, which can be attributed to the relatively weak interfacial interaction between pentacene and SiO₂. Consequently, the charge carriers in such pentacene thin films prefer to lateral transport along the overlapped π orbitals with high mobilities up to 5 cm²/Vs [33]. However, the existed plenty of grain boundaries may scatter the charge carriers and reduce the mobilities. Given that molecule-substrate and molecule-molecule interactions predominantly determine the film structures, so as to enhance the device’s performance, an adequate substrate is urgently required to ensure higher-crystalline pentacene thin films.

STM image in Figure 2b shows that Bi(001) is covered by an ordered single layer pentacene entirely and a second layer partially (with brighter contrast) [8]. The pentacene layer grows in a step flow mode, like h-BN grown on Ru(0001) [34], which can effectively reduce the grain boundaries and result the first layer pentacene in grains with a larger size exceeding 200 μm in diameter. The inserted molecularly-resolved STM image shows aligned spots. Each of them corresponds to a single standing-up pentacene molecule, indicating the pentacene molecular a-b plane parallel to Bi(001), as show in Figure 2e. Angle Resolved Photoemission Spectroscopy (ARPES) measurements demonstrate a higher highest occupied molecular orbital (HOMO) dispersion and more delocalized charge carriers than theoretical calculations along three high symmetrical directions (

\bar{Γ} - \bar{M}

\bar{Γ} - \bar{Y}

and

\bar{Γ} - \bar{X}

), which means a larger overlap of π-orbitals and higher carrier mobilties [9]. The results indicate the Bi(001) indeed improved the crystallinity of pentacene films and induced higher mobility.

HOPG is a famous inert substrate for surface science researches. The AFM image in Figure 2c shows the morphology of ~12 nm thick pentacene films on HOPG, which is characterized by large block-like ordered crystals with deep trenches [6]. On the contrary to above two cases, the long axes of pentacene molecules are parallel to the substrate surface according to X-ray diffraction results. Such a lying-down arrangement, as schematically shown in Figure 2f, can be attributed to the improved interfacial π-π interactions due to the epitaxial growth of pentacene on HOPG. The rather weak adsorption energy of the molecules on graphite enables a slight tilting of the molecules at the interface and thus allows the formation of crystalline multilayer films by suppressing any strain due to lattice mismatch between the molecular film and the substrate [35]. The films are possibly in orthorhombic polymorph and possess fiber textures with (100) as the fiber long axis along the surface normal. Thus, they have high enough crystallinity to show a HOMO-derived band dispersion of ~190 meV at room temperature, which is absent for pentacene grown on SiO₂ [6]. The results indicate that layered substrates like HOPG and MoS₂, moreover, their single- or few- layered derivatives like G and MoS₂, may improve the crystallinity of thin films of small organic molecules.

3. Pentacene on Layered Substrates

In terms of devices, G is an ideal electrode material due to its outstanding conductivity, flexibility, and transparency. Conductive and transparent monolayer G can be used as a template to tune pentacene molecular orientation from standing-up to lying-down in well-defined films [15,36]. The AFM image in Figure 3a shows that the morphology of 50 nm thick pentacene films on CVD-G-covered and bare SiO₂ has an abrupt change cross the boundary, which revealed remarkable differences in growth and the modulation effect of substrates. Pentacene films on G (left-hand side) show a highly ordered block-like crystals with deep trenches texture, similar to on HOPG, while on SiO₂ (right-hand side) are in typical polycrystalline grains [15]. They differ greatly in crystallinity, grain size, and orientation. Both the angle-dependent near-edge X-ray absorption fine structure (NEXAFS) and two-dimensional grazing incidence X-Ray diffraction (2D GIXRD) measurements corroborate that pentacene molecules in the first layer are in a lying-down orientation, while slightly tilted relative to the G plane in subsequent layers, as depicted in Figure 3d. It is ascribed to that the interfacial π-π interaction is reduced when pentacene grows into several layers [15]. It is well adapted to the cases of pentacene on G-covered glass [36] and perfluoropentacene on G-covered quartz [37]. It’s also important to mention that polymer residues remaining on G surfaces induce a stand-up orientation of pentacene [15]. The Fe film morphology was influenced by substrate surface defects [38]. Considering this reason, there can be a distinct structure and orientation of pentacene film if the substrate surface exhibits defects or becomes rough, because the template effect is no longer operative. In that case, molecules adsorb in an upright orientation and continue to grow as (001) oriented films. Thus, it is a crucial factor which avoids surface defects and roughness when utilizing template-guided molecular film growth [35]. The particular interaction between G and small molecules [39] is used to govern both the thin film morphology and electronic characteristics of pentacene films.

