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Article

Influence of ALD Coating Layers on the Optical Properties of Nanoporous Alumina-Based Structures

by
Ana L. Cuevas
1,
María del Valle Martínez de Yuso
2,
Víctor Vega
3,
Ana Silvia González
4,
Víctor M. Prida
4 and
Juana Benavente
5,*
1
Unidad de Nanotecnología, SCBI Centro, Universidad de Málaga, E-29071 Málaga, Spain
2
Servicios Centrales de Investigación, Universidad de Málaga, E-29071 Málaga, Spain
3
Laboratorio de Membranas Nanoporosas, Servicios Científico-Técnicos, Universidad de Oviedo, E-33006 Oviedo, Spain
4
Departmento de Física, Facultad de Ciencias, Universidad de Oviedo, E-33007 Oviedo, Spain
5
Departmento de Física Aplicada I, Facultad de Ciencias, Universidad de Málaga, E-29071 Málaga, Spain
*
Author to whom correspondence should be addressed.
Coatings 2019, 9(1), 43; https://doi.org/10.3390/coatings9010043
Submission received: 5 December 2018 / Revised: 4 January 2019 / Accepted: 11 January 2019 / Published: 15 January 2019
(This article belongs to the Collection Surface and Interface Science and Engineering for the Society of the Future)
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Versions Notes

Abstract

:
Optical changes associated with the surface coating of different metal oxides and nanolayers by the ALD technique of a nanoporous alumina structure (NPAS) obtained by the two-step anodization method were analyzed. The NPASs were coated with: (i) a single layer (SiO2 or TiO2), and (ii) a double layer of SiO2 plus Al2O3 or aluminum doped ZnO (AZO) to estimate the effect of surface layer coverage material, geometrical parameters (pore-size/porosity), and number of layers on light transmission/reflection. Chemical surface characterization of the different NPASs was carried out by analyzing XPS spectra, which allowed us to obtain an estimation of the coating layer homogeneity. Transmittance and spectroscopic ellipsometry measurements were analyzed in order to detect changes in characteristic optical parameters such as band gap, refractive index, and extinction coefficients associated with the material and the characteristics of the single or double coating layers.

1. Introduction

In the last 20 years, a significant number of papers focused on exploring the application of nanoporous materials synthesized by electrochemical techniques such nanoporous anodic alumina structures (NPASs) or porous silicon structures for application in sensing devices have been published [1,2,3]. In particular, the NPASs prepared by the anodization of aluminum foil by the two-step method present had enhanced thermal and chemical resistance as well as tunable optical properties and also had good biocompatibility and a large specific surface area [4,5,6,7,8]. This latter characteristic, the high specific surface area to volume ratio, is of great interest to enhance optical signals when the NPASs are incorporated into sensor devices [9]. In addition, their self-organized nanoporous structure with straight pores and a small pore size dispersion make NPASs excellent platforms for relevant applications (chemical/biological sensors, drug delivery, nanofilters, energy…) and template synthesis methods [10,11,12,13,14,15,16]. Moreover, the optical characteristics of NPASs such as light transmittance, absorbance, or reflectivity can be tools of interest for selective chemical and biochemical applications [9].
On the other hand, external and internal (or pore-walls) surfaces of the NPASs can easily be modified by different techniques such as dip-coating, sol-gel, chemical vapor deposition, or atomic layer deposition to obtain nanoporous structures with the most adequate pore size, chemical surface functionalization, selective transport/rejection of ions, and molecules or optical characteristics for a specific application [17,18,19]. In particular, the surface coating of NPASs by the atomic layer deposition (ALD) technique enables its modification through a broad range of materials (metal oxides, nitrides or sulfides), and has been used to modify both the external and inner surfaces of the NPASs due to its penetration along the nanopores [20,21,22]. As a consequence of the coating layer, a reduction in the pore radius and porosity of these new nanoporous alumina-based structures (NPA-bSs) as well as its effect on the diffusive transport (permselectivity and ion diffusion coefficients, parameters of interest for the membranes and nanofluidic applications), have already been observed [18,21], but changes in these latter parameters also seem to depend on the surface material used for nanopore coverage. Moreover, changes in the optical parameters of the NPASs dependent on thickness, pore size, and pore area percentage (or porosity) have already been reported [23,24]. Consequently, ALD coatings might also modify other characteristic properties of the nanoporous alumina support.
In this work, we describe the change in the optical properties associated with the surface coating of a NPAS by the ALD technique with different metal oxides through a single layer (SiO2 and TiO2) and double layer (SiO2 + Al2O3 and SiO2 + AZO) as a way to establish differences associated with the coating-layer material and layer number, independent of pore size and the porosity of the nanoporous alumina-based structures (NPA-bSs). In both cases, the supporting NPAS was obtained by the two-step aluminum mild anodization method using an oxalic acid solution [4]. Chemical surface modification of the NPA-bSs caused by the ALD treatments were analyzed by the x-ray photoelectron spectroscopy (XPS) technique, which provides information on the homogeneity and purity of the coated layer, while optical characterization was performed directly on NPA-bSs by transmittance and spectroscopic ellipsometry measurements. SiO2 and TiO2 were selected for alumina coverage due to the characteristics of these materials (chemical and thermal stability) as well as the biocompatibility of the first, and the photocatalytic behavior and high refractive index of the latter [25,26,27]. Double layered NPA-bSs were obtained by subsequently coating the NPAS + SiO2 sample with a new layer of a different material, Al2O3 or AZO (a mixture of ZnO and Al2O3, that is of interest in plasmonic materials [28]), which provoked modifications in both the nanostructured surface material and sample geometrical parameters (pore-size/porosity). The set of analyzed samples allowed us to estimate the effect on the optical parameters of samples with a similar pore-size and porosity, but with different (i) surface materials and (ii) number of coating layers.

