Formation of Au-Silane Bonds

Yochelis, Shira; Katzir, Eran; Kalcheim, Yoav; Gutkin, Vitaly; Millo, Oded; Paltiel, Yossi

doi:https://doi.org/10.1155/2012/903761

Journal of Nanotechnology

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Abstract Introduction Materials and Methods Results Conclusions Acknowledgments References Copyright Related Articles

Research Article | Open Access

Volume 2012 | Article ID 903761 | https://doi.org/10.1155/2012/903761

Formation of Au-Silane Bonds

Shira Yochelis,¹Eran Katzir,¹Yoav Kalcheim,²Vitaly Gutkin,³Oded Millo,²and Yossi Paltiel¹

Academic Editor: Ramón Antonio Zárate

Received08 Jan 2012

Revised03 Apr 2012

Accepted18 Apr 2012

Published27 Jun 2012

Abstract

Many intriguing aspects of molecular electronics are attributed to organic-inorganic interactions, yet charge transfer through such junctions still requires fundamental study. Recently, there is a growing interest in anchoring groups, which considered dominating the charge transport. With this respect, we choose to investigate self-assembly of disilane molecules sandwiched between gold surface and gold nanoparticles. These assemblies are found to exhibit covalent bonds not only between the anchoring Si groups and the gold surfaces but also in plane crosslinks that increase the monolayer stability. Finally, using scanning tunneling spectroscopy we demonstrate that the disilane molecules provide strong electrical coupling between the Au nanoparticles and a superconductor substrate.

1. Introduction

Organic-inorganic complexes bring many intriguing features to nanoscale phenomena and in particular to molecular electronics. Some of the attractive applications include organic light-emitting devices [1, 2] (OLEDs), memory devices, field-effect transistors (FETs), solar cells, and developing single-molecule and single-electron devices [3–6]. Consequently, for realizing molecular devices, it is crucial to understand how to exploit electron transport through organic molecules [7–9], metal passivation and corrosion [10], and surfaces’ wetting [11, 12].

One of the key matters in molecular electronics is associated with charge transport through the molecule and the corresponding electrode-molecule-electrode junctions that is playing a critical role in the transport of the electron through the molecule [13, 14]. The influencing factors in these junctions were illustrated by a systematic study of anchoring groups which affect the single-molecule conductance [15]. Chen et al. used alkanes terminated with different anchoring groups bound to gold electrodes as a model system and showed tight correlation to the bond strength. For example, –SH is known to form a strong S–Au covalent bonds, –NH₂–terminated alkanes are described by a weak covalent binding [13, 16], while COOH is believed to exhibit partially ionic and coordinated interactions [17]. A contact resistance was measured to confirm high sensitivity to the anchoring group and was found to vary in the order of Au–S > Au–NH₂ > Au–COOH. The phenomenon was attributed to different electronic coupling efficiencies provided by the different anchoring groups between the alkane and the electrodes. Zotti et al. presented a combined experimental and theoretical study revealing the influence of the anchoring group on electronic transport through single-molecule junction [18]. Transport experiments through tolane molecules attached to gold electrodes via thiol-, nitro-, and cyano- anchoring groups were performed and were fitted to a single-level tunneling model, which allowed extracting the position and broadening of the molecular levels that dominate the transport. Their calculation revealed that the anchoring groups control the nature of the conduction according to their donor or acceptor character. Recently, an analysis of the charge transport through single-molecule junction was performed to define the influence of molecular end groups for increasing electrode separation [19]. Inelastic electron tunneling spectroscopy results demonstrated that amino-ended molecules bind only weakly to Au, in contrast to thiol-ended bond ones. It was explained that the strong Au–thiol bond can cause a major mechanical deformation of the Au electrode. Other studies considered the dependence of the molecule junction conductance on the molecule conformation. It was shown that, for a series of seven biphenyl molecules with different ring substitutions that alter the twist angle of the molecule, the conductance for the series decreased with increasing the twist angle [20]. In another study the molecular conductance was measured by forming and breaking Au point contacts in the presence of amino-terminated molecules using modified scanning tunneling microscope (STM) [21]. It was found that the conductance of such an amino–Au bond does not vary significantly from junction to junction because of isotropy of the N lone pair to Au electronic coupling across the range of metal-molecule configurations. Such dependences are critical when considering development of devices for nanotechnological applications. Therefore, to understand the fundamental interface interactions and the various aspects of organized molecules on different surfaces via different anchoring groups is of utmost importance.

