Transparent and luminescent glasses of gold thiolate coordination polymers
Obtaining transparent glasses made of functional coordination polymers (CPs) represents a tremendous opportunity for optical applications. In this context, the first transparent and red-emissive glasses of gold thiolate CPs have been obtained by simply applying mechanical pressure to amorphous powders of CPs. The three gold-based CP glasses are composed of either thiophenolate [Au(SPh)] n , phenylmethanethiolate [Au(SMePh)] n or phenylethanethiolate [Au(SEtPh)] n . The presence of a longer alkyl chain between the thiolate and the phenyl ring led to the formation of glass with higher transparency. The glass transitions, measured by thermomechanical analysis (TMA), occurred at lower temperature for CPs with longer alkyl chains. In addition, all three gold thiolate glasses exhibit red emission at 93 K and one of them, [Au(SMePh)] n , remains luminescent even at room temperature. An in-depth structural study of the amorphous gold thiolates by XRD, PDF and EXAFS analysis showed that they are formed of disordered doubly interpenetrated helical chains. These d 10 metal-based compounds represent the first examples of transparent and luminescent CP glasses.
Introduction<!>Fabrication of transparent glasses<!>Samples characterization<!>Photoluminescent properties<!>PDF analyses
<p>Liquid, amorphous, and glass coordination polymers (CPs) and metal-organic frameworks (MOFs) have attracted great interest due to their mechanical properties, which are halfway between those of brittle inorganic glasses and ductile organic polymers. 1 The association of the intrinsic physical properties of CPs, such as porosity, conductivity, magnetism or photoluminescence, with the possibility of shaping the materials as transparent glasses opens up new areas of applications in display and communication technologies. 2 Still, a limited number of glasses of CPs have shown potential applications for molecule trapping and conservation 3 and for ion transport in energy devices. 4 Today, all the glass CPs reported in the literature are obtained via a two-step route that requires the synthesis of a crystalline CP, followed by ball milling and pressurization, 5 heating or melt quenching 6 of the crystalline phase. 1b Most of the melt quenching approaches require the use of high temperature (between 400 and 600 C) in the case of zeolitic imidazolate frameworks (ZIFs). 1a,7 Moreover, the formation of large scale and transparent glasses of CPs is still challenging because of the difficulty in amorphizing polycrystalline phases and the harsh conditions that are required from an amorphous phase, such as 4 GPa at 70 C for 2 hours. 8 Some of us reported a simple one-step synthesis of an amorphous gold(I) thiophenolate CP, which undergoes a solid state amorphous-to-crystalline phase change upon heating. 9 The rst advantage of the d 10 coinage metal chalcogenolates (MOCs) is their strong covalent so-so bonds between the d 10 coinage metal (Cu, Ag, or Au) and the chalcogenolate (SR, SeR, or TeR), leading to CPs with good thermal and chemical stabilities, 10 as opposed to the hard-hard interactions between oxygen atoms (carboxylates or phosphonates) and high oxidation state metals. 11 This strong interaction and the m 2 -bridging mode of the thiolate to Au(I) give access to wider bonding geometries, providing exibility 10b and favoring phase changes. The second benet of the coinage MOCs is their ability to exhibit various photoluminescent properties due to the presence of d 10 coinage metals and some metallophilic interactions. 11 The peculiar optical properties displayed by anisotropic 1D and 2D MOCs have demonstrated their great potential for temperature sensing and optoelectronic applications. 12 They are thus a good alternative to replace the lanthanide-based luminescent materials considered as critical elements and even banned by the European Union. 13 The formation of new CP glasses is based on our previous study on [Au(SPh)] n . 9 In its crystalline form, obtained under hydrothermal conditions, [Au(SPh)] n displays a 1D structure, consisting of two interpenetrated spiral chains of -Au-S-Au-Sthat form a double helix (Fig. 1). 