Vanadium Dioxide–Iridium Composite Development: Speciﬁc Near Infrared Surface Plasmon Resonance

: This work serves as a roadmap for the development of a Vanadium dioxide (VO 2 )–Iridium composite based on the self-assembly of closely packed colloidal polystyrene microspheres (P-spheres) coupled with a Pulsed Laser Deposition (PLD) process. The self-assembly of a monolayer of PS is performed on an Al 2 O 3 -c substrate, using an adapted Langmuir–Blodgett (LB) process. Then, on the substrate covered with P-spheres, a 50-nanometer Iridium layer is deposited by PLD. The Iridium deposition is followed by the removal of PS with acetone, revealing an array of triangular shaped metallic elements formed on the underlaying substrate. In a last deposition step, 50-, 100-and 200-nanometer thin ﬁlms of VO 2 are deposited by PLD on top of the substrates covered with the Iridium quasi-triangles, forming a composite. Adapting the size of the P-spheres leads to control of both the size of the Iridium micro-triangle and, consequently, the optical transmittance of the composite. Owing to their shape and size the Iridium micro-triangles exhibit localized surface plasmon resonance (LSPR) characterized by a selective absorption of light. Due to the temperature dependent properties of VO 2 , the LSPR properties of the composite can be changeable and tunable. of are determined transmittance measurements structural have been investigated using diffraction The ImageJ and OriginPro 2015 software are for data processing.


Introduction
Due to their ability to bring together and combine properties of different materials, composites find usage in a variety of applications. Composites are the future of materials and their field of applications, ranging from the development of hard-soft composite magnets [1] to the advances in light manipulation using composite nanostructures [2,3] or to nanocomposites based supercapacitors [4], is only expected to increase with time. Here, we propose the development of a composite based on the following two complementary materials: a noble metal (Iridium) that constitutes a sub-micro element of the composite and smart oxide matrix (Vanadium dioxide VO 2 ) for infrared surface plasmon resonancebased applications. The Vanadium dioxide-Iridium composite development is made possible by using the self-assembly of closely packed colloidal polystyrene microspheres (P-spheres) on an Al 2 O 3 -c substrate and a Pulsed Laser Deposition (PLD) process. The PS serve as templates/masks for the Ir microtriangle deposition using PLD. In a second step, VO 2 thin films are deposited on the substrate decorated with the Ir microtriangles, thus forming the composite. When the Iridium triangles are excited by electromagnetic radiation, the metallic elements show collective oscillations of their conduction electrons known as localized surface plasmon resonances (LSPR). The wavelength position of the LSPR peak depends on the size, shape and dielectric properties of the metal elements and is affected by the surrounding environment. The choice of vanadium dioxide as a covering matrix is based on its "smart" properties. With a notable metal-insulator transition (MIT) at a critical temperature of 68 • C, VO 2 has become, in the last few decades, since the pioneer Morin's work in 1959 [5], a material of great interest because of its promising strengths to investigate applications as new further thermochromic, electronic, thermal and optic switching devices [6][7][8]. Indeed, the VO 2 MIT is characterized by rapid (10 −9 -10 −12 ns) [9], huge and sharp changes in physical properties such as optical absorption, dielectric function and electrical and thermal conductivity [10]. However, obtaining a pure VO 2 phase is very challenging due to its narrow range of thermodynamic stability among some seventeen vanadium oxides, explaining the diverse chemical or physical techniques studied to grow VO 2 thin film [11][12][13][14]. Pulsed laser deposition is one of the most interesting processes to deposit pure VO 2 thin films, by controlling several deposition parameters such as temperature, pressure and fluence [15,16]. Moreover, due to a very high melting temperature, i.e., 2466 • C, it is also challenging to deposit thin Iridium films [17,18]. Using a highly powerful nano-second pulsed laser (10 8 -10 9 GW), the ablation of all the elements is possible, even for the most refractory. PLD is then also a convenient process to deposit Ir metallic films.