Another reason for the chemistry of gold surface to be extensively investigated is the important role that the surface of gold exhibits in catalysis [22, 23] and nanotechnology [24]. The covalent bond of gold is in the core of ligand-protected gold nanoparticles (NPs) and heterogeneous catalysis of organo-gold hybrids. Due to the importance of such systems, it is essential to extend the study of adsorption on gold surface to variety of molecules and linking groups. Gold surface adsorption was investigated so far mainly for thiol [25, 26], amine [27–29], phosphine [30, 31], and cyanide [24] head groups. We show here that self-assembly of alkanes with silane head groups gives Au–Si–Au sandwich systems that exhibits stable in plane polymerized monolayers. Consequently, this paper presents a new hybrid system sensitive to the coupling and therefore to charge and energy transfer through the organic molecules’ monolayer. Up to now, reports on organic molecules with silane head groups adsorbed to gold surfaces were limited and the nature of the corresponding bond type is still controversial.

The Si–Au bond was presented previously by several groups. Fundamental study performed in ultrahigh pressure proved the existence of the Si–Au bond [32]. The authors characterized the bond formation by reflection absorption infrared spectroscopy (RAIRS) and X-ray photoelectron spectroscopy (XPS). The RAIRS results demonstrated that the prominent Si–H bond seen for the solution of the octylsilane molecule was absent for the silane-based layers. Moreover, XPS data exhibited reduced Si 2p_3/2 binding energy at 99.8 eV supported the Si–Au bond. The bonding geometry was proposed to display Si atom that forms three covalent bonds to the gold surface. A different study demonstrating self-assembly from tetrahydrofuran solution of porphyrin oligo(phenyleneethynylene trimethylsilylethynyl) (P-OPE-silane) was carried out by Watcharinyanon et al [33]. They reported high-resolution XPS binding energy data for Si 2p_3/2 at 101.9 eV. The authors offered that the higher position of the Si binding energy peak was due to the fact that not all Si–CH₃ bonds were cleaved upon the film formation. Combining with their near-edge X-ray absorption fine structure spectroscopy results, the authors suggested that the self-assembled monolayer (SAM) had a poorly defined orientational order. An earlier work of self-assembled trichloro(octadecyl)silane (OTS) performed by Sabatani et al. [27, 34] exhibited electrochemical and reflection-absorption Fourier transform infrared measurements displayed well-defined crosslinked monolayer on gold electrode though not defect-free. In a further study, Olson et al. [35] showed that gold colloids were protected from exposure to solution-phase species upon surface modification by silane. Surface-enhanced Raman scattering (SERS) measurements exhibited enhancement of the substrate signal for immobilized gold colloids coated with well-packed highly ordered (n-octadecyl)trimethoxysilane with high reproducibility even when exposed to solutes. In their case it was stated that this monolayer eliminates the chemical or charge transfer contribution to the SERS mechanism due to the monolayer protection. In agreement with the previous results we present XPS results that demonstrate a reduced Si which we relate to Si–Au covalent bond. However, this reduced Si peak does not appear for all the studied molecules. To ensure that the Si–Au bond is universal and exists also for the specific studied molecules, we performed additional coupling measurements between gold NPs through the organic monolayer to a type II superconductor (serving as a sensitive sensor to charge or energy transfer). The results show that the superconductor properties are modified upon the adsorption of gold NPs on top of the molecular layers indicating that an efficient charge transfer mechanism exists through the Si–Au bond.

