Thibault
Degousée
*a,
William G.
Neal
b,
Zach
Edwards
c,
Saumya
Singh
c,
Jotham
Selvarajah
a,
Teymour
Talha-Dean
a,
Matteo
Palma
b,
Bob C.
Schroeder
c and
Jan A.
Mol
*a
aDepartment of Physics and Astronomy, School of Chemical and Physical Sciences, Queen Mary University of London, Mile End Road, London, E1 4NS, UK. E-mail: t.degousee@qmul.ac.uk; j.mol@qmul.ac.uk
bDepartment of Chemistry, School of Chemical and Physical Sciences, Queen Mary University of London, Mile End Road, London, E1 4NS, UK
cDepartment of Chemistry, University College London, London, WC1H 0AJ, UK
First published on 10th November 2023
Arrays of gold nanoparticles (AuNP) covered with organic molecules have promising applications in biology, electronics, energy, and fundamental physics, among other areas. Here we consider different approaches to synthesise, coat the AuNP with a ligand and to induce their self-assembly into a network within one hour. Arrays formed from aqueous AuNP are stabilised with small ions or alkane chains of 8 to 18 carbons long as the assembly is induced. Alternatively, the AuNP are exchanged to an organic solvent and covered with alkanethiols or oleylamine before the array formation. Beside the length of the ligand, the network morphology and electronic properties are highly affected by the deposition conditions. By using a solid-state exchange strategy, we alternately replaced the ligand on the AuNP with long and short alkanethiols, for which the change of the network's resistance appears reversible. Using this ligand exchanged strategy, we replaced a commercially available alkanethiol with a bespoke naphthalene diimide, resulting in improved conductivity of the networks and their stability in air. Crucially, this simple, rapid, and versatile AuNP–organic network formation offers a platform to the scientific community to investigate the physical and chemical properties of complex molecules.
Recently, Martin et al. reported a modified Brust–Schiffrin method to synthesize 3–5 nm AuNP in 10 minutes.20,21 In this method, sodium borohydride (NaBH4) converts gold cations into gold atoms in less than 1 second, forming nanoparticles less than 3 nm in size – in the first instance – that slowly aggregate to form larger nanoparticles.21 The ratio of Au/NaBH4 is the main factor determining the AuNP diameter, so control of the synthesis conditions (pH, temperature, heating time) as in the Turkevich synthesis11,22,23 is not required. The small AuNP synthesized with NaBH4 can rapidly be exchanged to hexane without using surfactant, while at the same time, 1-dodecanethiol (DDT) fully covers the AuNP.20 The excess of ligand remains at the water/organic interface after the phase exchange, thus no rinsing step is necessary. The hexane colloidal solution can be deposited on the surface of a toluene where a floating monolayer of AuNP–DDT self-assembles as hexane evaporated.20,21 Although this self-assembly strategy has been able to cover a 3 inch wafer, only few works24 have used it for opto-electronic applications, possibly because the assembly is highly dependent on the size and charge of the AuNP,21 thus rendering the monolayer formation challenging. Other strategies to self-assemble AuNP from colloidal solutions can be used to complement the fast aqueous AuNP synthesis with NaBH4. Furthermore, the availability of nanoparticles in water or in an organic solvent presents the opportunity to use self-assembly methods for both types of colloidal solutions.
Film formation from aqueous colloidal AuNP can be done by two-phases (liquid–liquid or liquid–air) or three-phases (liquid–liquid–air, 3pD) deposition methods.17,25,26 The injection of ethanol at the water–organic interface destabilizes the AuNP and drives them to the water–organic interface. The film formation at the interface is then guided by the minimization of the free energy of the AuNP in the total system (liquid–liquid or liquid–liquid–air).25,26 Coating of the AuNP is achieved at the interface where a ligand in the organic phase attaches to the surface. Thus, the half-covered AuNP have a Janus-like morphology. Janus materials are a novel class of functional 2D materials with properties useful for opto-electronic, energy storage or catalytic applications.27
For organic colloidal AuNP solutions, the nanoparticles can be assembled at a water–air interface by casting the organic solution on a convex water surface.19,28–31 As the organic solvent evaporates, a monolayer assembles at the surface of water and can be transferred to a substrate using a polydimethylsiloxane (PDMS) stamp in a lift-off manner.
