Local Electronic Structure of a Single-Layer Porphyrin-Containing

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Local Electronic Structure of a Single-Layer Porphyrin-Containing Covalent Organic Framework Chen Chen, Trinity Joshi, Huifang Li, Anton D. Chavez, Zahra Pedramrazi, PeiNian Liu, Hong Li, William R. Dichtel, Jean-Luc Bredas, and Michael F. Crommie ACS Nano, Just Accepted Manuscript • DOI: 10.1021/acsnano.7b06529 • Publication Date (Web): 20 Dec 2017 Downloaded from http://pubs.acs.org on December 21, 2017

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Local Electronic Structure of a Single-Layer Porphyrin-Containing Covalent Organic Framework Chen Chen1‡, Trinity Joshi2‡, Huifang Li3‡, Anton D. Chavez4,5, Zahra Pedramrazi2, Pei-Nian Liu6, Hong Li3,7, William R. Dichtel4*, Jean-Luc Bredas3,7*, Michael F. Crommie2,8,9* 1 Department of Chemistry, University of California at Berkeley, Berkeley, CA 94720, USA 2 Department of Physics, University of California at Berkeley, Berkeley, CA 94720, USA 3 Laboratory for Computational and Theoretical Chemistry of Advanced Materials, Physical Science and Engineering Division, King Abdullah University of Science and Technology, Thuwal 23955-6900, Kingdom of Saudi Arabia 4 Department of Chemistry, Northwestern University, Evanston, Illinois 60208, United States 5 Department of Chemistry and Chemical Biology, Cornell University, Ithaca, NY 14853, United States 6 Shanghai Key Laboratory of Functional Materials Chemistry and School of Chemistry & Molecular Engineering, East China University of Science and Technology, 130 Meilong Road, Shanghai, 200237, China 7 School of Chemistry and Biochemistry & Center for Organic Photonics and Electronics, Georgia Institute of Technology, 901 Atlantic Drive NW, Atlanta, Georgia 303320400, United States 8 Materials Sciences Division, Lawrence Berkeley National Laboratory, Berkeley, CA 94720, USA 9 Kavli Energy NanoSciences Institute at the University of California Berkeley and the Lawrence Berkeley National Laboratory, Berkeley, CA 94720, USA ‡ These authors contributed equally / *corresponding authors

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Abstract We have characterized the local electronic structure of a porphyrin-containing singlelayer covalent organic framework (COF) exhibiting a square lattice. The COF monolayer was obtained by the deposition of 2,5-dimethoxybenzene-1,4-dicarboxaldehyde (DMA) and 5,10,15,20-tetrakis (4-aminophenyl) porphyrin (TAPP) onto a Au(111) surface in ultra-high vacuum followed by annealing to facilitate Schiff-base condensations between monomers. Scanning tunneling spectroscopy (STS) experiments conducted on isolated TAPP precursor molecules and the covalently linked COF networks yield similar transport (HOMO-LUMO) gaps of 1.85 ± 0.05 eV and 1.98 ± 0.04 eV, respectively. The COF orbital energy alignment, however, undergoes a significant downward shift compared to isolated TAPP molecules due to the electron-withdrawing nature of the imine bond formed during COF synthesis. Direct imaging of the COF local density of states (LDOS) via dI/dV mapping reveals that the COF HOMO and LUMO states are localized mainly on the porphyrin cores and that the HOMO displays reduced symmetry. DFT calculations reproduce the imine-induced negative shift in orbital energies and reveal that the origin of the reduced COF wavefunction symmetry is a saddle-like structure adopted by the porphyrin macrocycle due to its interactions with the Au(111) substrate.