2. Materials and Methods

Self-assembly from a solution is a simple, fast, and reproducible method for producing organized monolayers suitable for molecular electronics. For our study we used three types of silane molecules (Figure 1) that were adsorbed to gold or Nb surfaces, each forming a different type of gold-molecule hybrid system. In all of the different cases the Si–Au bond formation was identified. One system SAM consists of 2-methylene-(1,3-propanediyl)bis(trichlorosilane) (MPdS) or 1,6-bis(trichlorosilyl)hexane (Hexa) molecules sandwiched between a gold or Nb surface and gold NPs chemically attached to them, as will be detailed below. The other system consists of OTS molecule with only one silane head group assembled on gold or Nb surface, providing no linking to the Au NPs deposited on top of them. The OTS molecule was chosen to monitor the Si–Au bond formation and to serve as a reference to the MPdS and Hexa that exhibit a bridge between two different Au surfaces. Chemisorbed monolayers of MPdS, Hexa, and OTS were formed by immersing evaporated gold (Cr : Au (10 : 100 nm)) or sputtered Nb films (on Al film on top of Si wafer) in diluted solutions of 1 mM organic molecules in bicyclohexyl solution or OTS in toluene solution for 2 min followed by sonication in toluene for 1 min. This procedure was repeated twice, followed by dipping the samples in 10 nm trisodium citrate hydrated gold solution for 24 hours or in the case of Hexa dipped in dodecanethiol functionalized gold nanoparticles in toluene. The samples were then washed with water or toluene and dried by nitrogen. The reactions were carried out under nitrogen environment, and the solvents chosen were anhydrous. The resulting SAMs were characterized by XPS, contact angle measurements, scanning electron microscopy (SEM), Woallam alpha-SE ellipsometry, and scanning tunneling microscopy (STM). STM tunneling spectra were collected for the systems that were lacking the XPS contact confirmation. Finally, measurements of V-I characteristic of a Nb superconducting film coupled by the Si–Au bond to gold NPs demonstrate enhancement of the critical current, implying charge coupling between the Au dots and the Nb film.

(a)

(b)

(c)

The XPS measurements were performed with a Kratos AXIS Ultra X-ray photoelectron spectrometer (Kratos Analytical Ltd., Manchester, UK). Spectra were acquired using the Al- monochromatic X-ray source (1,486.7 eV). Sample take-off angle was 90° (relative to the analyzer). The vacuum pressure in the analyzing chamber maintained to Torr. High-resolution XPS spectra were collected for C 1s, O 1s, Si 2p, and Au 4f peaks with pass energy 20 eV and 0.1 eV stepsize. The XPS binding energies were calibrated with respect to the peak position of the C 1s peak as 285.0 eV. Data analyses were done using the Kratos Vision data reducing processing software (Kratos Analytical Ltd.) and Casa XPS (Casa Software Ltd.). From the results C 1s (I) characteristic binding energy of 285.0 eV is corresponding to the hydrocarbon chains (CH_x) of the SAMs. In addition, two other peaks C 1s (II) and C 1s (III) around 286.6 eV and 289.7 eV (for Au substrate) appear at higher binding energy indicating the exposure to air. The peaks are related to C–O bonds and C=O probably coming from oxidation. The monolayers’ extra peak appears only for the C–O bond, at 286.6 eV. This suggests less oxidation of the samples which correlates with keeping the samples under nitrogen.

Using the XPS measurements, it is possible to calculate the thickness of the assembled layers. We have done so using the standard attenuation relations of the photoelectrons emerging from different sample depths. The thickness calculation is based on the Briggs et al. method and others [36–38].

For the Au substrate, the overlay thickness (nm) expressed as where and are the area intensities (area percentages) of Au and the overlayer peaks, respectively, (then are the intensities for carbon, oxygen, and silicon peaks), is the take-off angle (in our case ), and and are the volume densities. The inelastic mean free paths (IMFPs) parameters for the overlayer and for the substrate were assumed as 3.3 nm and 2.5 nm, respectively [36].

In addition to the XPS results, thickness measurements were performed also by ellipsometry. It was determined by the Cauchy model ( and , as these are good default values for many organic films).