In this work, we used different techniques to self-assembled gold nanoparticles from aqueous or organic colloidal solutions into half-covered or fully covered AuNP–ligand arrays. By using those different assembling strategies, ligands consisting of small ions up to eighteen carbons long alkane chains can be grafted on the nanoparticles. We combined electrical and morphological analysis to study the effects of deposition conditions and ligand length on the AuNP–ligand arrays properties. Using a particular route, all necessary steps in the formation of a homogeneous and uniform AuNP–alkanethiolate monolayers (synthesis, coating, self-assembly and transfer to a substrate) can be done under one hour. Using a solid-state exchange strategy, the initial ligand can be replaced by another ligand in a reversible manner. Therefore, the AuNP–ligand arrays offer a rapid and reliable platform to study the properties of more complex molecules, which we demonstrate with a bespoke naphthalene diimide ligand.
The monolayer formation was induced by the addition of ethanol to the organic phase. We carefully added 75 μL of ethanol in 20–30 seconds on top of the organic phase. We repeated this step until a monolayer larger than 1 cm2 formed at the air/water interface (∼650 μL needed). Finally, the excess of organic and aqueous solutions was drained to land the monolayer on the substrate, and the film dried in air. Later, we refer to oleylamine as OA and the alkanethiols as Cx, where x is the number of carbons along their chain.
For the resistance measurement, we formed a monolayer on the convex water surface and covered 40 devices at a time using a rectangular stamp (1.5 × 0.3 cm). We then repeated this process using the same monolayer to cover the next 40 devices on the interdigitated electrodes (IDE) chip.
In the 3pD assembly (Fig. 1(b)), the aqueous AuNP are partially covered with a mixture of hexane–chloroform containing the ligand. The addition of ethanol destabilised the nanoparticles which move toward the water–organic interphase where they are coated by the ligand. It was shown that these nanoparticles acquire a Janus structure, with half of their surface covered by the ligand and the other half remaining stabilised by the reducing agent used in the synthesis. The coated AuNP formed islands that migrated to the water–air interface from the water–organic interface. At the water–air interface, the islands rearranged to form a large layer. As coating of the AuNP is done at the water–organic interface, the concentration of ligand in the organic phase is crucial to ensure enough adsorption of the linker on the AuNP. Monolayers formed with the theoretical concentration of C12 (n = 1), or ten times more (n = 10) had a blue and purple colour, respectively (Fig. 1(b)-top). AuNP monolayers formed with short alkanethiols (10 carbons or less),34 mercaptopropionate or citrate ions35 were of a blue colour comparable to our n = 1 sample, which indicates that the nanoparticles were closely packed. The electrical resistance of AuNP-C12 (n = 1) layer is comparable to that of AuNP stabilized by boron hydrate (Fig. S2, ESI†). Hence, using the theoretical concentration of ligand n = 1 is considered insufficient to coat the AuNP. The reflected colour shifted toward purple as the distance between nanoparticles increased,35,36 like what we observed for our n = 10 film (Fig. 1(b)). However, one can see that this n = 10 film is inhomogeneous and has thick edges. In what follows, all AuNP–ligand networks were formed with a ligand concentration of n = 5.
The absorption spectra of the 3pD arrays (Fig. 1(b)-bottom) show a single and broad band between 500–900 nm centred at 674 nm (3pD–AuNP–C8) and 670 nm (3pD–AuNP-C12). It is known that the SPR peak strongly depends on the interparticle distance and of the dielectric constant on the surrounding media.37 Our results are in good agreement with previous work on 3pD arrays where a broad absorption band blueshifts as the length of the ligand increases.25 However, as seen below, these broad SPR bands centred at ∼670 nm are indicative of stacking of AuNP and not monolayers.