Key words: covalent organic framework; scanning tunneling microscopy and spectroscopy; density functional theory; electronic structure; porphyrin


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Covalent organic frameworks (COFs) are extended crystalline organic structures made of light elements with tailorable structures determined by the geometries and chemical identities of their monomers. Since the first successful synthesis of COF-1 from boronic acid precursors,1 numerous COFs with different chemical linkages,2-6 geometries,7-9 and pore sizes10 have been reported, showing properties of interest for applications such as gas storage, 11,12 catalysis,13-15 and photodetectors.16,17 The desirable electronic properties observed in single-layer twodimensional materials such as graphene and the transition metal dichalcogenides have sparked great interest in further understanding the properties of atomically-thin COF films. Such ultrathin COFs have been synthesized in solution,7,18,19 at air/water interfaces,20,21 and on surfaces.22-26 Although there has been rapid progress in synthesizing many different COFs, characterization of their local electronic properties has progressed at a slower rate. A limited number of COFs displaying honeycomb symmetry have been examined using scanning tunneling spectroscopy techniques, revealing different aspects of their frontier orbital electronic structure.27,28 COFs exhibiting square lattice symmetry have also been synthesized (e.g. porphyrin or phthalocyaninecontaining COFs),7,29-32 but their local electronic structure has not yet been characterized. Here we present a combined STM and theoretical study of the local electronic structure of a single-layer porphyrin-containing COF at the surface of a Au(111) crystal. The Schiff-base condensation of 5,10,15,20-tetrakis (4-aminophenyl) porphyrin core molecules (TAPP) with 2,5dimethoxybenzene-1,4-dicarboxaldehyde linker molecules (DMA) results in a 2D COF with a square lattice. The COF conduction and valence band states were measured by scanning tunneling spectroscopy (STS) and compared to the highest occupied molecular orbital (HOMO) and the lowest unoccupied molecular orbital (LUMO) of an isolated TAPP molecule. While the COF energy gap does not change significantly compared to the HOMO-LUMO gap of isolated,


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non-bonded TAPP molecules on Au(111), an energy downshift of 0.4 eV is observed for the COF band edges compared to isolated TAPP orbital energies. The valence band edge wavefunction of the COF exhibits reduced symmetry compared to the conduction band edge wavefunction, similar to behavior observed for isolated TAPP molecules. Density functional theory (DFT) calculations suggest that the observed energy downshift arises from the presence of electron-withdrawing imine linkages within the COF and that the reduced valence band symmetry arises from molecular buckling induced by interaction with the underlying Au(111) substrate. These results provide insight into how linkage-driven charge transfer causes the electronic structure of molecules to evolve as they covalently bond into networks. Results and Discussion We first performed STM/STS electronic characterization of an isolated TAPP molecule on Au(111) as a control (Fig. 1, all STM data reported here were obtained at T=7K in ultra-high vacuum). The STM topographic image of Fig. 1a shows that TAPP exhibits a four-lobe structure with a slight dip in the middle, corresponding to the core of the porphyrin. Energy-dependent LDOS obtained by dI/dV spectroscopy at the center of a TAPP molecule exhibits two peaks that are assigned to the TAPP HOMO (-0.44 ± 0.06 V) and LUMO (+1.42 ± 0.05 V), corresponding to a 1.85 eV transport gap (Fig. 1b) (dI/dV traces obtained on different parts of the TAPP molecule exhibit different amplitudes for these peaks, but the peak energies do not vary). dI/dV mapping was performed at the HOMO and LUMO peak energies to examine the wavefunction spatial distribution for isolated TAPP molecules (Figs. 1c, d). As seen in Fig. 1c, the HOMO state is nearly two-fold symmetric and exhibits an asymmetrical "dumbbell" structure in the interior. The LUMO state is more diffuse and has LDOS intensity in regions where the HOMO