In the literature, VO 2 -based composites for plasmonic applications often involve gold or silver inclusions as the metal component [19][20][21]. VO 2 deposition requires the substrate to be heated up to about 500 • C. This necessary temperature induces metal deformations, metallic melting and the metal de-wetting process, and consequently, gold or silver sketches or nanoparticles are affected, changing their shape and size, making it difficult to the understand and control the composite properties. In particular, the effects on the plasmonic characteristics of the composite of the dielectric environment are coupled with the contribution of the shape change of the nanoparticles. The high melting temperature of Iridium makes it an ideal candidate for isolating and understanding the contribution of such a complex dielectric environment (VO 2 ) to the plasmonic properties of the composite. In this context, the aim of our work is to precisely quantify the influence of VO 2 MIT characteristics onto the nanocomposite plasmonic behavior and to combine the metallic plasmonic properties with the dielectric tunability of VO 2 , resulting in a system that is able to tune the light transmittance in the InfraRed range.

Materials and Methods
The VO 2 -Ir composites are manufactured using a combination of the two processes (Langmuir-Blodgett colloidal lithography and Pulsed Laser Deposition) presented in Figure 1. First, polystyrene microspheres (P-spheres) are assembled in the form of a monolayer on a substrate, using a derivative-Langmuir-Blodgett colloidal lithography process (KSV Nima << Langmuir-Blodgett Deposition Through Medium, KN 2002 >>). The LB principle consists of the transfer of a one-molecule thick layer (Langmuir monolayer) spread at the air/sub-phase (in general water) interface onto a receiving substrate. On the basis of this classical process, the LB principle has been adapted for microsphere colloidal lithography. The role of the classical amphiphilic molecules is played by microspheres of polystyrene functionalized with a steric acid group, e.g., C18-triethoxy (octadecyl) silane [22]. Here, the colloidal lithography experiments are performed using P-spheres with diameters of 2 and 3 µm, commercially available at Microparticles GmbH ® and Micro Partikeltechnologie GmbH ® . The P-spheres are commercialized already functionalized with C18 and sold as a water suspension of 10 mL, 50 mg/mL. In a single colloidal lithography experiment, 7500 µL of ethanol are added to 2500 µL of P-spheres suspension and then the mixture is transferred on the surface of 230 mL of distilled water that acts as a sub-phase. The ethanol adjusts the surface tension of water and controls the interaction between the P-spheres, thereby enabling the formation of a P-spheres monolayer on the surface of the sub-phase. Then, the resulting P-spheres monolayer is further compressed to a surface tension of around 40 mN/m by using the barriers of the LB system and transferred onto an Al 2 O 3 -c substrate.
In a second experimental step, the Al 2 O 3 -c substrates decorated with P-spheres are covered by Iridium thin films using the PLD process. The 50-nanometer thin films of Iridium are deposited using a pulsed KrF laser (TUI ThinFilmStar100) working at a wavelength of 248 nm at 10 Hz and a fluence of 2-3 J/cm 2 . The deposition of Iridium is carried out in a vacuum (1 × 10 −7 mbar) and at room temperature (~25 • C). After the Iridium deposition, the P-spheres are removed with acetone, revealing a periodic and organized array of microtriangles. The resulting Iridium sketch is further covered with a thin film of Vanadium dioxide deposited using the PLD system, with identical pulsed laser and fluence in a reactive oxygen environment at a pressure of 2.2 × 10 −2 mbar and a deposition temperature of 500 • C. Different composites are made using vanadium dioxide with three thicknesses of 50, 100 and 200 nm, respectively. After the second deposition process, a composite consisting of Iridium microtriangles embedded in Vanadium dioxide is achieved. The optical characteristics of the composites are determined by transmittance measurements performed using a Fourier Transform InfraRed Spectroscopy (FTIR) (ThermoFisher-Nicolet 6700) system for the 1.5 to 5.5 µm optical wavelength range. The structural properties of the VO 2 -Ir microtriangles composites have been investigated using X-ray diffraction (XRD) in θ-2θ geometry (Bruker diffractometer, model "D8 Advance", CuKα x-ray source, λ = 0.154 nm) equipped with a focusing Kα1 mono filter and detector (LynxEye, model "A17-B60"). The ImageJ and OriginPro 2015 software are used for data processing. ium are deposited using a pulsed KrF laser (TUI ThinFilmStar100) working at a wavelength of 248 nm at 10 Hz and a fluence of 2-3 J/cm 2 . The deposition of Iridium is carried out in a vacuum (1 × 10 −7 mbar) and at room temperature (~25 °C). After the Iridium deposition, the P-spheres are removed with acetone, revealing a periodic and organized array of microtriangles. The resulting Iridium sketch is further covered with a thin film of Vanadium dioxide deposited using the PLD system, with identical pulsed laser and fluence in a reactive oxygen environment at a pressure of 2.2 × 10 −2 mbar and a deposition temperature of 500 °C. Different composites are made using vanadium dioxide with three thicknesses of 50, 100 and 200 nm, respectively. After the second deposition process, a composite consisting of Iridium microtriangles embedded in Vanadium dioxide is achieved. The optical characteristics of the composites are determined by transmittance measurements performed using a Fourier Transform InfraRed Spectroscopy (FTIR) (Ther-moFisher-Nicolet 6700) system for the 1.5 to 5.5 µm optical wavelength range. The structural properties of the VO2-Ir microtriangles composites have been investigated using Xray diffraction (XRD) in θ-2θ geometry (Bruker diffractometer, model "D8 Advance", CuKα x-ray source, λ = 0.154 nm) equipped with a focusing Kα1 mono filter and detector (LynxEye, model "A17-B60"). The ImageJ and OriginPro 2015 software are used for data processing.