9 The self-assembly is governed by aurophilic Au/Au and C-H/p interchain interactions. This crystalline phase is red emissive at room temperature originating from a Ligand-to-Metal-Metal Charge Transfer (LMMCT) and the radiative process implies the participation of the aurophilic interactions. On the other hand, under mild synthetic conditions, the [Au(SPh)] n amorphous phase is obtained and a solid state amorphous-to-crystalline phase change occurs upon heating. Then, an in-depth study of the amorphous phase allowed us to highlight the possibility of transparent glass formation via a simple mechanical pressurization. This study was further extended to two other gold thiolates based on methylthiophenolate and ethylthiophenolate ligands (Scheme 1).</p><p>Here we present the rst examples of the formation of transparent and luminescent glasses upon a so mechanical pressurization of 1D amorphous gold thiolate CPs. Previous reports have only shown the possibility to form transparent and luminescent glasses with molecular lanthanide complexes. 14 In addition, thermomechanical analysis (TMA) has been used for the rst time for CP glasses to determine the glass transitions more precisely than in the case of Differential Scanning Calorimetry (DSC). In-depth structural characterization on the glass phases allowed us to describe a double-helix model.</p><!><p>The amorphous gold thiolate compounds were synthesized directly from a redox reaction between HAuCl 4 and an excess of the corresponding thiol molecules, thiophenol (HSPh), phenylmethanethiol (HSMePh) and phenylethanethiol (HSEtPh) in methanol, at room temperate or 60 C. These conditions are similar to the rst step synthesis of gold thiolate clusters. 15 Then, 50 mg of the obtained pale yellow and white amorphous powders, a-[Au(SR)] n , 1a, 2a and 3a for a-[Au(SPh)] n , a-[Au(SMePh)] n and a-[Au(SEtPh)] n , can be mechanically pressed at 10 tons under ambient atmospheric conditions to form transparent glasses, g-[Au(SR)] n , 1g, 2g and 3g for g-[Au(SPh)] n , g-[Au(SMePh)] n and g-[Au(SEtPh)] n , respectively (Fig. 2a-f). The thicknesses of these pellets are 140, 155 and 156 mm, respectively. While 1g is a yellow translucent glass, 2g and 3g are yellow and colorless transparent glasses. Thus, the gain in the color and the transparency of the vitreous pellets appears to be related to the addition of the -CH 2motif between the thiolate and phenyl functionalities and the exibility of the ligands.</p><p>The transmittance curves of the three g-[Au(SR)] n pellets show that 1g and 2g start to let the light go through from 430 nm and reach a maximum transmittance of 19% at 850 nm, while 3g starts to be transparent from 400 nm and reaches a maximum transmittance of 26% at 850 nm (Fig. S1 †). This analysis proves the better transparency of 3g compared to the two other samples. The relatively low percentage of transmittance, compared to that of silica glass, which reaches 100%, can be explained by the reection at the interfaces and the scattering by defects at the microscale. In addition, when thicker pellets are prepared with 100 mg, the thicknesses are 295, 300 and 316 mm for 1g to 3g and the resulting transmittance is quasi null. A solution to increase the transparency would be to increase the applied pressure.</p><p>From powder X-ray diffraction (PXRD), the three powder and pellet samples exhibit patterns with similar amorphous features (Fig. S2-S4 †). Aer pressing the powder, no phase changes are observed in the PXRD patterns as has been seen for some Au(I) complexes upon mechanical grinding. 16 The PXRD patterns (Fig. 3) show a sharp peak at low angle and a broad feature at 2q between 20 and 40 characteristic of poorly crystallized (or noncrystalline) materials that will be called amorphous here. Similarly, the Pair Distribution Functions (PDFs) of the powder and pellet forms of [Au(SR)] n do not show any difference, meaning that there is no change of the local or average structure when the powder is pressed (Fig. S5 †). In-depth studies of the PDF data will be discussed in the next part.</p><p>Thus, the only evident change is the morphological aspect of the samples. The macroscopic texture of the powder and glass forms of [Au(SR)] n solids was studied by SEM (Fig. 2g-o). As powders, the compounds form large aggregates of around 500 nm for 1a (Fig. 2g), and well-dened spherical nanoparticles of around 80 and 50 nm for 2a (Fig. 2j) and 3a (Fig. 2m), respectively. Thus, the formation of smaller particles in the case of [Au(SEtPh)] n may also be related to the better transparency of the glass. The SEM images of g-[Au(SR)] n show a morphology characteristic of glass materials: at surfaces with clear cracks and the absence of grain boundaries.