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state is dark (Fig.1d). Similar frontier orbital LDOS patterns have been reported previously for related porphyrin molecule adsorbates on Au(111).33 TAPP molecules were covalently bonded into a COF network by condensing with DMA linker molecules. As shown in Fig. 2a, DMA molecules were first deposited onto a Au(111) surface with a coverage of 0.9 monolayer (ML), resulting in close-packed islands with an intermolecular spacing of 0.8 nm. TAPP molecules were then deposited onto this surface, resulting in an intermixed adlayer (DMA + TAPP) as shown in Fig. 2b. The TAPP/DMA intermixed adlayer was then annealed at 150° C for 1 hour in UHV to induce COF formation. The resultant COF covers the Au(111) surface in square-lattice patches (Fig. 2c) with a unit cell size of 2.5 ± 0.1 nm, in good agreement with the expected porphyrin core-to-core distance (2.57 nm) for the COF structure shown in Fig. 2d (see SI for details). The observed structure is also in agreement with room temperature ambient STM images of this COF obtained previously from samples grown on graphite via solution-phase processing.34 The zoomed-in STM image shown in Fig. 3a shows additional detail that confirms the formation of the COF, which we refer to as COF366-OMe following the naming convention used in the report of its solvothermal synthesis.30 The positions of each methoxy group can be inferred from the orientation of the oval-shaped linkages positioned between porphyrin centers in the zoomed-in image of Fig. 3a. We note that these methoxy groups are randomly distributed, i.e., there are no chiral domains within the COF. The local electronic properties of COF366-OMe were characterized by performing STS point spectroscopy at different locations on the 2D COF (Fig. 3b). The black curve shows a reference spectrum taken on a bare Au(111) region; the feature near -0.5 V corresponds to the well-known Shockley surface state of Au(111). When the TAPP core of the COF was probed (at the position of the blue X in Fig. 3a), two prominent peaks are seen at -0.9 V and +1.0 V (blue


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curve). In contrast, the spectrum of the DMA linker shows only a small peak at +1.0 V (red curve), suggesting that this feature arises from delocalization of the state into the linker. We assign the peak at -0.9 V as the COF366-OMe valence band maximum and the peak at +1.0 V as the conduction band minimum, thus leading to a band gap of 1.98 ± 0.04 eV for COF366-OMe (the uncertainty is the standard deviation of measurements obtained from 10 different cores, each connected to four nearest neighbors). Because the COF electronic structure is relatively localized, we refer to the COF valence band maximum as the highest occupied molecular orbital (HOMO) and the COF conduction band minimum as the lowest unoccupied molecular orbital (LUMO). A closer inspection of the extended structure in Fig. 3a reveals that some of the linkers are missing, resulting in TAPP cores that are covalently bonded to only two or three DMA linkers instead of the four found in the ideal COF structure. To understand the effect of this type of defect, we took dI/dV point spectra on TAPP cores connected to different numbers of DMA linkers. The average HOMO and LUMO energies for TAPP cores connected to different numbers of linkers are plotted in Fig. 3c. The HOMO-LUMO gap measured at the site of a TAPP core does not change significantly with the number of linkers bonded to it. However, a large energy downshift in the HOMO/LUMO states (0.4 eV) is seen as soon as even a single DMA linker is bound. Subsequent bound linkers do not significantly change the energy shift, although a slight downward trend in the HOMO energies is seen. Spectroscopic surveys performed in different COF regions and on different parts of the porphyrin cores yield no significant deviations from these findings. The spatial wavefunction distribution of the COF366-OMe HOMO and LUMO states was measured by dI/dV mapping conducted at their corresponding peak energies. Fig. 4a shows an STM topographic image of the COF segment on which dI/dV mapping was performed. As