We used a combination of AFM, SEM and TEM to characterise the films made by the 3pD. The AFM showed an average thickness of 8–12 nm, corresponding to 2–3 layers of AuNP (Fig. 2(a) and Fig. S3, ESI†). Whether assembled with a ligand or not, all 3pD layers are inhomogeneous with multiple defects and partial coverage of the substrate. We observed randomly distributed aggregates on the surface or forming long trails of ∼10 nanoparticles thick on some locations. We also noted partial reorganisation of the AuNP islands at the water–air interface, resulting in voids in the films (Fig. 2(a), (b) and Fig. S3, ESI†). Also, the edges of the islands overlap resulting in a thicker film in some locations. A closer look at the islands reveals a multitude of partially connected islets, some being monolayers and others stacks of multiple AuNP (Fig. 2(b)-bottom). These defects might have formed during the 3pD assembly, as seen in the Video S1 (ESI†) where the addition of ethanol destabilises the water–air and water–organic interfaces. Also, the draining step to land the films on the substrates might induce cracks in the films. This is shown in Fig. 1(b) where the hole at the top of the film is caused by the syringe, and the draining step induced a long crack of the entire film’ length.
For the 3pD assembly, the film inhomogeneity induced the broad distribution of the device resistance spanning several orders of magnitude (Fig. 2(c)). McCold et al. have shown that the network's quality is the key parameter in the charge transport characterization of AuNP–ligand arrays, where defects and voids in the films cause unreliable measurements.19 In our interdigitated electrode design, the resistance of one device corresponded to the equivalent resistance of the 100 sets of electrodes. Hence, defects or partial coverage of a set of electrode will affect the (equivalent) resistance of a device (Fig. S3, ESI†). Devices with resistance less than 10 kΩ have an ohmic behaviour, consistent with multiple layers of AuNP covering the electrodes.38 On the other hand, devices with the highest resistances showed a small charging effect under a bias larger than ±0.5 V. Although observed in monolayers of AuNP–C8,39 this charging effect could be induced partial covering of the electrodes as it is also visible in the AuNP layers without ligand (Fig. S4, ESI†). At room temperature, charge transport in metal nanoparticles arrays follows the sequential tunnelling mechanism.37,40 Hence, by increasing the length of the ligand, the distance between the AuNP increases, which translates to an increase of the resistance of the arrays. Although we noted a resistance increase with the length of the ligand (Fig. 2(c)), charge transport characterization in AuNP–ligand arrays assembled by the 3pD is challenging because of their inhomogeneous morphology.
Nevertheless, the 3pD formation enabled rapid Janus-like coating of AuNP with ligands of any length, which have applications in surface enhanced Raman scattering (SERS).25,41 While previously demonstrated by drop casting rhodamine 6G, we demonstrated the SERS capabilities of the 3pD arrays by transferring a 4 ± 1 nm film of poly(3-hexylthiophene) (P3HT) on top of the arrays (Fig. 2(d) and (e)). P3HT transferred to a plain silicon substrate showed a weak peak at 1440 cm−1. When transferred to a 3pD array, all vibration modes of P3HT can be clearly seen. Because the ligands are carbon chains, their main Raman bands overlap with those of P3HT in the 1200–1600 cm−1 region. Therefore, we used the C–S–C vibration of P3HT at 735 cm−1 to calculate the enhancement factor (EF) by:25
With ISERS and I0 the intensities of the Raman band of interest on the SERS layer and on silicon, respectively. The highest EF measured was for AuNP–C8 (1.6 × 103), followed by AuNP-C12 (6.3 × 102), AuNP–OA (3.1 × 102) and AuNP (1.6 × 102). These EF values are comparable with AuNP monolayers assembled by different strategies.41,42