Results and Discussions
In this article, experiments realized with 2 or 3 µm P-spheres give the same type of composites, the same behavior and similar results except for the geometrical considerations. The results obtained using 2 or 3 µm P-spheres will then be representative of the general composite characteristics and will be alternatively used.

Colloidal Lithography: 2D Arrangement of the Polystyrene Microspheres (P-Spheres) and Optimization Processes
In Langmuir-Blodgett colloidal lithography, the most common close packed Pspheres arrangements resemble a 2D crystal with a hexagonal close packed structure. In practice, the formation of the monolayer of P-spheres with a perfect 2D crystal structure is controlled by the optimization of the Langmuir-Blodgett procedure itself coupled with the intrinsic characteristics (polydispersity, sphericity, etc.) of the P-spheres. Here, the Pspheres are commercially provided by Microparticles GmbH ® and Micro Partikeltechnologie GmbH ® . Thereby, all the improvements of the 2D structure are only made by the optimization of the process. In LB, the P-spheres monolayer formation is driven by the balance of the different forces, (attractive or repulsive). Forces such as Van der Waals interaction, electrostatic interaction, steric effect and capillary forces govern the interaction

Results and Discussions
In this article, experiments realized with 2 or 3 µm P-spheres give the same type of composites, the same behavior and similar results except for the geometrical considerations. The results obtained using 2 or 3 µm P-spheres will then be representative of the general composite characteristics and will be alternatively used.

Colloidal Lithography: 2D Arrangement of the Polystyrene Microspheres (P-Spheres) and Optimization Processes
In Langmuir-Blodgett colloidal lithography, the most common close packed P-spheres arrangements resemble a 2D crystal with a hexagonal close packed structure. In practice, the formation of the monolayer of P-spheres with a perfect 2D crystal structure is controlled by the optimization of the Langmuir-Blodgett procedure itself coupled with the intrinsic characteristics (polydispersity, sphericity, etc.) of the P-spheres. Here, the P-spheres are commercially provided by Microparticles GmbH ® and Micro Partikeltechnologie GmbH ® . Thereby, all the improvements of the 2D structure are only made by the optimization of the process. In LB, the P-spheres monolayer formation is driven by the balance of the different forces, (attractive or repulsive). Forces such as Van der Waals interaction, electrostatic interaction, steric effect and capillary forces govern the interaction and arrangement in crystalline domains of P-spheres [23]. The capillary forces depend on the sphericity or on the "irregular contact line" between the individual P-spheres [24]. However, the Van der Waals interaction, electrostatic interaction and steric depend on the working temperature of the LB process [23]. This well-known phenomenon is clearly revealed in Figure 2. and arrangement in crystalline domains of P-spheres [23]. The capillary forces depend on the sphericity or on the "irregular contact line" between the individual P-spheres [24]. However, the Van der Waals interaction, electrostatic interaction and steric depend on the working temperature of the LB process [23]. This well-known phenomenon is clearly revealed in Figure 2. The quality of the arrangement of the P-spheres depends on the temperature. At 20 °C (Figure 2a), the P-spheres monolayer partially collapses, resulting in the deposition of additional P-spheres on top of the main monolayer. At 30 °C (Figure 2c), the P-sphere monolayer also partially collapses in a similar manner to Figure 2a. When the temperature is set to 25 °C (Figure 2b), the best arrangements are obtained and the number of additional P-spheres on top of the main monolayer reaches a minimum.