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shown in Figs. 4b and 4c, experimental HOMO and LUMO dI/dV maps both have significantly higher intensity on the TAPP cores than on the DMA linkers. The COF LUMO state exhibits a four-lobe structure with two nodal lines while the HOMO state exhibits a smaller “dumbbell” shape with bright intensity near the LUMO nodal region. There is some resemblance between the COF HOMO/LUMO states and the isolated TAPP precursor molecule HOMO/LUMO states (Fig. 1), but the COF states are more symmetric. We note that the “dumbbells” of the COF HOMO can be misaligned between adjacent porphyrin cores. We first performed a series of DFT-PBE calculations aimed at understanding the origin of the electronic structure observed in our experiments. The initial calculations focused on isolated TAPP molecules (i.e., core molecules with zero DMA linkers) as well as the full, periodic COF366-OMe network (i.e., core molecules with four DMA linkers) in the absence of substrate effects (i.e., the “freestanding” limit). After optimization both systems contained a planar central porphine macrocycle with the four phenyl rings twisted with dihedral angles ranging from 60º to 67º with respect to the central plane. The energies of the HOMO and LUMO states for the isolated TAPP molecule and the COF366-OMe network are plotted in Fig. 3d where zero energy represents the vacuum level (detailed methodology and band structure results are discussed in the SI). The formation of COF366-OMe results in a LUMO downshift of 0.57 eV and a HOMO downshift of 0.29 eV compared to the isolated TAPP molecule. Formation of the COF thus leads to an energy downshift similar to what is seen experimentally, but the calculation also shows an energy gap reduction. This reduction is not observed in the experiment owing to the interactions of the TAPP and COF monolayers with the Au(111) surface (vide infra).


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Although these calculations were performed at the standard DFT-PBE level, which tends to underestimate absolute HOMO-LUMO gaps, the observed relative energy level shifts due to covalent bonding to the DMA linkers are consistent with our STS measurements (additional calculations using hybrid functionals are given in the SI). This energy-level downshift is explained by the fact that the amine (–NH2) group of the isolated TAPP molecule is relatively electron-rich (i.e., electron-donating) whereas the imine (-C=N-) group of the COF is more electron-poor (i.e., electron-withdrawing). As a result, the transition from amine to imine due to the condensation reaction decreases electron density within the porphyrin core, thereby electrostatically shifting the frontier orbital energies downwards. This was further confirmed by the results of calculations on the electronic structure of a TAPP molecule bonded to a single DMA linker using a localized (atomic) basis set (with the Gaussian 09 package). Once again a clear downshift is observed in the frontier orbitals of the combined TAPP+DMA system compared to isolated TAPP molecules (full details shown in SI). To better understand the spatial wavefunction properties of these molecular systems, we extended the DFT calculations for both individual TAPP molecules and COF366-OMe networks to include contact with a Au(111) substrate. These calculations show that the interaction between an isolated TAPP molecule and the underlying Au(111) substrate leads to a “saddle-like” structure, where the four pyrrole rings in the porphine macrocycle tilt alternately up and down so as to maximize the nitrogen-gold interactions (the equilibrium geometry has all four porphine nitrogens nearly on top of four Au atoms in the top layer of the Au(111) surface). This is in agreement with earlier results on other porphyrin derivatives.35-37 After COF formation on the Au(111) surface, the porphine macrocycles are observed to retain the saddle structure (see SI Fig. S6). This distortion of the porphyrin core leads to a much stronger charge localization on the β-β


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C-C bond of the two up-tilted pyrrole rings compared to the β-β C-C bond of the two down-tilted pyrroles, resulting in the dumbbell shape of the COF HOMO state (Fig. 4e). In contrast, the calculated LDOS of the LUMO state (Fig. 4f) displays a nearly four-fold symmetric distribution on the TAPP core, in reasonable agreement with the four-lobe structure observed in the COF dI/dV map (Fig. 4c) (some discrepancy does exist between theoretical and experimental maps, likely due to differences in tip trajectory since the experimental dI/dV maps were taken along a surface of constant-current feedback while the theoretical simulation shows LDOS intensity taken along a plane at fixed distance above the COF). Inclusion of the substrate in our calculations also results in the HOMO-LUMO gap remaining constant for isolated TAPP molecules compared to a fully formed COF, thus explaining why we do not experimentally observe the gap reduction predicted by the “freestanding” calculations (see SI for full description). We note that although the core dominates both the experimental and theoretical LUMO LDOS images shown in Fig. 4, some LUMO state density does still extend across the DMA linker. The LUMO is thus not completely localized to the core, as can be seen from the isosurface plot of Fig. S8 in the SI. The reason the core dominates the LUMO maps of Fig. 4 is because the STM tip is relatively far from the surface (~4 Å) and the core LDOS is much greater than the linker LDOS at this distance. This is partly due to the fact that the phenyl rings of the core twist away from the Au surface by 35° (leading to the four brightest spots in the simulated LUMO dI/dV map) whereas the DMA linkers lie flat.