We looked at the topography of the layers to assess the influence of the organic phase on the networks (Fig. 3 and Fig. S6, ESI†). On the top row, the AFM scan of an AuNP-C12 array formed from a colloidal hexane solution, presented a reticulated aspect. The AuNP-C12 seems to assemble into 2–3 μm wide ribbons around circular void areas. Although voids were predominant in the array, a continuous and homogeneous network is observed over the whole scan area. The film thickness was ∼5.4 nm, consistent with the AuNP diameter + ligand length, confirming the self-assembly of the nanoparticles into a 2D array (Fig. 3-middle). On the other hand, the voids induced an irregular coverage of the electrodes. An AFM scan of a set of IDE showed the long continuous network connecting the electrodes so as the inhomogeneous coverage of the gap between them (Fig. S6, ESI†). The reticulated topography was not observed when arrays were cast from a mixture of hexane–chloroform (Fig. 3-bottom and Fig. S6, ESI†). The 50 × 50 μm scan of AuNP-C12 array showed almost complete coverage of the area whereas the voids were greatly reduced. The horizontal profile line indicated similar thickness as for pure hexane monolayer but with homogeneous coverage over tens of micrometres. At the nanoscale, the AuNP were closely packed, forming an almost defect-free monolayer. Although we observed a short-range order over ∼100 nm, we did not observe long-range order in the 2D arrays (Fig. 3(b)). From the TEM images, the AuNP diameter was estimated at 4 ± 0.9 nm in all array-ligands cast with different organic phases. We estimated the length of the ligand between AuNP by subtracting the averaged diameter of the AuNP from the centre-to-centre distance between the AuNPs (Fig. S7, ESI†). Although the large error bars in our analysis do not allow precise measurement of the ligand's length, the trend suggests an increase of AuNP spacing with increasing length of the alkanethiol. Despite being longer than C12, the distance between AuNPs was comparable to or shorter than that observed in AuNP–OA monolayers. Contrary to alkanethiols, OA possesses an unsaturated carbon–carbon double bond forming an angle of 120° with the adjacent single carbon bond.25 As a result, OA allows for closer packing of adjacent AuNP when linear alkanethiols chains form interdigitated structures with the chains on the neighbouring AuNP.
At room temperature, all networks showed Ohmic behaviour under a bias of ±1 V; only a small charging effect was observed for devices in the high end of the resistance distribution (Fig. 3(c)). This charging effect could be due to greater voids in the monolayers resulting in partial coverage of the electrodes. The narrow distribution of device resistances is a consequence of the homogeneous morphology of the monolayers. Arrays cast from pure hexane had a higher average resistance than arrays cast from hexane–chloroform because of their reticulated morphology and partial coverage of the electrodes. Nonetheless, a clear increase of the devices resistance can be seen as the length of the ligand increased. For interdigitated electrodes and a film thickness smaller than the electrodes, the electrical conductivity (σ) of the arrays is given by:44
With L the spacing between the electrodes, N the number of pair of electrodes, l the overlap of the electrodes, t the thickness of the arrays and R its resistance. Using the average resistance of the arrays (Fig. 3(c)), the electrical conductivities of our AuNP–ligand monolayers are in excellent agreement with previous works (Table 1).
Ligand | Diameter (nm) | σ (S cm−1) | Ref. |
---|---|---|---|
C8SH | 4 ± 1 | 1.2 ± 0.4 × 10−7 (hexane) | This work |
4 ± 1 | 2.5 ± 1.1 × 10−6 (hexane–chloroform) | This work | |
1.2 | 1.8 × 0.8 × 10−5 | 45 | |
1.6 ± 0.8 | 9 × 10−6 | 46 | |
C12SH | 4 ± 1 | 7.2 ± 3.5 × 10−8 (hexane) | This work |
4 ± 1 | 2.2 ± 2.0 × 10−7 (hexane–chloroform) | This work | |
4.6 | 2 × 10−7 | 47 | |
4.8 ± 0.6 | 7.8 × 10−8 | 48 | |
1.2 | 2.3 ± 0.8 × 10−7 | 45 | |
1.6 ± 0.8 | 5 × 10−7 | 46 | |
C18NH2 | 4 ± 1 | 0.8 ± 1.4 × 10−8 (hexane) | This work |
4 ± 1 | 3.6 ± 1.5 × 10−9 (hexane) | This work |
The homogeneous and uniform monolayers can be used as platforms for ligand exchange with molecules that are unable to coat AuNP during phase exchange. Previous ligand exchanges in a solid state have been demonstrated with AuNP–C8 and single29 or dithiolated oligo(phenylene ethynylene) (OPE),28,29 oligo(phenylene vinylene) (OPV)49 or perylene tetracarboxylic diimide derivative with pyrroline moieties substituted at the bay positions.50 Here, we replaced C12 with butanethiol (C4), as we failed to coat and exchange the AuNP to hexane–chloroform with this short alkanethiol (Fig. 4). The replacement of C12 by C4 is possible because the space between the AuNP is large enough to accommodate C4. After immersion for 5 h in a 1 mM solution of butanethiol in acetone, the resistance of 80 devices decreased by ∼2 orders of magnitude to 106–108 Ω, consistent