2. Materials and Methods

2.1. NPAS Fabrication and Surfaces Coating by Atomic Layer Deposition Method

The NPAS substrate used for surface modification was obtained by electrochemical anodization of an aluminum disc (0.5 mm thickness and 25 mm of diameter) of high purity (Al 99.999%, Goodfellow, UK) using a solution of oxalic acid (0.3 M) under an anodization voltage of 40 V. Prior to the first anodization, the Al foil was cleaned and electropolished with isopropanol, ethanol, and a 1:3 vol. solution of perchloric acid in ethanol, respectively. Other chemicals (HCl, CuCl2, CrO3, and H3PO4) were employed at the end of the electrochemical anodization process for the selective removal of the aluminum substrate and bottom oxide barrier layer. Figure 1a–c show a scheme of the anodization process, being the pore radii and interpore distance of the NPAS, rp = dp/2 = (16 ± 2) nm and Dint = (105 ± 5) nm [12], respectively; whereas a pore length Lp of approximately 60 µm was obtained by controlling the duration of the second anodization step, performed under the same anodization conditions as in the first step [18].
ALD coating of the NPAS was performed in a Savannah 100 thermal ALD reactor from Cambridge Nanotech (Waltham, MA, USA), working in exposure mode. High purity argon or nitrogen was employed as the carrier gas, with a typical flow of 50 sccm. For the deposition of the different coating layers, at least two precursors were used, the first of them corresponding to the metal precursor, while the other was H2O, which was employed as an oxidant agent and it is also responsible for the substrate functionalization. In the case of the SiO2 coating deposition, it was also necessary to use an additional oxidant agent, O3, in order to improve the functionalization performed by H2O [29]. The cycle configuration in the ALD exposure mode was defined by three different times for each precursor: t1 (pulse), t2 (exposure), and t3 (purge), as shown in Table 1. Long exposure (t2) and purge (t3) times were employed to assure the diffusion of the gaseous precursors along the high aspect ratio pore channels as well as remove the excess reactants and by-products of the ALD process. The use of exposure mode thus enabled the uniform ALD coating of high aspect ratio porous substrates, in contrast to the conventional flow mode (with only pulse and purge steps), which is adequate for flat or low aspect ratio materials. The precursor temperature and pulse time indicated in Table 1 were selected in order to obtain enough vapor pressure and precursor dose in the reaction chamber.
Figure 1d shows a scheme of a single layer nanoporous alumina-based structure, and to deposit a coating layer thickness of around 5 nm, the number of coating cycles was adjusted according to the growth rates of the respective oxides. For TiO2 deposition, performed at a substrate temperature of 200 °C, a growth rate of 0.05 nm/cycle was obtained, which was the reliability of this value for the NPAS + TiO2 sample already confirmed by the TEM and XPS depth-profile analysis [30,31]. Meanwhile, SiO2 deposition, carried out at 150 °C, yielded a deposition rate of 0.06 nm/cycle, as previously reported [18,29]. For the double layered samples, schematized in Figure 1e, a SiO2 layer was first deposited on the NPAS as described above; afterwards, the samples were coated with Al2O3 or AZO with a layer thickness of about 3.5 nm, which were the corresponding growth rates of the Al2O3 and AZO layers at 200 °C that had been previously studied by means of mechanical profilometry and ellipsometry measurements [32]. It is worth clarifying that the AZO layer consisted of a mixture of Zn and Al oxides obtained by performing 20 deposition cycles of ZnO, followed by one cycle of Al2O3, which corresponded to most of the external surface; through this approach, a doping of around 3% of Al in the ZnO layer was obtained [33,34]. According to previous results by SEM image analysis [30], a single layer coverage caused a reduction in pore size (dp) and porosity (θ) of around 20% and 30%, respectively (dp = (25 ± 2) nm, θ = 6%), while in the case of the double layer, these reductions increased by up to around 30% and 50%, respectively (dp = (21 ± 1) nm, θ = 4%). The supplementary materials show the purities, CAS numbers, and providers of all of the chemicals used (Table S1) as well as the SEM images of the surfaces and cross-sections of some samples and, as an example, the EDX diagram for the NPAS + TiO2 sample (Figure S1).