Conclusions


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In conclusion, we have characterized the local electronic structure of a single-layer porphyrin-containing square-lattice COF on Au(111). Energy shifts of the frontier orbitals of the porphyrin core are observed upon COF formation due to the electron withdrawing nature of the imine linkages. The experimentally measured HOMO and LUMO wavefunctions of the COF have highest intensity on the porphyrin cores and exhibit an energy gap of 1.98 ± 0.04 eV. DFTbased electronic local density of states simulations are consistent with our experimental data and confirm that substrate-induced buckling observed for isolated porphyrins persists in COF networks. This provides insight into how the electronic structure of molecular nanostructures is affected by forming covalent bonds between monomer components.

Methods A gold crystal with a polished Au(111) surface was used as the substrate for these experiments. Standard Ar+ sputtering/annealing cycles were applied to obtain an atomically clean surface. Precursor molecules were thermally evaporated onto the Au(111) surface held at room temperature in an ultra-high vacuum environment (base pressure ~2 × 10 Torr) using a home-built Knudsen-type dual-cell evaporator. The temperature of the evaporator was ~110 °C for the DMA precursor and ~320 °C for the TAPP precursor. The 2D COF network was formed by annealing the mixed adlayer at ~150 °C for 1 hr. The sample was then cooled down and placed into a home-built cryogenic STM to perform imaging and spectroscopy at T = 7K. A PtIr tip was used for all STM measurements. dI/dV spectra were measured using a lock-in amplifier with the sample bias modulated by a 451 Hz, 10 mV (rms) sinusoidal voltage under openfeedback conditions. All STM images were obtained in constant current mode and processed by WSxM38. dI/dV spectra were acquired from more than 20 different TAPP single molecules and


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from more than 10 different COF regions while utilizing numerous different tips to ensure reproducibility. Dispersion-corrected density-functional theory (DFT-D3) calculations39 were carried out with the projector-augmented wave (PAW) method40 using the Perdew−Burke−Ernzerhof (PBE) exchange-correlation functional41 for geometry optimization and self-consistent total-energy calculations. The kinetic energy cutoff of plane-wavefunctions was 400 eV and the total energy was converged to 10-6 eV for the self-consistent iterations. A Γ-point-only k-sampling method was adopted for geometry optimizations and a 6 × 6 × 1 k-grid generated by the Monkhorst–Pack scheme42 was used for self-consistent total-energy calculations and density-of-states (DOS) analyses. Atomic charges on the framework atoms were examined by the Bader charge decomposition method.43 Calculations were performed with the Vienna Ab Initio Simulation Package (VASP).44, 45 Calculations that included the Au(111) substrate used a repeated slab approach. The Au(111) surface slabs were separated by a vacuum space larger than 20 Å and each slab contained four Au layers. The top two Au layers (together with the molecular adlayer) were relaxed in the course of geometry optimizations while the bottom two Au layers were kept fixed in their bulk positions (lattice constant = 4.17 Å). All geometry optimizations were performed using a damped molecular dynamics scheme until the forces on the atoms were < 0.02 eV/Å. To compensate for long-range dipole−dipole interactions among the asymmetric slabs, a dipole sheet was introduced in the middle of the vacuum gap; this procedure leads to zero electric field and a flat electrostatic potential in the vacuum region, allowing a reliable evaluation of the surface potential. Simulated LDOS images were constructed using Tersoff-Hamann theory46 and were visualized via the p4VASP program. A 2D Gaussian filter (σ = 1.2 Å) was applied to the


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output of the p4VASP program to account for the finite size of our STM tip.

