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Near Field Enhancement Localization on Plasmonic Gratings Raymond Gillibert, Mitradeep Sarkar, Julien Moreau, Mondher Besbes, Michael Canva, and Marc Lamy de la Chapelle J. Phys. Chem. C, Just Accepted Manuscript • DOI: 10.1021/acs.jpcc.6b09717 • Publication Date (Web): 14 Nov 2016 Downloaded from http://pubs.acs.org on November 16, 2016

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The Journal of Physical Chemistry

Near Field Enhancement Localization on Plasmonic Gratings Raymond Gillibert,†,‡ Mitradeep Sarkar,¶ Julien Moreau,¶ Mondher Besbes,¶ Michael Canva,¶ and Marc Lamy de la Chapelle∗,† Université Paris 13, Sorbonne Paris Cité, Laboratoire CSPBAT, CNRS, (UMR 7244), 74 rue Marcel Cachin, F-93017 Bobigny, France, HORIBA Jobin Yvon S.A.S. 231 rue de Lille 59650 Villeneuve d’Ascq, France, and Laboratoire Charles Fabry, Institut d’Optique Graduate School, CNRS, Université Paris Saclay, 91227 Palaiseau, France E-mail: [email protected]

∗

To whom correspondence should be addressed Université Paris 13 ‡ HORIBA Jobin Yvon S.A.S. ¶ Institut d’Optique Graduate School †

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Abstract Plasmonic properties of arrays of gold nanodisks were investigated in order to study the localization of the near-field enhancement at the surface of the nanodisks. To measure the near field, Surface enhanced Raman spectroscopy (SERS) was performed on different kind of substrates with and without an over layer of silica that disabled the possibility for our SERS probe to adsorb on the top of our structures. Thanks to this we were able to determine, depending on the substrate, which fraction of the SERS enhancement was coming from the top of our structures. We demonstrate that the near-field enhancement is mainly localized at the top of the nano disks in the case of dielectric substrate whereas it comes from the nanodisk side for metallic subfilm substrate.

Introduction Surface Enhanced Raman Scattering (SERS) is a versatile technique based on the exploitation of the near field enhancement produced at the vicinity of metallic nanostructures through their specific optical properties (plasmon excitation, lightning rod effect...). SERS got a growing interest, especially due to the huge enhancement of the Raman signal of molecules that has paved the way of the single molecule observation 1–6 and with the apparition of new lithography techniques that enables fabrication of reproducible SERS substrates. 7–10 With such substrates, it is thus possible to control and tune precisely the optical properties of metallic nanostructures as well as their near field enhancement efficiency. 11–25 SERS method is intensively applied in the detection field in order to observe chemical or biological species at very low concentrations. 26–31 In this sensing framework, it is of first importance to be able to achieve a better understanding of the near field enhancement and to optimise it in order to reach limit of detection as low as possible. One of the main parameters that limits such optimisation is the non homogeneous distribution of the field around the nanostructure and the localization of the highest field enhancement. 32–34 Several simulations methods, 2 ACS Paragon Plus Environment

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such as Finite element method (FEM), 35–37 Discrete dipole approximation (DDA) 38–42 or Finite-difference time-domain (FDTD), 43–47 can be used to predict those properties and thus help to further optimize them. Those methods are very accurate when it comes to simulate any properties of the plasmonic structure as extinction, scattering or average electromagnetic field enhancement at the surface of the structures. 48–51 They can also provide some maps of the near-field distribution. However this generated near field distribution is less understood and hardly measurable since few experimental methods exist to measure it actually. In this paper, we use SERS to determine the effective near-field enhancement and its localisation. With electron beam lithography, we produced specific samples of gold nanodisks capped or not with silica layers. These latter ones allow us to block the accessibility of the molecules to the nanostructure surface and as a consequence to the enhanced near-field. We are thus able to compare the SERS signal produced by the nanodisks with or without silica layers and to provide information on the near field enhancement localisation, averaged on the different part of the nanostructures.