2.2. Chemical Surface Analysis

The chemical surface characterization of the NPA-bSs samples was performed by analyzing the XPS spectra obtained with a Physical Electronics Spectrometer (PHI 5700, Physical Electronics, Chigasaki, Japan) with x-ray MgKα radiation as the excitation source (300 W, 15 kV, 1253.6 eV). High-resolution spectra were recorded by a concentric hemispherical analyzer. operating in the constant pass energy mode at 29.35 eV, with the diameter of the analyzed area of 720 µm. Binding energies were determined with respect to the position of the adventitious C 1s peak at 285.0 eV (accurate ± 0.1 eV), maintaining the residual pressure in the analysis chamber below 5 × 10−7 Pa during data acquisition. Non-destructive XPS measurements were performed at a given take-off angle ϕ = 45° for the reason of spectrometer optimization. The software package used for data acquisition and analysis was the PHI ACCESS ESCA-V7.0 F. The Shirley-type background was subtracted from the signals, and the recorded spectra were fitted using Gauss–Lorentz curves for a more precise binding energy (BE) determination of the core levels of the different element [35]. The sensitivity factor area for each of the measured spectral regions was considered to determine the atomic concentration percentages of the different elements on the surfaces of the samples.
Although XPS is a surface sensitive technique, a depth profile study can also be performed by means of ion gun etching (a sample-destructive testing process), which analyzes a new sample surface after each ion gun etch cycle. The XPS depth-profile analysis revealed subsurface characteristics that provided information on the nanolayered structures or surface contamination [36]. For this reason, XPS depth-profile analysis for the NPAS + SiO2 sample was carried out by argon sputtering for 10 min (working conditions: 4 kV and 1.5 mA).

2.3. Spectroscopic Ellipsometry Measurements

For the characterization of the optical properties of the different NPA-bSs, spectroscopic ellipsometry (SE) measurements (accuracy of 5 decimals) were performed with a commercial spectroscopic ellipsometer (Sopra-Semilab GES 5E, Sopra-Semilab, Budapest, Hungary) for wavelengths covering the visible to near-ultraviolet regions (between 200 and 1000 nm) at a fixed incidence angle of 70°. The measurements were directly performed on the NPA-bSs, without employing any other substrate. Winelli software 2.2.0.7 (Sopra-Semilab) was used for the real and imaginary parts of the complex refraction index determination (accuracy of 4 decimals) from the experimental parameters.

2.4. Transmittance Measurements

Transmittance spectra of the NPA-bSs were recorded with a Varian Cary 5000 spectrophotometer (Agilent Technologies, Santa Clara, CA, USA) provided with an integrating sphere of Spectralon for a wavelength interval of 250–1500 nm. Transmittance spectra were measured for NPA-bSs, and no other substrate was used for these measurements.