Associated Content Supporting Information: The supporting information is available online at: Details on DFT calculations, saddle structure of porphyrin on Au(111), and DOS plots.

Acknowledgements This research was supported by the Army Research Office Multidisciplinary University Research Initiative (MURI) program under grant no. W911NF-15-1-0447 (STM spectroscopy, DFT analysis), by the Army Research Office grant no. W911NF-17-1-0339 to Georgia Tech (DFT calculations), and by the U.S. Department of Energy, Office of Basic Energy Sciences Nanomachine Program under contract no. DEAC02-05CH11231 (sample preparation). The KAUST IT Research Computing Team and the KAUST Supercomputing Laboratory are gratefully acknowledged for providing generous computational resources for part of our theoretical work. T. J. acknowledges support from NSF Graduate Research Fellowship Program under grant no. DGE 1106400. A. D. C. acknowledges support from the NDSEG Fellowship Program.

Author Contributions C.C., T.J., Z.P., and P.-N.L. performed STM and STS measurements. C.C. and T.J. performed data analysis. H.L., H.L., and J.-L.B. performed DFT calculations and interpretation of STM data. A. D. C. and W.R.D performed synthesis of COF precursor molecules and interpretation of STM


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data. M.F.C. supervised the experimental scanned probe measurements and helped to interpret the results. All authors contributed to the scientific discussion and helped in writing the manuscript. Additional Information Correspondence

and

requests

for

materials

should

be

addressed

to

W.R.D.

([email protected]), J.-L.B. ([email protected]), and M.F.C. ([email protected]).