</p><!><p>The presence of thiolates in the amorphous samples was conrmed by FT-IR spectroscopy exhibiting well dened bands of aromatic rings and alkane functionalities (Fig. S6 †). From the thermogravimetric analysis (TGA) carried out in air, the weight loss of the amorphous phases corresponds well to the expected 1 : 1 ratio of ligand : gold (Fig. S7 †). These experiments also show that 1a, 2a and 3a start to decompose at 240, 184 and 225 C, respectively (Table S1 †). Thus 2a is the less thermally stable compound as a powder. For 1g, 2g and 3g, the decomposition begins at 225, 185 and 185 C, meaning that the two more stable compounds, 1 and 3, become less thermally stable in their glassy state, while 2 exhibits a constant thermal stability in the powdery and glassy forms.</p><p>In the Differential Scanning Calorimetry (DSC) curves, before their decomposition, 1a and 3a exhibit an intense exothermic peak of crystallization (T C ) at 220 and 140 C, respectively (Fig. 4a, S8, S9 and Table S1 †). The solid state amorphous-tocrystalline phase change of [Au(SPh)] n from 1a to 1c has been reported. 9 In the case of 3a, the formation of a crystalline phase has also been observed (Fig. S10 †), while, for 2a, due to its lower thermal stability, no crystallization peak is observed before its decomposition (Fig. S11 †).</p><p>The assignments of the glass transition temperature (T g ) have rst been made by DSC on the three 1a, 2a and 3a samples (Fig. 4a). The T g of 1a and 2a, when heated at 10 C min À1 , cannot be determined with accuracy because of the slight increase of the DSC signals due to an expansion of the samples during the glass transition. For 3a the glass transition is more pronounced and the onset T g is observed at 56 C (Fig. S12 †). Additional thermomechanical analysis (TMA) has been performed on the pellet samples (glass). Indeed, the TMA technique is better suited for T g determination than DSC due to its high sensitivity to volume changes during thermal expansion (the material becomes less rigid in the transition from glassy to rubbery behavior). Thus, TMA measures material deformations under controlled conditions of force (here in compression mode at 0.01 or 0.1 N), temperature (25 to 120 C) and heating rate (3 or 5 C min À1 ). Fig. 4b shows clear T g values for the three pellets of g-[Au(SR)] n samples that correspond to the slope change of the dimension change curve for a heating rate of  3 C min À1 and a force of 0.1 N. The onsets of the T g decrease from 72 to 57 and 51 C with the increase of the alkyl chain in the ligand (Fig. S13-S15 †). When a faster heating rate is used at the same applied force (0.1 N), the onset of the T g is shied towards higher temperatures for 1g (79 C) and 2g (68 C), while the one for 3g (48 C) does not change as much (Fig. S16-S18 †). Then a weaker force was applied (0.01 N) at 3 C min À1 (Fig. S16-S18 †). The dimension change is less important at this force for 1g (1%) and 2g (3%), but it is 10% for 3g with a T g onset that is well-dened at 53 C. This clearly shows that amorphous [Au(SEtPh)] n is more suitable to undergo the glass transition and it justies also that the corresponding glass is the most transparent one.</p><p>The gradual improvement of transparency and the lowering of glass transition temperatures from 1a to 3a imply that the glass transitions are governed by the exibility of the ligand associated with the length increase of the aliphatic chain. Indeed, a more exible backbone (from 1a to 3a) induces more movements, T g at lower temperature and better transparency. These three compounds still have short chains, and each of the ligands can be considered as discrete entities with their own environment and behavior. 17 In contrast, crystalline layered copper, 18 silver 17,19 and gold 20 n-alkanethiolates are known to melt due to the presence of long chains, while the strong M-S bonds remain intact.