Experimental section Gold nanostructures

Figure 1: (a) Schemes of used samples, and SEM images of the sample deposited on ITO substrate with silica cap (b) at normal incidence and (c) with a 45o tilt. Arrays of gold nanodisks with diameters (D) from 50 up to 250 nm were fabricated using electron beam lithography on two different substrates: ITO coated glass slide, commonly used for e-beam lithography, or a gold film (Figure 1). The ITO substrate is a commercial 3 ACS Paragon Plus Environment


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0.7 mm thick glass slide already covered with a 160 nm thick indium thin oxide layer whereas the gold film substrate is a commercial 0.7 mm thick glass slide covered by a flat gold layer with a thickness of 30±3 nm. For both substrates, a 140 nm thick Poly(methyl methacrylate) (PMMA) layer was deposited by spin coating. The PMMA exposition was performed using the electron beam of a scanning electron microscope and its development was done for 40 s in a standard 1:3 methyl isobutyl ketone : isopropanol (MIBK/IPA) solution. The exposition was performed with the same patterning parameters for all samples in order to ensure identical structures. 50±3 nm of gold were deposited by thermal evaporation. To have a good adhesion of the gold on the ITO or on the glass, 3±1 nm of chromium were deposited before gold. Finally, a lift-off is done on the sample to remove the remaining PMMA layer and to produce the nano disks. To study the effect of the molecular localisation, a silica blocking layer (10±3 nm) was sputtered on top of the nanodisks before the lift-off. For such samples with silica layer, the probe molecules are expected to be localised only on the edges of the nanodisks as the, thiol group (–SH) cannot graft to silica (SiO2 ). Since we have no probe molecules on the top of the nanodisks with the silica cap, no SERS signal could be collected from this region. The height of the nanodisks is 50 nm and a constant gap of 200 nm is maintained between the nanodisks avoiding any significant near-field coupling. Furthermore, even if the ITO is a conductive material, we assume that the eventual far field coupling between the nanodisks through the ITO substrate is limited and have almost no impact on the nanodisk properties as the positions of our plasmon resonances are similar to the ones measured on nanodisks deposited on glass. 51 The period of the arrays were P = D + 200 nm. Scanning electron microscope was used to ensure the quality of our substrate (figure 1). The grating’s constant can be verified accurate ±1 nm, The standard deviation on the diameter of the nanodisks is around ±3 nm for all structures.


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Extinction spectroscopy Extinction was performed with an XploRA confocal Raman micro spectrometer (Horiba Scientific) after removing the edge filters. A non polarised white lamp was used to enlighten the substrate in transmission configuration. The transmitted light is collected with a 10× magnification objective (numerical aperture of 0.25). A reference spectrum is also recorded outside the nano structures in order to normalize the transmitted spectrum by the transfer function of the spectrometer.

Raman spectroscopy SERS measurements were performed with the same XploRA confocal Raman micro spectrometer (Horiba Scientific) in backscattering configuration. The Raman signal is recorded with a 100× magnification objective (numerical aperture of 0.90) in the case of ITO substrate to ensure a good collection of signal to maximize SERS intensity. However, for gold substrate, as it was demonstrated that the SERS emission is anisotropic, 50 we used a 10× objective (numerical aperture of 0.25) that SERS signal can be measured at normal incidence as well as with a 50o tilt. An excitation wavelength of 660 nm was used. The spectral resolution is fixed at 3 cm−1 . To measure the SERS signal, thiophenol was chosen as the probe molecule because of its high Raman cross-section and the strong affinity of the thiol group towards the gold surface. Thiophenol is also known to form a self-assembled monolayer on metal surfaces and to not graft to silica surfaces. After UV-Ozone treatment all nanodisk samples were functionalized with thiophenol for 1 hour in a 1 mM concentrated solution in ethanol. Several intense Raman peaks of thiophenol are observable at 415, 998, 1023, 1075 and 1575 cm−1 . For all nanostructures, five Raman spectra were measured at different locations randomly distributed. The SERS intensity was determined using the area of the 1075 cm−1 band as it is the most intense one. An average intensity was calculated by using the five Raman spectra and the standard deviation was used as error bar. 5 ACS Paragon Plus Environment