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13. Ding, S.-Y.; Gao, J.; Wang, Q.; Zhang, Y.; Song, W.-G.; Su, C.-Y.; Wang, W., Construction of Covalent Organic Framework for Catalysis: Pd/Cof-Lzu1 in Suzuki–Miyaura Coupling Reaction. J. Am. Chem. Soc. 2011, 133, 19816-19822. 14. Lin, S.; Diercks, C. S.; Zhang, Y.-B.; Kornienko, N.; Nichols, E. M.; Zhao, Y.; Paris, A. R.; Kim, D.; Yang, P.; Yaghi, O. M.; Chang, C. J., Covalent Organic Frameworks Comprising Cobalt Porphyrins for Catalytic Co2 Reduction in Water. Science 2015, 349, 1208-1213. 15. Fang, Q.; Gu, S.; Zheng, J.; Zhuang, Z.; Qiu, S.; Yan, Y., 3d Microporous BaseFunctionalized Covalent Organic Frameworks for Size-Selective Catalysis. Angew. Chem. Int. Ed. 2014, 53, 2878-2882. 16. Wan, S.; Guo, J.; Kim, J.; Ihee, H.; Jiang, D., A Photoconductive Covalent Organic Framework: Self‐Condensed Arene Cubes Composed of Eclipsed 2d Polypyrene Sheets for Photocurrent Generation. Angew. Chem. Int. Ed. 2009, 121, 5547-5550. 17. Dogru, M.; Handloser, M.; Auras, F.; Kunz, T.; Medina, D.; Hartschuh, A.; Knochel, P.; Bein, T., A Photoconductive Thienothiophene-Based Covalent Organic Framework Showing Charge Transfer Towards Included Fullerene. Angew. Chem. Int. Ed. 2013, 125, 2992-2996. 18. Colson, J. W.; Woll, A. R.; Mukherjee, A.; Levendorf, M. P.; Spitler, E. L.; Shields, V. B.; Spencer, M. G.; Park, J.; Dichtel, W. R., Oriented 2d Covalent Organic Framework Thin Films on Single-Layer Graphene. Science 2011, 332, 228-231. 19. Tanoue, R.; Higuchi, R.; Enoki, N.; Miyasato, Y.; Uemura, S.; Kimizuka, N.; Stieg, A. Z.; Gimzewski, J. K.; Kunitake, M., Thermodynamically Controlled Self-Assembly of Covalent Nanoarchitectures in Aqueous Solution. ACS Nano 2011, 5, 3923-3929. 20. Dai, W.; Shao, F.; Szczerbiński, J.; McCaffrey, R.; Zenobi, R.; Jin, Y.; Schlüter, A. D.; Zhang, W., Synthesis of a Two-Dimensional Covalent Organic Monolayer through Dynamic Imine Chemistry at the Air/Water Interface. Angew. Chem. Int. Ed. 2016, 55, 213-217. 21. Sahabudeen, H.; Qi, H.; Glatz, B. A.; Tranca, D.; Dong, R.; Hou, Y.; Zhang, T.; Kuttner, C.; Lehnert, T.; Seifert, G., Wafer-Sized Multifunctional Polyimine-Based Two-Dimensional Conjugated Polymers with High Mechanical Stiffness. Nat. Commun. 2016, 7, 13461. 22. Zwaneveld, N. A.; Pawlak, R.; Abel, M.; Catalin, D.; Gigmes, D.; Bertin, D.; Porte, L., Organized Formation of 2d Extended Covalent Organic Frameworks at Surfaces. J. Am. Chem. Soc. 2008, 130, 6678-6679. 23. Gutzler, R.; Walch, H.; Eder, G.; Kloft, S.; Heckl, W. M.; Lackinger, M., Surface Mediated Synthesis of 2d Covalent Organic Frameworks: 1, 3, 5-Tris (4-Bromophenyl) Benzene on Graphite (001), Cu (111), and Ag (110). Chem. Commun. 2009, 0, 4456-4458. 24. Sánchez-Sánchez, C.; Brüller, S.; Sachdev, H.; Müllen, K.; Krieg, M.; Bettinger, H. F.; Nicolaï, A.; Meunier, V.; Talirz, L.; Fasel, R.; Ruffieux, P., On-Surface Synthesis of BnSubstituted Heteroaromatic Networks. ACS Nano 2015, 9, 9228-9235. 25. Bieri, M.; Nguyen, M.-T.; Gröning, O.; Cai, J.; Treier, M.; Aït-Mansour, K.; Ruffieux, P.; Pignedoli, C. A.; Passerone, D.; Kastler, M., Two-Dimensional Polymer Formation on Surfaces: Insight into the Roles of Precursor Mobility and Reactivity. J. Am. Chem. Soc. 2010, 132, 1666916676. 26. Liu, X.-H.; Guan, C.-Z.; Ding, S.-Y.; Wang, W.; Yan, H.-J.; Wang, D.; Wan, L.-J., OnSurface Synthesis of Single-Layered Two-Dimensional Covalent Organic Frameworks Via Solid–Vapor Interface Reactions. J. Am. Chem. Soc. 2013, 135, 10470-10474. 27. Morchutt, C.; Björk, J.; Straßer, C.; Starke, U.; Gutzler, R.; Kern, K., Interplay of Chemical and Electronic Structure on the Single-Molecule Level in 2d Polymerization. ACS Nano 2016, 10, 11511-11518. 14 ACS Paragon Plus Environment

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Captions for figures:

Figure 1. Single TAPP molecule electronic structure. (a) STM topographic image of a single TAPP molecule on a Au(111) surface (sample bias = 2.0 V, tunneling current = 10 pA). (The “X” represents the location where the dI/dV curve shown in (b) was obtained.) (b) dI/dV point spectra measured on top of a single TAPP molecule shows HOMO and LUMO states (open feedback parameters: = 1.0 V, = 60 pA; modulation voltage = 10 mV). Inset shows chemical structure of a TAPP molecule. dI/dV maps of the TAPP HOMO and LUMO states are shown for bias voltages (c) -0.42 V and (d) 1.50 V (open feedback parameters: = 1.0 V, = 60 pA; modulation voltage = 10 mV).