</p><p>From the PXRD, the d spacing of the rst peak in Fig. 3 corresponds to the distance between the helical chains. The increased distances of 1.14, 1.23 and 1.31 nm for 1a, 2a and 3a, respectively, can be correlated with the increasing length of the ligands with stacking of the organic moieties without interpenetration of the aromatic rings (Fig. S19 †).</p><!><p>Bearing in mind that the crystalline [Au(SPh)] n CP (1c) is a luminescent material, the photophysical properties of the amorphous phases have been studied as a function of the temperature. As mentioned before, 1a is non-emissive at room temperature. However, it becomes emissive below 250 K, and the intensity of emission increases with lowering the temperature (Fig. 5a, S20 and S21 †). This intensication is due to the enhanced rigidity of the network and the faster intersystem crossing process at low temperature, reducing the energy loss by non-radiative decay. The position of the maximum of emission is slightly red shied from 675 nm for 1c (l ex ¼ 320 nm) to 690 nm for 1a (l ex ¼ 412 nm) (Fig. S22 †). In addition, the emission peak at 93 K of 1a is wider than the one of 1c (the width at half maximum is 63 nm (1359 cm À1 ) vs. 165 nm (3371 cm À1 ), respectively). The Stokes shi is different too -9780 and 16 435 cm À1 for 1a and 1c, respectively (Table S2 †). The lifetime decay at 93 K of 1c has one major contribution of 8.4 ms (98%), while 1a exhibits a long decay of 9.9 ms (71%) and a shorter one of 0.1 ms (29%) (Fig. S23 and Table S3 †). So, the large Stokes shi and microsecond lifetime decays support the presence of a phosphorescence process in 1a that can be close to that in 1c. However, the less intense emission of 1a associated with two lifetime decays can be explained by (i) the trapping of energy on the defects that are omnipresent in amorphous materials and/or (ii) a reduced number of aurophilic interactions, that can be related to the aggregation induced emission observed for some Au(I) thiolate clusters and complexes. 21 Similarly to 1a, 3a is not luminescent at room temperature, while 2a is weakly red emissive (Fig. S24 †). The previous analyses carried out show that the three amorphous samples are quite similar; a tentative explanation for the presence of the emission of 2a at RT could be related to some different electronic transitions induced by the ligand. At 93 K, 2a and 3a possess a close red emission centered at 675 nm and an important Stokes shi > 12 000 cm À1 (Fig. 5a and S25, and Table S2 †). The two-component lifetime decays of 2a are 0.8 ms (88%) and 73 ms (12%) and those of 3a are 7.7 ms (82%) and 0.2 ms (18%), indicating phosphorescence mechanisms (Table S3 and Fig. S26 †). The shi of the positions of the excitation peak centered at 412, 372 and 340 nm for the three samples from 1a to 3a can be explained by the different distributions of the electronic density of the HOMO level on the different organic ligands (Fig. 5a).</p><p>Aer the pelletizing process, the vitreous samples retain their photophysical properties (Fig. 5b, S23-S25, and S27-S29, and Tables S2 and S3 †), which conrms that there is no structural modication upon pressurization. In addition, due to the stability of gold thiolate coordination polymers, 10b 2g glass remains luminescent at RT aer 1.5 years storage under ambient storage conditions (Fig. S30 †). Pellet 2g is the rst example of a transparent and RT luminescent glass made of pure coordination polymers (Fig. 5b).</p><p>In order to gain in-depth structural information to try to explain the different T g and luminescent properties, Pair Distribution Function (PDF) and Extended X-ray Absorption Fine Structure (EXAFS) analyses were carried out.</p><!><p>The structural characterization of these samples in reciprocal space is greatly challenged due to the poor crystallinity which results in broad features in the PXRD patterns. To overcome this difficulty, we analyzed the PDF obtained by total scattering measurements. The PDF represents the probability of nding a pair of atoms at a given distance r in the sample, and yields structural information in direct space on the local atomic arrangement. The PDF was shown to provide important information on the structure of complex non-crystalline compounds such as amorphous inorganic zeolites 22 and MOFs, 23 which is difficult to obtain by other techniques. One of the main targets here is to distinguish if the amorphous phases are built of continuous molecular networks or of isolated complexes. The PDF of the known crystalline [Au(SPh)] n (1c) is rst reported and compared to that of its amorphous counterpart (1a). Finally, the PDFs of 2a and 3a are compared to that of 1a.