(a) (b) (c) Besides the presence of an additional P-sphere on top of the main monolayer, the size of the individual crystalline domains is also of great interest. Ideally, all the P-spheres should arrange in a single crystallin domain on the substrate, but in practice the P-spheres monolayer is composed of multiple domains resembling a 2D poly crystalline entity. The quality of the P-spheres arrangement can be assessed through the generation of a Fast Fourier transform (FFT) [25]. The results of the FFT procedure are presented in inserts of Figure 2. A ring in a reciprocal space (after FFT calculation) is proof of the presence of a constant characteristic distance in all directions in the 2D space. This is the case for Pspheres arrangements at 20 °C (see Figure 2a). If specific directions are favorized (increasing the quality of the arrangements), then discrete points appear symmetrical to the center in the reciprocal space (see Figure 2b,c). The diameter or the distance between two points are inversely proportional to the characteristic length. The FFT calculation shows that the quality and size of the individual 2D crystalline domains increase versus the temperature. There is, however, a tradeoff between increasing the size of the individual 2D domains and the presence of additional P-spheres on top of the main monolayer. Considering these two aspects, domain size vs. additional P-spheres, 25 °C (see Figure 2) constitutes the op- Besides the presence of an additional P-sphere on top of the main monolayer, the size of the individual crystalline domains is also of great interest. Ideally, all the P-spheres should arrange in a single crystallin domain on the substrate, but in practice the P-spheres monolayer is composed of multiple domains resembling a 2D poly crystalline entity. The quality of the P-spheres arrangement can be assessed through the generation of a Fast Fourier transform (FFT) [25]. The results of the FFT procedure are presented in inserts of Figure 2. A ring in a reciprocal space (after FFT calculation) is proof of the presence of a constant characteristic distance in all directions in the 2D space. This is the case for Pspheres arrangements at 20 • C (see Figure 2a). If specific directions are favorized (increasing the quality of the arrangements), then discrete points appear symmetrical to the center in the reciprocal space (see Figure 2b,c). The diameter or the distance between two points are inversely proportional to the characteristic length. The FFT calculation shows that the quality and size of the individual 2D crystalline domains increase versus the temperature. There is, however, a tradeoff between increasing the size of the individual 2D domains and the presence of additional P-spheres on top of the main monolayer. Considering these two aspects, domain size vs. additional P-spheres, 25 • C (see Figure 2) constitutes the optimal P-spheres deposition temperature for the presented system. In addition to the temperature, the substrate nature can modify the surface tension and affect the sphere organization. To emphasis this effect, experiments were conducted with two other substrates, a Borosilicate glass (BK7) and a silicon (Si) wafer, in the same deposition process. At the three substrate surfaces, P-spheres depositions present identical characteristics for the optimized temperature of 25 • C (data not shown here).