3. Results and Discussions

The first different between the molecules types is reflected in the durability towards attempts to removed the adsorbed gold NPs. Thoroughly washing the MPdS samples with acetone, ethanol, and distilled water (DW) under sonication and hot toluene did not remove the gold NPs, as seen by SEM images (taken using Serion from FEI) presented in Figure 2. In contrast, Au NPs deposited on OTS were easily washed out.

(a)

(b)

The XPS results for MPdS, Hexa, and OTS SAMs on Au substrate are summarized in Table 1. Based on our results and previous studies by Sabatani et al. [34], it is realistic to assume that the SiCl₃ goes through oxidation to Si(OH)₃ and then chemisorbed to the surface while presenting a stable polymerized in plane monolayer having Si–O–Si groups with defects in the monolayer as evident by Si–OH free groups. Focusing on the different Si bonds, we find three types of bonds, two oxidized Si: Si–O, Si–OH, and one reduced Si. We show that, for the Hexa and OTS monolayers, the results exhibit reduced Si that is argued as the Si–Au bond (as no other reasonable bond is found in that specific energy). However, for the MPdS monolayer, we find only oxidized Si.

For the Hexa and OTS monolayers, we find a reduced Si 2p (I) peak: at 101.8 eV for the OTS (Figure 3(a)) and at 101.5 eV (Figure 3(b)) for the Hexa (the Si⁰ doublet is found at 99.2 eV and 99.8 eV binding energies). The results suggest that this Si exhibits Si–Au bond keeping in mind the monolayer remained on the surface also after sonication in toluene. Comparing it to the OTS bulk sample (adding repeatedly the organic molecule solution and drying under nitrogen stream on top of the gold surface) demonstrating Si 2p (I) at 102.6 eV, it seems that the Si–Au binding energy peak is missing. This indicates that the OTS and Hexa monolayers exhibit Si–Au bond in a good agreement to previous study that presented reduced Si peak at 101.9 eV [33]. The Hexa monolayer exhibits also an oxidized Si 2p (II) at 102.7 eV. It is reasonable to assume that the organic assembly appears as in-plane polymerized monolayer composed of Si–O–Si bridges between the molecules [39], as the silane chloride exchanges the chloride ions by hydroxyl groups to have a condensation of the Si–OH free groups.

(a)

(b)

(c)

In contrast, the MPdS monolayer shows two binding energy positions: for Si 2p (I) at 103 eV and for Si 2p (II) at 103.5 eV (Figure 3(c)). This involves two bond types. Both of the Si are oxidized as for the high binding energies. XPS and ellipsometry thickness measurements for the MPdS and OTS monolayers are given in Table 2. A comparison between the different thickness measurements and the estimated length for the MPdS molecule indicates for a multilayer assembly, assumed a continuous film. For rough calculation points it is composed of about seven layers cross-linked by Si–O–Si bonds. This may explain the absence of the reduced Si–Au bond in the XPS spectra as it is in a very small amount compared to the oxidized Si. The first Si 2p (I) is probably attributed to the Si–O-Si species. The second Si 2p (II) peak at 103.5 eV demonstrates the existence of Si–OH free groups which indicates that the crosslinking in plane is not complete. As illustrated by the XPS and ellipsometry thickness results, the OTS is arranged as one layer-thick monolayer, normal to the surface.

Nevertheless, as mentioned before, the Au NPs attached to the monolayer stay adherent to the layer also after roughly washing the samples under sonication in acetone and ethanol and dipping in hot toluene (see Figure 2). We also examined the bulk sample of MPdS prepared by adding repeatedly the organic molecule solution and drying under nitrogen stream on top of the gold surface. The results exhibit two oxidized Si bonds at 102.9 eV and 104.1 eV as in the monolayer. As mentioned before, the first corresponds to Si–O–Si bond and the second to Si–OH groups that did not cross-link to Si–O–Si bonds. The gold amount (atomic percent) reduced by 6 as a result of masking it by large amount of the organic molecule. In addition, we looked at Au take-off angle in order to examine whether it is possible to gain some information from the surface Au atoms that are bonded to the silane group. The results exhibit very stable 83.99−83.97 eV signals at angles between 0 and 60° meaning it is not possible to measure the oxidized Au as a result of the binding to the silane group. We believe that the difficulty is arising from the negligible amount of surface Au atoms that are oxidized compared to the bulk Au substrate.