</p><p>The PDF G(r) and reduced structure functions F(Q) 24 of samples 1c and 1a are shown in Fig. 6a and S31. † A qualitative inspection of Fig. 6a rst indicates that sample 1c is crystalline with well-dened Bragg peaks. PDF oscillations extend over 250 Å, indicating that the size of the structure coherence domains exceeds this value. The observed decay of the PDF with r is essentially due to the effect of experimental spatial resolution. For 1a the Bragg peaks in F(Q) are replaced by broad oscillations, characteristic of amorphous or disordered materials. Due to the large contrast in scattering power between the organic molecule and metal atoms, the diffraction and PDF signals are strongly dominated by the scattering of gold and to a lesser extent sulfur atoms. In fact, as can be seen in Fig. S32, † most features of the PDF correspond to the contribution of Au-Au atomic pairs, with only the rst peak at 2.3 Å being solely due to Au-S pairs. In the PDFs of 1a and 1c, this rst peak is almost identical for the two samples, indicating that Au-S bond lengths are not modied between the crystalline and amorphous compounds (Fig. S33 and Table S4 †). At longer distances between 3 and 9 Å, the relatively well-dened peaks are essentially due to Au-Au distances of gold atoms bridged by a thiolate molecule and the aurophilic interactions between the chains. Despite some similarities, one can observe marked differences between the PDFs of 1a and 1c in this distance range, implying some structural reorganization on the local scale (Fig. S33 †). At longer distances, these well-dened oscillations in 1c are replaced by much broader and roughly periodic oscillations in 1a that progressively decrease in amplitude up about 50 Å (Fig. 6a). Their approximate period of $11.5 Å is close to the distance between the double helix chains in the crystalline compound, suggesting that these chains conserve some positional correlation in the amorphous phase up to several tens of angstroms. On the other hand, the structural coherence along them is much shorter (up to 9 Å) (Fig. S33 and Table S4 †). In order to verify that the crystal structure of 1c, determined by standard crystallographic techniques, is also valid at the local scale, we have performed a renement of its PDF using MolPDF soware 25 and of complementary Au L 3 edge EXAFS data providing ne details of the partial pair distribution function of atoms surrounding gold. The MolPDF soware allows applying restraints on bond distances and angles, which is necessary to reduce the number of rened parameters while maintaining the conguration of the molecules within the structure, especially in the presence of heavy atoms such as gold. The crystallographic structure of 1c in space group C2/c was used as a starting model for the renement, disregarding the hydrogen atoms. 9 The rst neighbor C-C distances and the C-C-C and C-C-S angles were constrained to their starting values. Atoms of the same elements had equal isotropic thermal parameters, which were varied as well as the atomic positions, cell parameters, scale factor and a sharpening factor. The last constraint was applied to the restrained C-S and C-C bonds and allows us to consider the difference between the Debye-Waller factor of intramolecular and other distances. The renement was carried out between 1.7 and 30.0 Å. The results are reported in Table S4 † and the renement plot in Fig. 6b, which shows a quite satisfactory agreement for this type of so material with distances between the rened positions and the original ones from ref. 9 not exceeding 0.2 Å for Au and S atoms. The main differences consist of relatively small rotations of the molecules as seen in Fig. 6c, which are difficult to conrm given the weak contribution of the molecules to the rened patterns both for the present PDF renement and the original Rietveld renement of ref. 9. However, the present PDF analysis conrms the validity of the crystallographic structure at the local scale.