VO 2 -Ir Microtriangles Composite Development and Structural Characteristics
In the 2D hexagonal arrangement, the maximum coverage rate of the substrate, τ sphere_covering , by the P-spheres, is defined by Equation (1). τ sphere_covering = S michosphere /S total = Area disk /Area hexagon = π/2 √ 2 = 0.907 (1) where S michosphere is the projected surface occupied by microsphere on the substrate and S total is the total surface available on the substrate. Equation (1) shows that the τ sphere_covering, for an ideal structure is equal to a constant 90.7% and is independent of the colloidal P-spheres D-diameter. Thus, a decrease or increase in the D-diameter will never affect τ sphere_covering and the quantity of light transmission. This is an interesting specific characteristic of the process presented here. The theoretical remaining ≈9.3% of the substrate surface is exposed to the flux of ablated Iridium metal during the PLD process. Then, the P-spheres are removed with acetone. As expected, post optical measurements reveal that the Ir microtriangles are covering approximately 9 to 11% of the substrate surface. The specific quasi-triangular shape of the Ir microtriangles is linked to the 2D hexagonally close packed arrangement of the P-spheres. This quasi-triangular shape can be defined by a specific parameter "a", (the perpendicular bisector of the triangles, see Figures 1 and 3a), defined in Equation (2) as follows: In the 2D hexagonal arrangement, the maximum coverage rate of the substrate, τsphere_covering, by the P-spheres, is defined by Equation (1). τsphere_covering = Smichosphere/Stotal = Areadisk/Areahexagon = π/2√2 = 0.907 (1) where Smichosphere is the projected surface occupied by microsphere on the substrate and Stotal is the total surface available on the substrate. Equation (1) shows that the τsphere_covering, for an ideal structure is equal to a constant 90.7% and is independent of the colloidal Pspheres D-diameter. Thus, a decrease or increase in the D-diameter will never affect τsphere_covering and the quantity of light transmission. This is an interesting specific characteristic of the process presented here. The theoretical remaining 9.3% of the substrate surface is exposed to the flux of ablated Iridium metal during the PLD process. Then, the Pspheres are removed with acetone. As expected, post optical measurements reveal that the Ir microtriangles are covering approximately 9 to 11% of the substrate surface. The specific quasi-triangular shape of the Ir microtriangles is linked to the 2D hexagonally close packed arrangement of the P-spheres. This quasi-triangular shape can be defined by a specific parameter "a", (the perpendicular bisector of the triangles, see Figures 1 and 3a), defined in Equation (2) as follows: Thus, taking into account Equation (2), the quasi-triangular made using P-spheres of 3 µm in diameter (resp. 2µm), have the relevant parameter "a" equal to 0.70 µm (resp. 0.45 µm) When the composite is developed at 500 °C (VO2 is deposited on the Ir microtriangles covered Al2O3-c substrate), the specific parameter "a" size and the shape of the triangles remained unmodified. Due to a high melting temperature (2450 °C), Ir microtriangles are effectively preserved even after the VO2 deposition. The atomic force microscopy (AFM) image presents the composite consisting in 0.70 µm Ir microtriangles embedded in 200 nm VO2 (Figure 3a). The resulting materials can be considered as a composite in which the sub-micro role is taken by the Ir microtriangles. Thus, taking into account Equation (2), the quasi-triangular made using P-spheres of 3 µm in diameter (resp. 2 µm), have the relevant parameter "a" equal to 0.70 µm (resp. 0.45 µm).
When the composite is developed at 500 • C (VO 2 is deposited on the Ir microtriangles covered Al 2 O 3 -c substrate), the specific parameter "a" size and the shape of the triangles remained unmodified. Due to a high melting temperature (2450 • C), Ir microtriangles are effectively preserved even after the VO 2 deposition. The atomic force microscopy (AFM) image presents the composite consisting in 0.70 µm Ir microtriangles embedded in 200 nm VO 2 (Figure 3a). The resulting materials can be considered as a composite in which the sub-micro role is taken by the Ir microtriangles.
The X-ray patterns recorded at room temperature and presented in Figure 3b,c show no influence of the Iridium microtriangles on the VO 2 single phase and mono-orientation. In both cases, using the 0.70 µm, resp. 0.45 µm Ir microtriangles (not shown here), the main characteristics of the VO 2 matrix, i.e., MIT, are preserved. VO 2 has a monoclinic structure with a (020) orientation. The Ir has a (111) orientation and a face-centered cubic (fcc) structure. The shift of the Ir and VO 2 peaks from their theoretical counterparts (the dotted lines 2θ = 39.76 • for VO 2 ) is linked to the lattice mismatch between them and the Al 2 O 3 -c substrate [26]. For example, the mismatch between VO 2 (monoclinic) and the Al 2 O 3 -c substrate is estimated at~13% [27]. This lattice mismatch induces compressive strain within the films, both in VO 2 thin films and the VO 2 -Ir microtriangles composite, onto the Al 2 O 3 -c substrates. The strain alters the orbital occupancy near the Fermi energy level and leads to an increase in the insulator state's band gap size that give rise to a higher MIT temperature. As the VO 2 thickness increases, the peak position shifts closer to the theoretical one due to normal strain relaxation [28]. The Ir microtriangles are tensile strained in the out-of-plane direction onto the Al 2 O 3 -c substrate.