3. Results and Discussion

3.1. Chemical Characterization of the Nanoporous Alumina-Based Structures

The XPS technique was used for chemical surface characterization of the alumina-based nanoporous structures to obtain information on the homogeneity of the coating layer. Atomic concentration percentages (A.C.%) of the different elements present on the surfaces of the studied NPA-bSs were determined by analyzing the XPS spectra, taking into account the area of the corresponding signals [37]. Table 2 only shows the A.C.% obtained for the characteristic elements of each sample (O and Si, Ti, Al, and Zn, depending on the sample, and consequently a 100% value was not reached); moreover, the presence of other non-characteristic coating layer material elements or impurities (P, Cl…with A.C.% < 0.5 as well as nitrogen and carbon with higher percentages) associated with sample processing or environmental contamination were also detected, as has already been reported for commercial and experimental inorganic and polymeric samples by different authors [37,38,39]. Results collected in Table 2 showed rather good coverage of the alumina support by the TiO2 and the SiO2 single layers according to the low Al% obtained, but the high content of carbonaceous species from contamination hindered the corroboration of correct material stoichiometry; in fact, the high carbon percentage detected on the sample surfaces is discussed in the next paragraph. For example, the core level spectra of Ti, O, Al, and C for the NPAS + TiO2 sample are given as supplementary information (Figure S2), where a clear and well defined peak at 285.0 eV (Figure S2d) associated with aliphatic carbon as well as a shoulder at 288.5 eV could be observed.
To determine the effect of contamination on the coating layers, destructive depth-profile analysis for the NPAS + SiO2 sample was also performed, and Figure 2a shows the variation with the Ar sputtering time of the atomic concentration percentages of its characteristic elements, silicon, aluminum, and oxygen, but the changes in the carbon percentage, which is an element commonly observed and associated with contamination (both environmental and manufacture contamination), are also indicated. This point was confirmed by the significant reduction in the C% (around 60%) after approximately 0.5 min Ar sputtering, which caused a notable increase in the other three elements, Al%, Si%, and O% in part (ii), confirming the surface contamination contribution. Subsequently, a reduction in Si% was detected once the external SiO2-cover layer was eliminated, and a practically constant value associated with nanopore coverage was finally reached, while the higher constant value determined for the Al% was due to the solid body of the NPASs, as it is schematically indicated in Figure 2b. In the case of carbon%, the practically constant residual value can be attributed to impurities related to the chemicals used for surface coverage by the ALD method. On the other hand, due to the inhomogeneity of the coating layer, direct sputtering time-depth correlation was not possible since the applied factor depends on the specific material, although an analyzed depth of around 25–30 nm was assumed. From these results, a thickness of around 5–7 nm for the superficial silica layer in the NPAS + SiO2 sample was estimated, which is in agreement with previous results obtained for the NPAS + TiO2 sample [30]. Moreover, the values in Figure 2a also show that once the environmental contamination layer was eliminated (part (i)), the stoichiometry ratios for the bulk NPA-bS (part (ii)) characteristic elements matched adequately.