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Electromagnetic numerical simulation The extinction spectra were calculated numerically to compare with the extinction spectra obtained experimentally. The numerical model used is a combination of two well-known methods namely the Fourier modal method (FMM) and the finite element methods (FEM). 52,53 For the calculations, a plane wave was considered to be TM polarized and incident from the side of the substrate. This is similar to the experimental conditions used to measure the extinction spectra. The reflectivity (R) and transmission (T) from one unit period of the structure was then calculated and the absorption (A) of the structure was taken to be A = 1 − R − T . Such extinction spectra were calculated for different nanodisks diameters (with the range of 50–250 nm with steps of 20 nm). Similarly, to compare the experimentally obtained SERS intensity, local electromagnetic intensity was calculated for the nanodisks arrays using FEM for one unit period of the structure. For the calculation, a TM polarized plane wave was considered to be incident from air on the structure arrays with incident electric field E0 = 1V /m. The local electric field intensity (I = E 2 /E02 ) distribution for each finite element of meshed domain was thus calculated. The SERS intensity is proportional to the product of the local field intensity at the excitation wavelength and the emission wavelength, integrated over the surface where the molecules are expected to be localized. Thus from the calculated intensity distribution the SERS intensity was evaluated as: Z GSERS =

2 Eex (λex ) × ER2 (λR )dS

(1)

Ssurf

where λex = 660nm is the excitation wavelength and λR = 710 nm is the emission wavelength for the thiophenol band at 1075cm−1 . The Ssurf denotes the surface over which the integral was performed. It was taken as the total surface of the nanodisks for the samples without the silica layer on top and only the sides of the nano-disks for the case where the silica layer was considered on top of the disks.


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Results and discussion Extinction analysis P e r io d ( n m ) 2 5 0

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7 5 0 7 0 0 6 5 0 6 0 0 5 5 0 5 0 0 5 0

1 0 0

D ia m e te r ( n m )

Figure 2: (a) Experimental and (b) Theoretical LSPT resonance position as a function of nanodisks diameter when arrays are deposited on ITO substrate. The hollow red dots represent the same mode position with the silica overlayer. For the nanodisks on ITO substrate, as there is no coupling, we observe the localized surface plasmon (LSP ) of the individual nanodisks. Since the nano disks are excited with TM polarized light at normal incidence (incidence direction parallel to the axis of the disks), the electric field lies in the plane perpendicular to the axis to the disks and as a consequence, the excited LSP is the transverse one in the plane of the disk (perpendicular to the disk axis). We call it the LSPT . The positions of the LSPT resonance as a function of the nanodisk diameter obtained from the experimental and numerical extinction spectra are shown in figure 2a and 2b, respectively. We observe that the positions of the calculated extinction spectra match closely to the experimental ones. The LSPT position is redshifted with increasing diameters as expected since the LSPT is oriented along the direction transverse to the axis of the disks and thus the change of disk diameter has an important effect on the LSP resonance positions. For the samples with the silica layer deposited on the top of the nanodisks we observe a 7 ACS Paragon Plus Environment


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B M g

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Figure 3: (a) Experimental and (b) theoretical extinction peaks position as a function of nanodisks diameter when arrays are deposited on a gold film with a normal incident excitation. The hollow red scatters represent the same modes with the silica overlayer. slight redshift of the LSPT resonance less than 10nm (red dots in figure 2a). Similar trend of the LSPT resonance shift with a silica layer is also observed for the numerically calculated extinction spectra (data not shown). For the nanodisks on gold substrate, hybrid modes called the Bragg modes (BM) are excited. As described in our previous publication, 50 the uniform gold film can support propagating surface plasmons (PSP) and Bragg modes are excited when the in-plane propagation vector of the PSP (kspp ) matches the Bragg wave-vector given by kB = 2π/P owing to the periodicity (P) of the array. The resonance condition for the BMs depends purely on the array periodicity and undergoes a redshift with increasing periods. The resonance wavelength (λBM ) can be analytically written as 2πninc sin θ/λBM = kspp ± kB , where ninc is the refractive index of the incident medium and θ is the angle of incidence with respect to the axis of the disks. For a periodic array on a thin metal film, two types of BM s are excited: the BMg caused by the PSP on the metal-substrate interface and the BMa caused by the PSP on the metal-air interface. The peaks of the extinction spectra obtained experimentally for the nanodisks arrays on gold substrate are shown in figure 3a. BMg and BMa were observed for the structures


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P e r io d ( n m ) 2 5 0 9 0 0