Compositional Characteristics of the VO 2 -Ir Microtriangles Composite
The chemical composition of the samples is assessed using Energy Dispersive X-ray Spectroscopy (EDS). In Figure 4a patterns; (c) Zoom on a part of (b) XRD patterns from 39.6° to 41° θ-2θ XRD patterns of the composite. The thickness the Iridium triangles within the composite is fixed to 50 nm, while the VO2 thickness is 50, 100 and 200 nm. The dott lines in image (c) correspond to the theoretical position of VO2 and Iridium.
The X-ray patterns recorded at room temperature and presented in Figure 3b no influence of the Iridium microtriangles on the VO2 single phase and mono-orien In both cases, using the 0.70 µm, resp. 0.45 µm Ir microtriangles (not shown he main characteristics of the VO2 matrix, i.e., MIT, are preserved. VO2 has a mon structure with a (020) orientation. The Ir has a (111) orientation and a face-centere (fcc) structure. The shift of the Ir and VO2 peaks from their theoretical counterpa dotted lines 2θ = 39.76° for VO2) is linked to the lattice mismatch between them a Al2O3-c substrate [26]. For example, the mismatch between VO2 (monoclinic) a Al2O3-c substrate is estimated at ~13% [27]. This lattice mismatch induces comp strain within the films, both in VO2 thin films and the VO2-Ir microtriangles com onto the Al2O3-c substrates. The strain alters the orbital occupancy near the Fermi level and leads to an increase in the insulator state's band gap size that give rise to a MIT temperature. As the VO2 thickness increases, the peak position shifts closer theoretical one due to normal strain relaxation [28]. The Ir microtriangles are strained in the out-of-plane direction onto the Al2O3-c substrate.

Compositional Characteristics of the VO2-Ir Microtriangles Composite
The chemical composition of the samples is assessed using Energy Dispersive Spectroscopy (EDS). In Figure 4a Figure 3a). Following the chemical composition analysis, the composite architecture is confirmed and the presence of VO 2 validates the synthesis procedure and acts as a "blanket" on top of the Ir microtriangles.

VO 2 -Ir Microtriangles Composite's Optical Transmittance Characteristics
The optical properties in terms of the light transmittance of VO 2 are dependent on the temperature. At room temperature, VO 2 is transparent to near infrared light but as the measurement is performed at a temperature closer to the MIT temperature (i.e., around 68 • C) the light transmittance decreases and can reach a minimum depending on the thickness. Characteristics such as MIT temperature, transition hysteresis and transmission contrast depend on the intrinsic and extrinsic properties of the VO 2 composite. The presence of Ir microtriangles can obviously affect the quality of the transition. Figure 5 makes a direct comparison between the optical characteristics of VO 2 -Ir composites and original VO 2 samples. Except for the metallic sketch (presence of Ir microtriangles in the composites), all the other deposition parameters are the same. Figure 5a-c shows the temperature dependence of the light transmittance of the composites vs. VO 2 samples. At room temperature, the transmittance is dependent on the thickness of VO 2 and on the presence of Ir microtriangles. The light transmittance measured at 1.5 µm for the composites is approximatively 15% lower compared to the one of pristine VO 2 samples (for a 200nanometer thickness). This 15% transmittance difference fits well with the approximatively 9% coverage of Ir microtriangles on the substrate surface. When comparing the optical transmittance of the composites made with 0.45 µm vs. 0.70 µm Ir microtriangles (data are not presented here) no difference is pointed out, as is to be expected since the microtrianglesubstrate coverage is equivalent. If the temperature increases, all the samples show similar optical transmittance characters to reach a thickness-dependent minimum above the MIT temperature. The hysteresis areas are approximatively constant, meaning that the matrices of VO 2 are preserving their flexibility in temperature.
The difference between the extrema of the first derivatives (see Figure 5c,d) of the temperature-dependent optical transmittance shows that the average hysteresis width of the composites is close to 6 • C, equal to that of the VO 2 thin films. The MIT temperature is approximatively 75 • C, when the thickness of the VO 2 is 200 nm, which proves that the quality of the VO 2 component of the composites is preserved. The slight shift of the MIT temperature (75 • C compared to the reference 68 • C) is a direct consequence of a weak strain inside the VO 2 thin film, as discussed previously.