The AFM image in Figure 3b displays the morphology of 40 nm thick pentacene on SiO₂ covered with/without mechanically exfoliated 2L MoS₂ (blue/red dash block) [40]. On the MoS₂ side, pentacene, perhaps in a lying-down configuration (Figure 3e), is more compact and homogeneous but in smaller grains. The abrupt change in the pentacene film grain size coincides with the boundary with the underlying MoS₂.

The AFM image in Figure 3c shows the well-defined crystal facets of ~2 ML pentacene grown on mechanically-exfoliated h-BN [7], indicating that pentacene is highly-crystalline and grows in a layer-by-layer mode with obvious difference in the first three layers. The average thickness of the wetting layer (WL), the first (1L), and the second conducting layer (2L) are 0.5, 1.14, and 1.58 nm, respectively. The subsequent layers have the same height and molecular packing as 2L. The thickness of WL approximates the length of pentacene molecule along b-axis (0.606 nm), and far less than that along c-axis (1.601 nm) [12], which indicates the molecules adopt the lying-down configuration. In addition, the thickness of 2L is consistent with the (001) plane spacing of thin film phase (1.45 nm). However, 1L is clearly in a new polymorph which slightly differs with 2L. The transitional height implies more tilted molecular packing compared to 2L, as schematically illustrated in Figure 3f. The molecular packing is very different with on G and MoS₂.

Figure 3g–i shows the transfer characteristics of pentacene based OFETs with G, MoS₂ and h-BN as function layers, respectively. Figure 3g demonstrates transfer characteristics of lateral FETs using monolayer G with/without PMMA residues (black/red curve) as electrodes. The devices with/without PMMA residues show an average field-effect mobility of 1.2/0.4 cm²/Vs and a comparable current on-off ratio of 10⁸. The poorer field-effect mobility is due to the orientation of the pentacene long axis parallel to the substrate plane on clean G. That is, the π conjugate direction is normal to electron transport direction of planar FET devices.

Figure 3h displays the transfer characteristics of a MoS₂ FET (blue), a pentacene FET (red), and a type II p-n heterojunction based on pentacene/MoS₂ (green), respectively [40]. The gate-tunable asymmetric antiambipolar transfer characteristic of pentacene/MoS₂ heterojuntion is different than the symmetric one with a MoS₂−WSe₂ p-n heterojunctions [41,42], suggesting harnessing to achieve simultaneous phase [43] and amplitude [44] shift-keying for wireless telecommunication technologies. In addition, this heterojunction exhibits a photovoltaic effect but poor power conversion efficiencies of ~0.004% @ 625 nm, Performance of FET devices is unsatisfied because of a low on/off ratio and mobility. It seems that the reduced carrier diffusion length results from charge carrier scattering and trapping due to smaller grain size. Hence, the crystalline of pentacene on MoS2 continue to be a primary issue for application.

Figure 3i shows the temperature dependent transfer characteristics of a 2L pentacene/h-BN based FET [7]. The extracted field effect mobility is about 3 and 5.2 cm²/Vs at room- and low-temperature (110 K), respectively, far surpassing devices based on pentacene polycrystalline thin films at similar temperatures. On the contrary to the bandlike transport of 2L devices, the WL devices exhibit no conduction due to the absence of intralayer π-π stacking, and the 1L devices display characteristic of 2D hopping transport mode. In 2L, a sufficient extended density of states along a-b plane caused by the π orbital laterally-overlapping leads to bandlike transport for planar FETs. In 1L, a more tilted molecular orientation results in disconnected bonding and localization in both directions. The strong modulation demonstrates that h-BN is an excellent candidate for an insert layer which enables the conversion of molecules’ arrangement by vdW interactions.