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7 5 0 7 0 0 6 5 0 6 0 0 5 5 0 5 0 0 5 0

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Figure 4: (a) Experimental and (b) theoretical extinction peaks position as a function of nanodisks diameter when arrays are deposited on a gold film with a 50o tilted excitation. The hollow red scatters represent the same modes with the silica overlayer. and the resonance condition was seen to undergo a redshift with increasing diameters. The numerically and analytically calculated extinction spectra also show the presence of the two peaks (coloured map and black lines on the figure 3b respectively). It can be noticed that the positions of the extinction peaks correspond closely with the condition of the BMs excitation. It should be noted that the redshift of the BMs with respect to the diameter is due to the fact that the array period is also increased with increasing diameters (P = D + 200nm). A specific behaviour is observed when the incident light is no more perpendicular to the sample surface but comes with an oblique angle. For this experiment, the sample was tilted such as the incidence direction was at an angle (θ) of 50o with the axis of the disks. In this case the two BM s are still excited as expected and the resonance wavelengths are shown in figure 4a. These two modes are observable on the numerically calculated extinction spectra (figure 4b) and match closely to the analytical condition for resonance positions above 600nm (plain and dotted lines on the figure 4b). Below 600nm, a divergence between the numerical and the analytical models can be observed since the extinction peaks bend away towards higher wavelengths with decreasing diameters. At oblique incidence, the incident electric field (TM polarization) has two components one



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perpendicular to the nanodisk axis that excites the BM modes and one along the nanodisk axis. This latter one excites a LSP oriented perpendicularly to the film and in the disk axis direction (we will call it LSPL for longitudinal LSP). The change of diameter of the disks is expected to only induce a slight blue shift with increasing diameters and constant height owing to the change of aspect ratio of the disks. For nanodisks of height 50 nm the LSPL is expected to undergo resonance at a wavelength around 570 nm. 53 Thus, when the BM resonance condition is close to the LSPL resonance condition, an harmonic coupling occurs between these two plasmonic modes. Such coupling results in the appearance of plasmonic band gaps and an anti-crossing phenomena as observed numerically and experimentally between 500 and 600 nm on the figure 4. As for the nanodisks directly on ITO, the BMs position are slightly redshifted with a silica layer (less than 10 nm) in both conditions (normal and tilted incidences). Thus whatever the substrate used (ITO or gold), the deposition of a silica layer and as a consequence the modification of the optical index at the top of the nanodisks have nearly no influence on the position of the plasmon resonance and thus on the resonance itself. In the case of the tilted incidence, a larger effect on the resonance position can be expected, since we excite the LSPL that could induce a large field enhancement at the top of the disk. This is only slightly observe for diameter lower than 100 nm. This means that the field created by the LSPL is very low compare to the one created by the BM mode. As a consequence, the main contribution to the plasmon mode in the tilted configuration comes mainly from the BM mode and not from the LSPL .

SERS Analysis Arrays on ITO substrate The experimentally measured SERS intensity for the nanodisks arrays on ITO substrate as a function of the diameter and the LSPT resonance position is shown on figure 5a and 5c. It can be noticed that the SERS intensity reaches a maximum for a diameter of 120 nm and a LSPT 10 ACS Paragon Plus Environment

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1 .4 1 .2 1 .0

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C a lc . S E R S In te n s ity

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L S P R P o s itio n ( n m )

Figure 5: (a) Experimental and (b) simulated SERS intensity of the thiophenol 1075 cm−1 Raman band as a function of nanodisks diameter for ITO substrate (λex =660 nm) without (solid black squares) and with (hollow red circles) silica overlayer. On figure b, the black and red lines are just a guide for the eyes. (c) Experimental and (d) simulated SERS intensity of the thiophenol 1075 cm−1 Raman band as a function of LSP resonance position for ITO substrate (λex =660 nm) without (solid black squares) and with (hollow red circles) silica overlayer. On figure d, the black and red lines are just a guide for the eyes. The vertical lines on c and d represent the spectral positions of the excitation wavelength (660 nm) and the emitted Raman band (710 nm) resonance position close to 650 nm. Such observation is in agreement with the numerical calculation of the SERS intensity shown on figure 5b and 5d. The LSPT resonance wavelength is close to the SERS excitation wavelength (660 nm) as already observed previously. When the top of the nanodisks is covered with the silica layer, we observe a large decrease in the SERS intensity, confirmed by the numerical calculations (figure 5, red dots). This