Plasmonic Properties of the VO 2 -Ir Microtriangles Composites
The dependence of the optical absorbance vs. wavelength for different VO 2 thicknesses (50, 100 and 200 nm) is presented in Figure 6a. In the 1.5-5.5 µm range, the global absorbance value increases with the thickness. These curves are references useful to estimate the contribution of VO 2 films on the absorbance spectra of the composites. These baselines are subtracted from the global absorbance spectra of the composite in order to extract the absorbance spectra of the zones with Ir microtriangles plotted in Figure 6b.
The composites exhibit several surface plasmon resonances that correspond to multiple absorbance peaks. The origin of these localized absorptions lies in the Ir microtriangles component and peak effects of the metallic architecture [29].
The absorbance spectra of the Ir microtriangles array, without matrix contribution, show an absorption peak in the infrared part of the electromagnetic spectrum (Figure 6b). This absorption peak is identified as the localized surface plasmon resonance properties of the Ir geometric architecture and is dependent on the dimension of each microtriangle. For Ir microtriangles with the typical dimension of a = 0.45 µm (resp. a = 0.7 µm), the LSPR maximum is localized at λ LSPR = 2.95 µm (resp. λ LSPR = 4.40 µm) and is strongly affected by the surroundings, as shown by the absorbance spectra of the composites measured as a function of thickness (Figure 6b). The absorbance spectra of the composites are measured as a function of thickness. The LSPR peaks of the composites shift to higher wavelengths with an increasing VO 2 thickness (Figure 6b). This is due to the sensitivity and dependence of the triangles' LSPRs to the dielectric environment [30].
perature, the transmittance is dependent on the thickness of VO2 and on the presence of Ir microtriangles. The light transmittance measured at 1.5 µm for the composites is approximatively 15% lower compared to the one of pristine VO2 samples (for a 200-nanometer thickness). This 15% transmittance difference fits well with the approximatively 9% coverage of Ir microtriangles on the substrate surface. When comparing the optical transmittance of the composites made with 0.45 µm vs. 0.70 µm Ir microtriangles (data are not presented here) no difference is pointed out, as is to be expected since the microtrianglesubstrate coverage is equivalent. If the temperature increases, all the samples show similar optical transmittance characters to reach a thickness-dependent minimum above the MIT temperature. The hysteresis areas are approximatively constant, meaning that the matrices of VO2 are preserving their flexibility in temperature. The difference between the extrema of the first derivatives (see Figure 5c,d) of the temperature-dependent optical transmittance shows that the average hysteresis width of the composites is close to 6 °C, equal to that of the VO2 thin films. The MIT temperature is approximatively 75 °C, when the thickness of the VO2 is 200 nm, which proves that the quality of the VO2 component of the composites is preserved. The slight shift of the MIT temperature (75 °C compared to the reference 68 °C) is a direct consequence of a weak strain inside the VO2 thin film, as discussed previously.

Plasmonic Properties of the VO2-Ir Microtriangles Composites
The dependence of the optical absorbance vs. wavelength for different VO2 thicknesses (50, 100 and 200 nm) is presented in Figure 6a. In the 1.5-5.5 µm range, the global absorbance value increases with the thickness. These curves are references useful to estimate the contribution of VO2 films on the absorbance spectra of the composites. These baselines are subtracted from the global absorbance spectra of the composite in order to extract the absorbance spectra of the zones with Ir microtriangles plotted in Figure 6b.
The composites exhibit several surface plasmon resonances that correspond to multiple absorbance peaks. The origin of these localized absorptions lies in the Ir microtriangles component and peak effects of the metallic architecture [29].