Contact angle of the SAMs shows an angle of 70° for the MPdS SAM and 111° for the OTS. By the results of the OTS, it appears as hydrophobic SAM which indicates the formation of SAMs on the surface. Regarding the MPdS layer, the angle is too small to imply fully covered SAM surface. This may result from the discontinuous layer evidenced by the XPS results which demonstrates free Si–OH groups.

Comparing our results to previously reported results using different techniques of film formation, it was shown that Au–Si bond appears at 99.8 eV for tricoordinated Au, and 101.9 eV for lower coordinated Au [32, 33]. These results were explained by both theoretical and practical studies claiming that Au prefers dicoordinated bonding [34]. As was mentioned before, we believe that in our case it is realistic to assume that the SiCl₃ goes through oxidation to Si(OH)₃ and then chemisorbed to the surface while presenting a stable polymerized in-plane monolayer with defects as evident by the Si–OH free groups. This was supported by Sabatani et al. study [34] for the OTS measured by electrochemical and RAFTIR measurements. We find that the silane anchoring group is attached directly to the gold surface from the XPS results having reduced Si 2p.

The above explanation should also be true for the MPdS molecules; however, in this case we did not find a reduce Si 2p (I) peak. Therefore, to further examine whether covalent bond exists also for the MPdS molecule, we measured electrical coupling between the Au NPs and a superconductor through the organic layers. For this we used scanning tunneling spectroscopy and transport measurements. As detailed below, strong coupling and efficient charge transfer were found to exist between the Nb film and the Au NPs. This behavior is manifested both in our scanning tunneling spectroscopy measurements, monitoring a modified density of states, and in transport measurements, revealing significant changes in the critical currents. For these experiments, the Nb films were sputtered on a 100 nm aluminum film on silicon wafers. As detailed elsewhere [40], the transition temperature, , changed noticeably when using molecules having two silane end groups, whereas no change was observed for OTS, implying good electrical contact and thus chemical linking only in the former case. Tunneling spectra acquired using STM on the Au dots reveal consistently different behaviors for Au NPs that are chemically attached to Nb by MPdS compared to the Au NPs that are adsorbed to the Nb. Figure 4 presents tunneling I–V characteristics measured at 4.2 K on single Au NPs deposited either on top of MPdS (a) or OTS (b) monolayers self-assembled on Nb. The I-V curves acquired for MPdS (Figure 4(a)) show enhanced zero-bias conductance, which clearly manifests itself as a pronounced peak in the tunneling dI/dV versus V spectra (proportional to the local density of states) [41] presented in the inset. It is important to note that the existence of this zero-bias conductance peak was independent of the STM current and voltage settings (before disabling the feedback loop for spectrum acquisition) and disappeared above . As detailed in [41], this peak is associated with coupling between electronic states in the Nb and Au dots, resulting in modification. Such coupling points to the formation of Au–Si chemical bonding. In contrast to these results, the tunneling spectra measured on Au NPs deposited on OTS have never shown enhanced zero-bias conductance and rather exhibited single-electron charging effects (Coulomb blockade and staircase) [42], indicating weak electrical coupling to the Nb film, even though the thickness of the OTS layer is smaller than that of the MPdS (we note in passing that, far enough from the NPs, the spectra exhibited the superconducting gap of Nb). Figure 4(b) demonstrates this effect. The blue curve exhibits a region around zero bias where current was immeasurable (the Coulomb blockade), followed by a step-like feature that can be associated with the addition of a single electron to the dot (staircase). Upon changing the STM current-voltage setting, an effect similar to changing the gate voltage in single-electron tunneling devices [36, 42, 43], the Coulomb blockade, can be suppressed, resulting in finite conductance at zero bias. This effect is depicted by the red curve in Figure 4(b) and by its derivative, presented in the inset, in which the staircase (at higher-bias voltages) is more clearly evident. Although the I-V curves presented in Figure 4(b) do not exactly conform to the “text book case” single-electron tunneling characteristics excepted for metallic dots [43, 44], possibly due to the effect of the OTS molecules, the data clearly demonstrate that the coupling between the Au NPs and the Nb substrate is weak, indicating that they are only physisorbed on the OTS layer, in contrast to the case of MPdS. The STM results thus support our picture that MPdS indeed provides good covalent linking between the Au NPs and the substrate, allowing for charge transfer through the organic molecule.