1 .0 0 .9 0 .8

S E R S In te n s ity R a tio

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2 πr h 2 πr h + πr

0 .7 0 .6

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Figure 6: SERS intensity ratio between the sample with and without silica overlayer in regard of nanodisk diameter, for the experimental (black squares) and the simulated values (red triangles). The blue dashed line represents the ratio between the surface area of the sides of the disks (2πrh) and the surface area of the disks (2πrh + πr2 ). demonstrates that a significant proportion of the SERS intensity comes from the molecules localised on the top of the nanodisks and this is a clear evidence that a large part of the enhanced near-field is localised at this nanodisk surface. To quantify the field enhancement on the top compared to the one of the whole nanodisk, we calculated the ratio between the SERS intensity measured with and without the silica overlayer, ISERS

with silica

and ISERS

without silica

respectively, as a function of the disks diameter (figure 6)

as: ISERS ISERS

with silica

=

without silica

ISide (IT op + ISide )

(2)

with IT op , the SERS signal from the top of the nanodisk and ISide , the SERS signal from the side of the nanodisk. This ratio gives us directly the proportion of the near-field intensity coming from the side of the nanodisks (figure 6). For both the experimental and numerical results we see that the SERS intensity ratio decreases with increasing diameters. This means that the contribution of the nanodisk side to the SERS intensity decreases with the diameter and that the top of the nano disks give more


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Figure 7: Electromagnetic enhancement maps and SERS intensity as a function of curvilinear coordinate on the structures profile for (a) 110 nm nanodisks on ITO with normal incidence excitation (b) 170 nm nanodisks on gold film with normal incidence excitation and (c) 150 nm nanodisks on gold film with a 50o tilted excitation. and more SERS signal with the diameter. To be sure that it is not a simple geometrical effect, we have also calculated the ratio between the surface area of the sides of the disks (2πrh) and the surface area of the disks (2πrh + πr2 ) (figure 6). We see that this geometrical ratio is always largely higher than the experimental values. We can conclude from these results that for the LSPT mode, the SERS intensity comes mainly from the molecules localised at the top of the nanodisks. The top surface contribution goes from around 50% up to nearly 85% of the SERS signal for diameter larger than 180 nm. Indeed, for such nanoparticles, the near-field enhancement is mainly localised at the corners of the nanostructures (between the top and the side) and at the interface between the nanostructure and the substrate. In the latter case, this enhancement 13 ACS Paragon Plus Environment


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is hardly exploitable since the field is inside the substrate and very few molecules can be excited at this interface. Thus, the SERS signal is essentially due to the corners as can be seen on figure 7. In our case, the silica layer covers these corners and should make these ones inaccessible to the molecules, reducing drastically the SERS signal. It can also be noticed that the experimental SERS intensity ratio is systematically lower than the calculated one. This can be due to the fact that the silica layer is perfectly modelled and does not cover entirely the nanodisk corners. In this case, the corners can still contribute to the SERS signal and thus provide higher SERS signal compared to the experiments.

Arrays on gold film SERS measurements were performed in the same manner on nanodisks arrays deposited on gold substrate at normal incidence (figure 8) and with a 50o tilt in transverse magnetic configuration (TM) (figure 9). For both experimental and numerical SERS intensity the correlation between the position of the BM and the excitation or Raman wavelengths is not so clear and no specific rule can be actually defined to optimise the SERS signal. However, we can observe a continuous increase of the SERS signal with the diameter in the case of the normal incidence (figure 9). This behaviour can be observed in the simulations and an additional sharp SERS intensity increase is observed for diameter 170nm. This peak is not present in the experiment and this can be due to the fact that a non null numerical aperture is used for collection of the SERS signal. Thus several angles for scattered light and for excitation light are collected and integrated in the same signal, which means we are averaging the signal of several angles collected simultaneously. As demonstrated previously, 50 the SERS of such substrate is strongly dependent on the excitation and collection angle. Hence, we assume that the deviation between the experimental and simulated SERS intensities is due to the difference between the experimental and simulated conditions for the excitation and collection of the SERS intensities. For the tilted incidence (figure 9 we observe a maximum for a diameter