4. CuPc on Layered Substrates

The modulation of layered substrates on the growth of CuPc are also interesting. Figure 4a,b show the AFM topography images CuPc on glass covered with/without CVD-grown G [45]. On bare glass, elongated CuPc grains, 94 ± 34 nm long and 35 ± 6 nm wide, are observed with a root mean squared film roughness of 2.0 nm, and similar to previous AFM observations of standing up oriented CuPc [46,47].Round CuPc grains are observed on a few layers of G (FLG) with a greater roughness of 4.2 nm. The 2D-GIXRD pattern in Figure 4d for CuPc on bare glass only shows one single sharp peak concentrated on the meridian (q_xy = 0), implying that CuPc molecules are oriented perpendicularly to the surface of the glass substrate, similarly on Si [48]. On the contrary, the pattern in Figure 4e shows multiple new diffraction points for CuPc on FLG-covered glass. Furthermore, it is not dispersed much, indicating that CuPc molecules are well oriented on G-covered glass [49]. Thus, CuPc adopts a near face-on orientation with the molecular plane tilted on average 9° with respect to the substrate. The continued appearance of the (100) reflection along the meridian indicates that there are still some crystallites adopt the edge-on configuration in the film [48]. Conductive atomic force microscopy (C-AFM) measurements show that at a single-grain level CuPc on (G covered) PEDOT:PSS/ITO presents a hole mobility of (1.9 ± 0.2) × 10⁻³ ((1.6 ± 0.2) × 10⁻²) cm²/Vs. G-templated CuPc thin films exhibit an order of magnitude higher out-of plane hole mobility relative to untemplated thin films. Whether the G coating affects the charge injection requires further research.

The AFM image in Figure 4c presents the 1D nanorod-like structure of 4.8 nm thick CuPc on bulk MoS₂(0001) [50]. The corresponding 2D-GIXRD pattern in Figure 4f proves a good crystallization, as well as a standing-up orientation. It should be noted that this study was carried out in ambient conditions. In situ LEED patterns illustrate that CuPc molecules assemble into large domains at a thickness of 4.8 nm with the molecular plane (quasi-)parallel to the MoS₂(0001) substrate [51]. Thus, MoS₂ may have different effect on CuPc growth compared with G. Furthermore, photodetectors based on the vdW heterostructure of 2 nm-thick p-type CuPc/5L n-type MoS₂ presents the highest performance with a photoresponsivity of ~1.98 A/W, a detectivity of ~6.11 × 10¹⁰ Jones, and an external quantum efficiency of ~12.57%, due to the transfer of photo-generated charge carrier form CuPc to MoS₂ and the CuPc layer thickness-dependent interlayer recombination processes across the CuPc/MoS₂ interface [52].

Raman spectroscopy is an effective and non-destructive method at ambient conditions to determine surface characterization. Figure 5a demonstrates the spatially-averaged Raman spectra for a 50 nm thick pentacene film on glass covered with/without a monolayer of G [36]. The band at 1596 (1533) cm⁻¹ can be assigned to a B_3g (A_g) mode. The intensity ratio between them (R = I₁₅₉₆/I₁₅₃₃) can be used to quantitatively define the orientation of the pentacene long axis on different substrates [53]. For pentacene on G (center), R = 5.6, while on glass (upper) R = 0.22. Thus, the pentacene molecules are lying almost flat on the G surface, consistent with precious results [15,54].

Figure 5b shows the Raman enhancement effect of 2D layered materials, such as G, h-BN, and MoS₂ on CuPc [55]. Compared to the low intensity of Raman signals for CuPc on blank SiO₂/Si substrate, shown by the black curve in Figure 5b, 1531, 1450 and 1340 cm⁻¹ vibrational modes can be explicitly observed for CuPc on G, h-BN, and MoS₂ substrates. The enhancement factors of CuPc on G (blue line) and h-BN (red line) are stronger than on MoS₂ (green line). Insulated h-BN with a strong B–N bond is favorable to strong dipole-dipole coupling and G with a nonpolar C–C bond is a benefit to the occurrence of charge transfer. Thus, a remarkable Raman scattering enhancement requires strong molecule-substrate coupling and, thus, effective charge transfer between them.