(a)

(b)

Figure 4

Tunneling I-V characteristics at 4.2 K acquired on single 5 nm dia. Au NPs deposited on two different molecular layers self-assembled on a 150 nm superconducting Nb film. (a) On MPdS (di-Silane), showing enhanced zero-bias conductance that reflects strong electrical coupling to the Nb film. Inset: the corresponding dI/dV-V spectrum. (b) On OTS, showing single-electron tunneling effects that indicates weak electrical coupling. Two curves are presented, taken with different STM settings. The black curve shows a Coulomb blockade, which is removed in the red curve that exhibits a clear Coulomb staircase. Inset: derivative spectrum of the red curve. The voltage-current settings were (a) mV; nA, (b) mV; and −0.35 nA, for the black and red curves, respectively.

Lastly, when gold NPs are in proximity to a superconductor below , a proximity influence is expected to take place. This proximity effect is induced by the Andreev reflection [44] and therefore stimulates charge transfer through the organic molecules. Coupling our hybrid layers to a type II superconductor enables us to measure the fingerprint of this charge or energy transfer. With the change of the gold NP state, pinning or antipinning centers are induced to the system thus changing the superconductor critical current [45]. The superconductor in this case acts as a sensitive probe for charge or energy transfer through the organic matter. Indeed, we observed an increase in the critical current of a Nb superconducting film when gold NPs are deposited on top of the 4 nm thick MPdS layer, as demonstrated by Figure 5. This effect is quite remarkable, since the adsorbed MPdS monolayer alone destroys the film’s superconductivity due to surface effects [46] and the critical current goes to zero (blue curve), while, by adsorbing 10 nm dia. Au NPs, the critical current increases from 2 mA for the bare film (black curve) to around 8 mA (red curve) with the NPs. These results show that the strong crosslinking of the disilane molecules creates an efficient network for charge transfer even at distances which were assumed to be too large for tunneling effects.

Figure 5

V-I characteristics of 150 nm Nb superconductor film at 8 K, just below the critical temperature for superconductor transition. The black line presents data corresponding to clean Nb film, where the critical current (onset of voltage drop) is around 2 mA. The blue line was measured on the same Nb film after MPdS adsorption, showing that the critical current is suppressed. The red line presents the situation after 10 nm dia. gold NPs were deposited onto the MPdS, significantly enhancing the critical current to around 8 mA.

4. Conclusions

The present work demonstrates that, despite the gold nobility, it may be activated by silane groups to form highly stable and crosslinked organized monolayer even not fully covers the gold surface. Moreover, the organized monolayer networks maintain strong coupling to the substrate even at 3-4 nm distances. We believe that our results provide a paramount step towards understanding the chemical mechanism of the Au–Si bond formation. From the technological point of view, we have showed that silane-based SAMs are viable potential components for stable hybrid organic Au devices.

Acknowledgments

Special thanks are given to Dr. Nadav Katz from the Hebrew university who has grown the superconducting Nb clean films. The authors would like to acknowledge the support of the Peter Brojde Center for Innovative Engineering and Computer Science. O. Millo thanks support from the US-Israel BSF foundation, the German-Israel DIP program, and the Harry de Jur Chair in Applied Science.

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Copyright © 2012 Shira Yochelis et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

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