</p><p>The rened structure of 1c was used as a starting point for the renement of the structural model of the amorphous phase 1a keeping the C2/c monoclinic symmetry and applying the same type of structure constraints as for sample 1c. The renement was carried out between 1.7 and 12.0 Å, which only corresponds to distances within a double helix chain. The results of the renement are given in Fig. 6d and Table S4. † Although the agreement is poorer than in the case of the crystalline sample, the t reproduces reasonably well all Au-S and Au-Au distance peaks up to $9 Å, indicating the preservation of the double helix chain coherence up to two unit cells along the b axis on average. This length corresponds to six gold atoms along one helix (Fig. 6e). One can propose that the Au-S covalent bonds would tend to preserve the structural coherence along the chains while disorder would be introduced through displacements/rotations between the molecules weakly linked by parallel p interactions. The largest local structure modication with respect to the crystalline phase is a displacement of $0.3 Å of both Au atoms in the (b,c) plane leading to a decrease of the double helix distortion. The difference between the longer Au2-Au2 distances (3.81(3) Å) and the shorter Au1-Au1 ones (3.27(4) Å) for sample 1a is much smaller than for sample 1c (4.16(1) Å and 3.36(1) Å, respectively) (Fig. 6f). The slight decrease of the Au-Au distances in 1a, that induces stronger aurophilic interactions, does not correlate with the less intense photoemission of 1a compared to 1c. 26 So, as already stated in the photoluminescent analysis part, the less effective photoemission of 1a may be due to (i) the trapping of energy on the defects and/or (ii) a reduced number of aurophilic interactions.</p><p>The PDF data of the amorphous 1a phase were also rened with a model consisting of tetramer rings, since gold thiolates are known to form cyclic structures with bulky ligands, 27 and several tetrameric oligomers, [Au(SR)] 4 , have been reported as intermediates in the formation or fragmentation of gold thiolate clusters. 28 The distorted 8-membered ring model was built based on the rened double-helix model of 1c, by the displacement of half of the thiophenolate molecules by 0.5 f. u. along the b-axis (Fig. S34 †). In the tetrameric ring and doublehelix models, the atomic positions of gold atoms are preserved. The main difference is the more acute S-Au-S angles of the tetrameric ring -104 and 140 (vs. 159 and 166 , see Table S5 †). Despite the fact that the nearest Au-S and Au-Au distances corresponding to the contacts inside the ring are well described by this model, it fails to reproduce longer correlations at 4.5 and 7.7 Å corresponding to Au-Au contacts between neighboring tetramers (Fig. S35 and S36 †) and the renement yields poorer agreement factors.</p><p>Therefore, our renements indicate that for the amorphous sample 1a, the connectivity of Au-S corresponds to double helices with a coherence length of $9 Å and not to tetrameric species. This hypothesis is supported by the insolubility of 1a, since small oligomeric molecules are likely to be soluble. 29 However, the presence of tetrameric motif defects intercalated in a double helix could occur, which would reduce the coherence length.</p><p>All three 1a, 2a and 3a amorphous compounds show PDFs with similar features (Fig. S37 †). The peaks corresponding to the rst Au-S and Au-Au are positioned at 2.3 at 3.5 Å for all three materials. Thus, one can propose that these three amorphous phases are formed with a disordered double-helix Au(I)-S core. At long r, only broad features are observed, which are damped out to disappear at around 50 Å (Fig. S37b †). Similarly to 1a, this can be interpreted for 2a and 3a as due to the positional correlations between the double helices. Expectedly, the shi of these broad features to longer distances is related to the longer thiolate ligands in 2a and 3a.</p><p>Au-L 3 XAS study of crystalline (1c) and amorphous (1a) [Au(SPh)] n Next, the Au-L 3 EXAFS providing ne details of the partial pair distribution functions involving the absorber, i.e. Au, is introduced. As well as for PDF analysis, the interpretation of EXAFS does not make any assumption on the symmetry and periodicity of the structure, and the quantitative analysis of EXAFS provides accurate interatomic distances, coordination number and mean-square displacements for the nearest shells.