5. C8-BTBT on Layered Substrates

C₈-BTBT can epitaxially grow on exfoliated G and MoS₂ with precisely controlled thickness down to a monolayer into 2D molecular crystals for OFETs [56,57]. The AFM image in Figure 6a shows that C₈-BTBT molecules prefer to grow on G than on SiO₂ accompanied with a layer-by-layer manner and atomic smoothness due to the high diffusion coefficient. According to the measured thickness of the first two layers of 0.6 and 1.7 nm, a schematic illustration of the C₈-BTBT molecular packing is shown in the inset in Figure 6d, similar to above-mentioned case of pentacene on h-BN. Figure 6b displays the AFM image of three layers C₈-BTBT grown on MoS₂ [57]. Interestingly, the average thickness of the first C₈-BTBT layer on MoS₂ is ~1.4 nm, suggesting no WL and the different effect of MoS₂ on organic molecule growth to G. This is attributed to reduced interfacial interactions between C₈-BTBT layer and MoS₂ due to that MoS₂ [58,59] is natively not a π-conjugated system and the lattice constants are rather different from G. A higher density of nucleation sites on MoS₂, especially at the edges, is attributed to the high density of sulfur vacancies in the mechanically-exfoliated monolayer MoS₂ [60,61]. The frequent and purposeful interruption and ambient exposure for AFM characterization does not distinctly affect the film growth, implying that the crystals are of pristine quality and stable in the ambient environment. Figure 6c shows the transfer characteristic of a 1L C₈-BTBT/h-BN-based planar OFET at room temperature [56]. The calculated field-effect mobility reaches up to 10 cm²/Vs, much higher than previously reported values for monolayer OFETs [62,63,64,65,66]. The most significant part of these results is that growing C₈-BTBT molecule on layered substrates does not drastically alert the charge transport characteristic, signifying organic semiconductor crystal can be regarded as quasi-freestanding with minimal disturbance from the substrate.

Figure 6d shows the calculated binding energy (BE) of a single C₈-BTBT with different substrates, which depends highly on the underlying substrate. Such a BE gradient creates temperature windows for C₈-BTBT thermodynamically stable on the corresponding substrates, resulting in self-limited organic molecule beam epitaxy (SLOMBE) [67]. Thus, highly precise, controllable, self-limited epitaxy of layered monocrystalline organic semiconductors (C₈-BTBT) and related heterojunctions (C₈-BTBT/PTCDA) can be obtained on exfoliated G by controlling the substrate temperature. Figure 6e shows the AFM topography image of a heterojunction of bilayer (WL+1L) C₈-BTBT/1L PTCDA/G, indicating the C₈-BTBT was uniformly grown on PTCDA in a self-limited manner. The photodetector based on such a p-n junction displays a photoresponsivity of ~0.37 mA/W @ 514 nm laser, where the organic films are ~15 nm thick to minimize the direct tunneling effects. Thus, by harnessing the vdW interactions at the interfaces, highly controllable, SL epitaxy of layered organic semiconductors and heterojunctions are achievable for future devices.

6. PTCDA on Layered Substrates

PTCDA usually forms an in-plane herringbone structure because of intermolecular hydrogen bonding. EG is continuously over SiC step edges due to its bottom-up growth mechanism [68]. Thus, the EG-covered SiC step edges would not hamper the carpet-like PTCDA growth. As demonstrated in Figure 7a, monolayer PTCDA in a herringbone arrangement follows EG continuously over bi- and tri- SiC bilayer steps. This confirms the possibility to grow a pinhole-free PTCDA monolayer on EG. Synchrotron-based PES investigation reveals weak charge transfer and weak interactions between PTCDA and EG [68]. It is important for the functionalization of the EG surface using PTCDA derivatives to enhance the adhesion of a gate dielectric layer on EG, facilitating the growth of defect-free ultrathin dielectric layers in G-based electronic devices.