The absorbance spectra of the Ir microtriangles array, without matrix contribution, show an absorption peak in the infrared part of the electromagnetic spectrum (Figure 6b). This absorption peak is identified as the localized surface plasmon resonance properties Taking the benefit of the MIT transition of the VO 2 matrix, the composites present modulable LSPR (in position and amplitude) (Figure 6c,d). As the temperature increases, the LSPR peaks of the composites will start to shift to a higher wavelength compared to their room temperature position. The LSPR peak shift is due to the temperature-dependent dielectric characteristics of VO 2 that are transferred to the composites. For a 50-nanometer composite made, including 0.45 µm Ir microtriangles (Figure 6c), the LSPR position modulation (extracted using a Voigt function) is equal to 210 nm (3.34 µm to 3.55 µm). For the same composite, the LSPR amplitude temperature induced modulation varies between 0.18 to 0 (a.u.) (Figure 6d). Cooling the samples from 80 • C to room temperature, induces "a return" of the LSPR peaks back to their original position and amplitude, also revealing the hysteresis of the composites. An active LSPR temperature modulation (position and amplitude) was obtained for all the composite's configurations. The LSPR peak shifts and positions observed from different configurations of the composites are summarized in Table 1. The LSPR adaptability can be effective in the order of several hundreds of nanometers, up to 400 nm of magnitude, a very large scale with respect to the near infrared regime. The position of the LSPR peaks of the VO 2 -Ir composites is solely related to the influence of the VO 2 matrix on the Ir microtriangles plasmonic properties. Ir microtriangles keep their own shape and size, which do not affect the LSPR compared to the system VO 2 -gold nanoparticles. By selecting the appropriate size of the Ir microtriangles and the thickness of the VO 2 layer, the LSPR peaks can be tuned to the desired wavelength, making this VO 2 -Ir composite a promising candidate for the development of specific near infrared surface plasmon resonance-based applications. Taking the benefit of the MIT transition of the VO2 matrix, the composites present modulable LSPR (in position and amplitude) (Figure 6c,d). As the temperature increases, the LSPR peaks of the composites will start to shift to a higher wavelength compared to their room temperature position. The LSPR peak shift is due to the temperature-dependent dielectric characteristics of VO2 that are transferred to the composites. For a 50-nanometer composite made, including 0.45 µm Ir microtriangles (Figure 6c), the LSPR position modulation (extracted using a Voigt function) is equal to 210 nm (3.34 µm to 3.55 µm). For the same composite, the LSPR amplitude temperature induced modulation varies between 0.18 to 0 (a.u.) (Figure 6d). Cooling the samples from 80° C to room temperature, induces "a return" of the LSPR peaks back to their original position and amplitude, also revealing the hysteresis of the composites. An active LSPR temperature modulation (position and amplitude) was obtained for all the composite's configurations. The LSPR peak shifts and positions observed from different configurations of the composites are summarized in Table 1. The LSPR adaptability can be effective in the order of several hundreds of nanometers, up to 400 nm of magnitude, a very large scale with respect to the near infrared regime. The position of the LSPR peaks of the VO2-Ir composites is solely related to the influence of the VO2 matrix on the Ir microtriangles plasmonic properties. Ir mi- Figure 6. Optical absorbance spectra (calculated as Absorbance = 2-log (Transmittance (%))) of composites vs. of VO 2 thin films; (a) Optical absorbance spectra of VO 2 thin films and Al 2 O 3 substrate alone; (b) Optical absorbance spectra of composite and of the Ir microtriangles array; (c) Temperature evolution of the LSPR position of a 50-nanometer composite made with 0.45 µm Ir microtriangles; (d) Temperature evolution of the LSPR amplitude of a 50-nanometer composite made with 0.45 µm Ir triangles. The LSPR position/amplitude are extracted using a Voigt fit function of the temperature dependent absorbance spectra.

Conclusions
Through the combination of Langmuir-Blodgett colloidal lithography and Pulsed Laser Deposition processes, the development of composites based on Vanadium dioxide and Iridium is achieved. The composites have similar characteristic in terms of structure and composition to that of their pure constituents. The similar optical transmittance of the composites and pure VO 2 thin films proves that Vanadium dioxide preserves its integrity and intrinsic properties. The composites show LSPR properties in the infrared part of the electromagnetic spectrum. The position and amplitude of the LSPR peaks can be controlled and modulated through the size of the Iridium microtriangles and the thickness of the VO 2 . Furthermore, the LSPR position and amplitude of this smart composite can be actively tuned and modulated acting on temperature. A small change from 25 to 80 • C of the temperature composites can induce a maximum of 400-nanometer shift in the position of LSPR.