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Figure 8: (a) Experimental and (b) simulated SERS intensity of benzenethiol 1075 cm−1 Raman band as a function of disks diameter for gold substrate without (solid black squares) and with (hollow red circles) silica overlayer at normal incidence. (c) Experimental and (d) simulated SERS intensity of the thiophenol 1075 cm−1 Raman band as a function of BMg position for ITO substrate (λex = 660 nm) without (solid black squares) and with (hollow red circles) silica overlayer. On figure d, the back and red lines are just guides for the eyes. The vertical lines on c and d represent the spectral positions of the excitation wavelength (660 nm) and the emitted Raman band (710 nm) of 150 nm and a signal increase for low diameters due to the excitation of the BM and of the LSPL mode respectively. This time the simulated values predict very accurately the measured intensity. We notice that there is almost negligible difference between the SERS signal recorded experimentally with and without the silica layer in normal incidence as well as for the tilted measurements. The same observation can be made for the numerically calculated values.



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8 0 k 6 0 k 4 0 k 2 0 k 0 6 0 0

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7 0 0

7 5 0


Figure 9: (a) Experimental and (b) simulated SERS intensity of benzenethiol 1075 cm−1 Raman band as a function of disks diameter for gold substrate without (solid black squares) and with (hollow red circles) silica overlayer with a tilt of 50o . (c) Experimental and (d) simulated SERS intensity of the thiophenol 1075 cm−1 Raman band as a function of BMa position for ITO substrate (λex = 660 nm) without (solid black squares) and with (hollow red circles) silica overlayer. On figure d, the back and red lines are just guides for the eyes. The vertical lines on c and d represent the spectral positions of the excitation wavelength (660 nm) and the emitted Raman band (710 nm) This is quite clear on the EM field maps (figure 7b,c). The top of the nanodisk has an enhancement factor smaller than 1 on most of its area for both normal and tilted excitation. We can conclude from these results that for the BMs, the significant contribution to the SERS intensity enhancement comes from the molecules localised on the sides of the nanodisk and that the molecules localised on the top of the nanodisks have negligible contribution. This is because the BMs result from the PSP, owing to the periodicity of the structure and so a major portion of the electric field intensity for these modes lies in the gaps between 16 ACS Paragon Plus Environment

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adjacent nanodisks.

Conclusion Using different lithographed structures, with and without silica capping, it has been demonstrated that SERS signals from molecules deposited on substrates consisting of gold nanodisks arrays are very different depending on their specific localization on the structure. More specifically, the main contributions can be respectively attributed to either the top of the disks, in the case of sole metal disks arrays, or from the disk’s sides, in the case of the use of underlying gold film. This is indicative of the regions of high electromagnetic field enhancement and of the field distribution around the nanostructures; in good agreement in the case of a gold substrate and partial agreement in the case of ITO substrate with the field calculations performed using the hybrid FEM/FMM model. It demonstrates that the field distribution is highly dependent on the direct environment of the nanostructures and on the substrates used (dielectric or gold film) and as a consequence on the nature of the excited plasmon: localized plasmonic mode in the former case and Bragg mode in the later where the propagating and localized modes are resonantly coupled to the array periodicity. This observation is also of first importance for sensing issues. Indeed, to be highly efficient and to reach the lowest detection limit, it is necessary to capture preferentially the molecules to be detected inside the highest field enhancement localisation using molecular layer functionalization. It means that different strategies have to be developed depending on the nanostructures used and thus on the SERS sensor architecture.

Acknowledgement The authors acknowledge ANR P2N (ANR-12-NANO-0016) and the support of the French Government and ANRT Association Nationale de la Recherche et de la Technologie for funding of the project in which this work takes place and initiatives d’excellence, IDEX Paris-Saclay.



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Thanks to the Centrale de Proximité en Nanotechnologies de Paris Nord (CPN2, 99 Avenue Jean-Baptiste Clément 93430 Villetaneuse, France) to supply the clean room for samples fabrication. In addition, Thanks to Dr Inga Tijunelyte for SEM measurements.

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