Such a self-assembled PTCDA layer can also be used as a buffer layer to protect the topological surface states (TSSs) of Bi₂Se₃, which exhibits a Dirac cone-like dispersion similar to G [69]. Fe deposition on bare Bi₂Se₃ results in resonance states at Fe adatoms due to Coulomb scattering between the Fe adatoms and the TSSs, and the shift of the Dirac point (DP) energy position downward by ~80 meV (doping effect) due to charge transfer from the Fe adatoms to the Bi₂Se₃ surface. On the contrary, Fe deposition on one ML PTCDA covered Bi₂Se₃ results in neither resonance states nor doping effect, as shown in Figure 7b, because of the charge transfer from the Fe adatom to PTCDA molecules and concentration of the Coulomb charge. Thus, organic molecules are promising as spacers in the future TI devices to prevent undesirable doping and scattering effects at the interfaces.

The highest occupied molecular orbital-lowest unoccupied molecular orbital (HOMO-LUMO) gaps of small organic molecules are dependent on the electronic screening effects from the substrate. It is measured to be 3.73, 3.49, and 3.10 eV for PTCDA on SL WSe₂/graphite (semiconducting), graphite (semimetallic), and Au(111) (metallic), respectively, as demonstrated in the scanning tunnelling spectroscopy (STS) results in Figure 7c, although the lattice parameters for these herringbone arrangements are very similar for the different substrates [70].Thus, the semiconducting 2D transition metal dichalcogenides (TMDs) layers can participate actively in hybrid organic−inorganic devices with tailored structures and properties.

7. Conclusions

2D layered-material templated growth is a newly developed method for fabricating high-quality organic semiconductor thin films with controllable morphologies, interface properties, molecular orientations, and electronic structures. G, MoS₂, and h-BN show obviously different effects on the growth of pentacene, CuPc, and C8-BTBT, indicating slight differences in the interfacial interactions. PTCDA can be used as protecting layer due to its inherent intermolecular H-bonding. Large-scale high-quality 2D layered materials are required for future thinner organic (opto-) electronics like OLEDs, OPVs and OFETs.

Acknowledgments

We acknowledge the financial support from the National Natural Science Foundation (NSF) of China (Grants No. 11304398, 11334014, 51173205). Han Huang acknowledges the support from State Key Laboratory of Powder Metallurgy, Central South University and that from NSF of Hunan province (Grants No. 2016JJ1021).

Author Contributions

All authors contributed to the writing and production of this manuscript.

Conflicts of Interest

The authors declare no competing financial interests.

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Figure 1. Molecular structures of pentacene (a), CuPc (b), PTCDA (c), C₈-BTBT (d), respectively. (e) The a-b and b-c planes of a pentacene single crystal, showing the anisotropy of small organic molecules. (f) Schematics of three layered substrates, G, MoS₂ and h-BN.

Figure 2. Morphologies of pentacene thin films on different substrates. (a) AFM topography image of fractal islands of pentacene on SiO₂ at a coverage of ~3 ML. Inset: nucleation at submonolayer coverage. (b) STM image of pentacene on Bi(001) at a coverage of slightly over 1 ML. Inset: high-resolution STM image showing pentacene molecules in the first layer in a standing-up configuration. (c) Twelve nanometer thick pentacene film on Highly Oriented Pyrolytic Graphite (HOPG). (d–f) Schematic representations of the proposed molecular packing corresponding to image in panel (a–c). Panel a reprinted with permission from [12]. Copyright 2004 American Chemical Society. Panel b reprinted from [8] with the permission of AIP Publishing. Panels c, f reprinted with permission from [6] as follows: Koch, N. Physical review letters, 96 (15), 156803, 2006. Copyright 2006, American Physical Society.

Figure 3. Epitaxial growth of pentacene molecular crystals on layered substrates. (a) AFM image of ~50 nm thick pentacene films over the sharp linear boundary between G-covered and bare SiO₂. (b) Forty nanometer pentacene films over the boundary between MoS₂-covered and bare SiO₂. (c) Approximately two ML pentacene crystals with a flat-lying wetting layer on mechanically exfoliated h-BN. (d–f) Schematic illustrations of the molecular packing of (a–c), respectively. (g–i) The transfer characteristics of FETs based on the films in (a–c), respectively. Panel a,d,g reprinted with permission from [15]. Copyright 2011 American Chemical Society. Panel b, h reprinted with permission from [40]. Copyright 2015 American Chemical Society. Panel c, f, i reprinted with permission from [7] as follows: Zhang, Y. Physical review letters, 116 (1), 016602, 2016. Copyright 2016 American Physical Society.