</p><p>The comparison between the c(k) and FT c(R) signals of 1a and 1c is given in Fig. 7, where the peaks corresponding to the three Au-S nearest paths have been highlighted. The loss of intensity in these peaks observed on the amorphous sample is correlated with the increased atomic disorder in 1a. This observation is supported by the increased mean-square displacement (s 2 ) rened values reported in Table S6. † Table S6 † introduces the rened distances (R) and mean square deviations in distance (s 2 ) for the ve innermost shells involving the coordinating species Au and S as well as the coordination numbers (N) of the rst nearest S neighbor. Note that the contribution of the Au-C and Au-H partial pair distribution functions to the EXAFS signal is minor (the Au-C estimated contribution is <10% that of Au-S) and these paths were not included in the renement.</p><p>The EXAFS data of 1c were rened based on its known crystallographic structure, giving a good t to the data (Fig. 7), and interatomic distances in good agreement with those from the PDF (Tables S2 and S6 †). The EXAFS data of 1a were also rened with the double-helix model, which also gave an excellent t to the data and rened distances in good agreement with the PDF, albeit with a coordination number for the rst S neighbor of only 1.5(1), lower than the expected value of 2. The lower number of S neighbors could be an indication of some breaking of the chains in the amorphous 1a. A coherence length of six Au atoms along one helix chain as found by PDF analysis gives eight Au atoms with coordination number (CN) 2 and four with CN 1 providing an average coordination number of 1.7 close to the value rened by EXAFS. Unfortunately, the second model, the tetramer ring model, where only the distribution of the rst nearest neighbors is known, could not be used to t the EXAFS. Unlike in PDF, where peak positions are directly translated into interatomic distances, in EXAFS, the peak position also depends on the phase amplitude. Thus, when tting EXAFS data a cluster of $9 Å around the absorber atom is considered in order to compute reasonably well the muffin tin potentials. A complex structural modelling approach based on the Reverse Monte Carlo Modelling of combined datasets is currently under investigation, which could allow for a full structural description in this disordered system.</p><p>The near-edge region of the spectra (XANES), giving a projection of the unoccupied density of states, was also evaluated. In 5d transition metals, 2p 3/2 / 5d 5/2 , 5d 3/2 dipole allowed transitions are responsible for the near-edge structure at the L 3 absorption edge. Since this study deals with Au(I) compounds with electronic conguration [5d 10 6s 0 ], a low intensity white line, similar to the one recorded for a metallic Au foil standard (Fig. S38 †), has been observed, as expected.</p><p>A slight increase in intensity of the white line can be observed from the comparison between 1c and 1a XANES in Fig. S39. † With both compounds having the same oxidation state of Au and thiolate ligands, this difference is attributed to the different environments around the Au(I) and S-Au-S bonding geometries introduced earlier. We have applied rstprinciples calculations based on density functional theory optimized (FDMNES) for XAS analysis to compute the XANES region of the rened 1c and 1a models to compare with the experimental data in Fig. 8 and S39. † 30 In the XANES region, the photoelectron interacts with a large number of atoms: a cluster of 7.5 Å radius, taking into account interaction with 116 atoms, was considered in our calculations. Thus, we have used the agreement between the simulated and experimental data to measure the veracity of the proposed models for 1a. Note that the double-helix model for crystalline Au-thiolate successfully reproduces the experimental XANES, validating this simulation approach (Fig. 8).</p><p>As for PDF analysis, the double-helix model provides a better description of the overall shape of the XANES spectra than a block model. In the former, the rst peak at 7.92 eV aer the edge and the valley at 80 eV are accurately reproduced, while these features are absent for the calculated tetramer ring model spectra.</p>