Figure 2. Synthesis of COF366-OMe on a Au(111) surface. (a) STM topographic image of DMA molecules deposited on Au(111) surface ( = 0.8 V, = 10 pA). Inset shows the structure of a DMA molecule. (b) STM topographic image shows a mixture of TAPP and DMA molecules on Au(111) surface before reaction ( = 1.0 V, = 10 pA). (c) Large-scale STM image of COF366-OMe on Au(111) after reaction of TAPP and DMA molecules ( = 2.0 V, = 10 pA). (d) Model structure of COF366-OMe. The black square shows a unit cell.


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Figure 3. STS measurements of COF366-OMe on Au(111) surface. (a) Zoomed-in STM image of COF366-OMe ( = 1.0 V, = 10 pA). Red and blue crosses indicate the positions at which dI/dV spectra were taken. (b) dI/dV spectra taken at location of DMA linker (red curve) and TAPP core (blue curve) shown in (a), as well as bare Au(111) surface for reference (black curve). Each curve is normalized by the value at = −1.0 V, and the red (blue) curve is upshifted by 1 (2.5) a.u. for clarity (open feedback parameters: = 1.0 V, = 40 pA, 60 pA, 80 pA for the red, black and blue curve respectively; modulation voltage = 10 mV). (c) Effect of number of DMA neighbors on the HOMO and LUMO energies of a porphyrin core (0 DMA neighbors refers to an isolated TAPP molecule). Each data point consists of at least eight different measurements, and the error bars are smaller than the size of the dots. (d) DFT calculations of the electronic structure of freestanding, isolated TAPP molecule and COF366-OMe, indicating a downshift in HOMO and LUMO energies upon COF formation (zero energy is the vacuum level).

Figure 4. Spatial distribution of COF366-OMe electronic states. (a) STM topographic image shows zoom-in view of COF366-OMe ( = 1.0 V, = 60 pA). Experimental dI/dV maps for (b) the COF HOMO at -0.90 V and (c) the COF LUMO at +1.00 V (open feedback parameters: = −0.90 V for HOMO and +1.00 V for LUMO, = 60 pA; modulation voltage = 10 mV). (d) DFT-optimized adsorption geometry of COF366-OMe on Au(111) surface. Simulated LDOS maps of COF366-OMe on Au(111) for (e) HOMO state and (f) LUMO state.


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Topography (b)

(a)

6

x

dI/dV / dI/dV (-0.8 V)

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5

NH2

4 HOMO 3

NH H 2N

N

(c)

N HN

NH2

2 NH2

1

1 nm

LUMO

STM Spectroscopy

0 -1.0 -0.5

0.5 1.0 0 Sample Bias (V)

dI/dV HOMO (d) -0.42 V

ACS Paragon Plus Environment

1.5

dI/dV LUMO 1.50 V

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(a)

DMA/Au(111)

(b)

O O H3 C

CH3

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DMA+TAPP/Au(111)

O O

3 nm

1 nm (c)

COF366-OMe/Au(111)

(d)

10 nm


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x

2 nm (c)

2.0 1.5 1.0 0.5 0.0 -0.5 -1.0

x

Experiment

(b) dI/dV / dI/dV (-1.0V)

COF366-OMe/Au(111)

LUMO HOMO

0 1 2 3 4 Number of DMA neighbors

COF366-OMe Spectroscopy

5

TAPP Core DMA Linker Au(111)

4 3 2 1 0

-1.0 -0.5 0 0.5 1.0 Sample Bias (V)

(d) -2.0 Energy (eV)

(a)

Energy (eV)

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Theory

-3.0 TAPP -4.0 -5.0


COF366-OME

0 4 Number of DMA neighbors

1.5

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(a)

Topography

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(b) Exp. dI/dV HOMO (-0.9 V) (c) Exp. dI/dV LUMO (1.0 V)

1 nm (d)

(e)

Theory HOMO


(f)

Theory LUMO

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LUMO

HOMO

1 nm

COF366-OMe/Au(111)


Local Electronic Structure of a Single-Layer Porphyrin-Containing

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