with the change of resistance observed with the length of the ligand. The resistance of the devices did not further change upon immersion for 24 h (Fig. 4). Furthermore, the ligand exchange process was reversible, as evidenced by the devices recovering their initial resistance when immersed in 1 mM of dodecanethiol in acetone for 24 hours. This reversible substitution of the organic linker implies that the morphology of the AuNP network is not affected by long immersion in acetone and remains comparable to the initial state when cast. Note that we did not optimize the concentration of ligand, solvent, temperature, or immersion time, all of which are known to affect the solid-state ligand exchange process.51,52
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Fig. 4 Resistance changes of an AuNP-C12 array when C12 is replaced by butanethiol (C4) and subsequently replaced by C12. The gap between the IDE for this sample was 1 μm. |
The solid-state ligand exchange process was also performed with a naphthalene diimide (NDI) derivative, namely 3-(7-(2-(octyldisulfaneyl)ethyl)-1,3,6,8-tetraoxo-3,6,7,8-tetrahydrobenzo[lmn][3,8]phenanthrolin-2(1H)-yl)propanoic acid (7). NDI compounds are known for their air stability which makes them promising n-type electronic materials.53 The detailed synthetic procedure for compound 7 can be found in the ESI† (Fig. S8–S11) and is summarised in Scheme 1. NDI derivative 7 was functionalised with both a disulfide group to facilitate anchoring to the AuNP,54 as well as a carboxylic acid group to enhance solubility in polar solvents. In addition, the polar carbocyclic acid groups facilitate hydrogen bonding between decorated AuNPs or alternatively promote dispersion in solution, especially when deprotonated (pH 8). Two chips of 80 devices were covered with a hexane–chloroform AuNP-C12 monolayer, one of them acting as a control sample.
Initially, the average resistance distribution of both AuNP-C12 monolayers was alike. After immersing one of the arrays for 4 hours in 1 mM of 7 in acetone, the average resistance of each device was reduced by half (Fig. S11, ESI†). After one week in air, the resistance distribution of the control sample spanned over seven orders of magnitude indicating degradation of the monolayer. On the other hand, the resistance distribution of the AuNP–7 layer remained nearly unchanged after one week in air. Furthermore, the UV-Vis spectroscopy of the AuNP-C12 layer before and after ligand exchange with 7 clearly showed the signature of the NDI core, thus confirming that C12 had been replaced (Fig. S11, ESI†). To further evaluate the ligand exchange and verify if it indeed took place via the formation of a chemical Au–S bond, we performed 1H-NMR experiments on the AuNP–7 and compound 7 (Fig. S12, ESI†). Comparing the two spectra, it becomes apparent that numerous new proton environments arise in the AuNP–7 spectrum, further evidence of the successful binding of 7 on the AuNP surface. The spectra can be roughly separated into two regions, downfield (9.0–7.0 ppm) and upfield (4.5–0.5 ppm). The downfield region reflects the aromatic proton environment and multiple new peaks with complex splitting patterns arise once 7 is bound to the AuNP surface. Similarly, a series of additional peaks were recorded for AuNP–7 further upfield in the spectrum resulting from the different chemical environments in the side chains of 7. It is unlikely that these changes are the result of chemical modifications to the structure of 7 when bound to gold, but rather reflect the presence of numerous chemical species bound to the AuNP resulting in a variety of distinct chemical environments.55 Specifically, we could expect dodecanethiolate from the original ligand shell, as well as octanethiolate and 2-(7-(2-carboxyethyl)-1,3,6,8-tetraoxo-3,6,7,8-tetrahydrobenzo[lmn][3,8] phenanthroline-2(1H)-yl)ethane-1-thiolate, the two products resulting from the dissociation of the disulfide bond in 7, to be present on the AuNP surface.
The family of NDI molecules is particularly interesting as multiple side chains or groups can be attached to the core, hence changing the physical and chemical properties of the molecule.56,57 This simple ligand exchange proves that our AuNP–ligand arrays can be used to study the properties of bespoke molecules.
Footnote |
† Electronic supplementary information (ESI) available. See DOI: https://doi.org/10.1039/d3tc01497e |
This journal is © The Royal Society of Chemistry 2023 |