Figure 4. The AFM morphologic images and 2D-GIXRD images of CuPc on glass (a,d), G-covered glass (b,e), and bulk MoS₂ (c,f), respectively. The insets show the corresponding CuPc packing. Panel a, b, d, e is reproduced from [45] with permission from The Royal Society of Chemistry. Panel c, f is reprinted with permission from [50], copyright 2015 American Chemical Society.

Figure 5. (a) Raman spectra from pentacene on glass without/with monolayer G, and from G on glass. (λ = 532 nm; 3.0 mW). (b) Raman spectra from 2 Å thick CuPc on G (blue line), on h-BN (red line), on MoS₂ (green line), and on the blank SiO₂/Si substrate (black line). Panel a reprinted with permission from [36], copyright 2015 American Chemical Society. Panel b reprinted with permission from [55], copyright 2015 American Chemical Society.

Figure 6. C₈-BTBT on layered substrates. AFM image of C₈-BTBT on G (a) and MoS₂ (b). (c) Transfer characteristic of 1L C₈-BTBT/h-BN based planar OFET at room temperature. Black and blue lines are drawn in linear and log scales, respectively. Inset shows the optical microscopy image of the device. (d) Blue dots: calculated binding energies of a single C₈-BTBT molecule on G, IL/G, 1L/IL/G, and 2L/1L/IL/G. Red dash line: C₈-BTBT−C₈-BTBT interaction. Inset shows the molecular structure of C₈-BTBT and molecular packing of different C₈-BTBT layers on G. (e) AFM images of SLOMBE of bilayer C₈-BTBT on PTCDA. (f) Output characteristics of the p-n junction (>15 nm) under the dark conditions (black) and under the 0.67 μW laser illumination. Inset shows schematic layout of the device. Panel a, c reprinted with permission from [56], copyright 2014, Nature Publishing Group. Panel b reprinted from [57], with the permission of AIP Publishing. Panel d, e, f adapted with permission from [67], copyright 2016 American Chemical Society.

Figure 7. PTCDA on layered substrates. (a) Molecularly-resolved STM image of one monolayer PTCDA covered epitaxial G on SiC(0001). (b) STM image of ~0.01 ML Fe (protrusions) on one monolayer PTCDA covered Bi2Se3 (left) and STS curves at positions with/without Fe (purple/black, right). (c) STS curves at positions of PTCDA on Au(111), graphite, and WSe2/graphite. Panel a printed with permission from [68], copyright 2009 American Chemical Society. Panel b printed with permission from [69], copyright 2015 American Chemical Society. Panel c printed with permission from [70], copyright 2016 American Chemical Society.

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Huang, H.; Huang, Y.; Wang, S.; Zhu, M.; Xie, H.; Zhang, L.; Zheng, X.; Xie, Q.; Niu, D.; Gao, Y. Van Der Waals Heterostructures between Small Organic Molecules and Layered Substrates. Crystals 2016, 6, 113. https://doi.org/10.3390/cryst6090113

AMA Style

Huang H, Huang Y, Wang S, Zhu M, Xie H, Zhang L, Zheng X, Xie Q, Niu D, Gao Y. Van Der Waals Heterostructures between Small Organic Molecules and Layered Substrates. Crystals. 2016; 6(9):113. https://doi.org/10.3390/cryst6090113

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Huang, Han, Yingbao Huang, Shitan Wang, Menglong Zhu, Haipeng Xie, Lei Zhang, Xiaoming Zheng, Qiliang Xie, Dongmei Niu, and Yongli Gao. 2016. "Van Der Waals Heterostructures between Small Organic Molecules and Layered Substrates" Crystals 6, no. 9: 113. https://doi.org/10.3390/cryst6090113

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Huang, H., Huang, Y., Wang, S., Zhu, M., Xie, H., Zhang, L., Zheng, X., Xie, Q., Niu, D., & Gao, Y. (2016). Van Der Waals Heterostructures between Small Organic Molecules and Layered Substrates. Crystals, 6(9), 113. https://doi.org/10.3390/cryst6090113

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