3.2. Optical Characterization of the Nanoporous Alumina-Based Structures

The effect of various coating materials and layers on the transmittance characteristics of the nanoporous alumina support structure was investigated by comparing the corresponding transmittance curves. Figure 3 shows the variation of light transmittance % with the wavelength for the different samples, where the similarity of the curve shape and the practical constancy of the transmittance value for wavelengths higher than 500 nm for the NPAS + SiO2, NPAS + TiO2, and NPAS + SiO2 + Al2O3 samples could be observed, but this value increased to around 800 nm in the case of the NPAS + SiO2 + AZO sample. Taking into account the similar values of geometrical parameters presented by the NPAS + SiO2 and NPAS + TiO2 samples at one side, or the NPAS + SiO2 + Al2O3 and NPAS + SiO2 + AZO samples on the other side, differences in the transmittance percentages must be caused by the coating layer material. In this context, a comparison of the transmittance curves for the NPAS + TiO2 sample and the NPAS support (grey dashed line) for the whole wavelength range is presented as supplementary information (Figure S3), where the NPAS support values at high wavelengths were practically similar to those obtained for the NPAS + SiO2 sample. Moreover, the inset in Figure 3 showed a magnification of the transmittance results obtained at wavelengths lower than 500 nm for the analyzed NPAb-Ss and the NPAS support where differences/similarities depending on the coating layer material could be observed.
For comparative reasons, the percentage of transmitted light at two characteristic wavelengths, one in the visible region (λ = 550 nm, which corresponds to the optimum human-eye response) and the other in the infrared region (λ = 950 nm) as well as the band gap value (both in nm and eV units), which represents the energy threshold for the light adsorption of a given material, are indicated in Table 3. Clear differences can be observed in the values obtained when both SiO2 or TiO2 single-layers, and both double-layer coated nanoporous structures (SiO2 + Al2O3 or SiO2 + AZO) are compared, which demonstrate the importance of the coating-layer material for optical applications of NPA-bSs, taking into account the similarity of their geometrical parameters (pore size, porosity, and thickness) of the analyzed samples. On the other hand, differences in transmittance % between the two selected wavelengths were around 3% for NPAS + SiO2, NPAS + TiO2 and NPAS + SiO2 + Al2O3, but this difference increased up to 13% in the case of the NPAS + SiO2 + AZO sample. It should be indicated that a rather similar transmittance percentage (around 85%) was obtained for the AZO films deposited on quartz glasses (Al content between 0.9% and 4.4%) [40]. Moreover, differences in band-gap values for the studied nanostructures depending on the coating layer material could also be observed in Table 3, which supports the possible election of a particular material for a specific optical application. Taking into account the referenced band-gap values for the pure ceramic oxides of the coating layers [41]: SiO2 (155–119 nm), TiO2 (413–330 nm), Al2O3 (177–133 nm), and AZO (379–346 nm for the Al content varying between 0 and 4.4%), our results showed rather good similarity for the NPAS + TiO2 and NPAS + SiO2 + AZO samples, but differences seemed to exist when the other samples were considered, which might be related to the surface contamination already detected by the XPS measurements.
On the other hand, different characteristic material parameters such as the refractive index, the extinction coefficient, and the real and imaginary parts of the complex dielectric constant (ε) can be determined by the SE technique. SE is a nondestructive and noninvasive technique that allows changes to be measured in the light polarization due to its reflection from a solid structure as is schematically shown in Figure 4a for a single structure and in Figure 4b for the layer coverage of a support. The interactions of polarized light with a sample include the parallel (p) and normal (n) components of the electric field for both incident (i) and reflected (r) light. [42]. Ellipsometric measurements consider two main parameter: angles Ψ and Δ, which are related with differential changes in light amplitude and phase through the following expression [42]:
tan(Ψ)eiΔ = rp/rs
where tan(Ψ) is the amplitude ratio upon reflection and Δ = δp − δs is the phase shift difference, where rp and rs are the amount (intensity) of reflected light polarized in the perpendicular and parallel planes with respect to the plane of incidence, respectively.
Figure 5 shows a comparison of the wavelength dependence of measured parameters, cos(Δ) and tan(Ψ) as well as the determined Δ and Ψ angles, where differences dependent on the single-layer or double-layer coated samples as well as the material layers can be observed. Oscillatory values for cos(Δ) were similar to those reported in the literature for anodized nanoporous aluminum oxide films [43], where oscillation separation or maximum–minimum height in the case of tan(Ψ) representation seems to be related to the time employed during electrochemical etching, which is related to the pore-size/porosity of the sample. Figure 5c,d show the variation of Ψ and Δ with the wavelength for single and double double-layer coated samples, showing behavior rather similar to that referenced in the literature [42]. Moreover, the effect of the incident light ellipsometry angle Φi on the cos(Δ) and tan(Ψ) measured parameters as a function of the wavelength can also be considered by comparing the values obtained for the NPA-bS + TiO2 sample at 70° with those previously determined at 65° [30], as shown in Figure 5e,f. As observed, increasing Φi hardly modified the shape of the curves, but increased the tan(Ψ) values.
As previously indicated, the sample refractive index (n), extinction coefficient (k), and dielectric constant can be determined from SE measurements using the ellipsometer software (Winelli, Sopra-Semilab). Figure 6 shows the dependence of the n and k parameters on the wavelength for the studied nanoporous alumina-based samples, where rather constant values for the refractive index for the wavelength ranging between 375 and 1000 nm was obtained for the NPAS + SiO2, NPAS + TiO2, and NPAS + SiO2 + Al2O3 samples (<nNPAS+SiO2> = 1.34, <nNPAS+SiO2+Al2O3> = 1.44, and <nNPAS+TiO2> = 1.70). These values had rather good agreement with those reported in the literature for pure materials and followed the same tendency [44]; moreover, this parameter seemed to be practically independent of the incident angle according to the values previously obtained for the NPAS + TiO2 sample at 65° (n = 1.72). Disparity in the shape of the n curves is an indication of the differences in the material characteristics, layer thickness, layer interference, or crystallinity [45]. Values of n and k at the two selected wavelengths (550 and 950 nm) are indicated in Table 4 for comparative reasons. Moreover, Figure 6 also shows the low wavelength dependence for the n and k parameters obtained for the NAPS + SiO2 + Al2O3 sample, that is, for the alumina/silica/alumina sandwiched nanoporous structure as well as the practically constant value of the NAPS + TiO2 sample for the range 400–800 nm as already reported by Taherniya and Raoufi [46], who studied changes in the optical properties of TiO2 thin films obtained by the sol-gel technique associated with film thickness (50, 100 and 150 nm), which also affected the porosity (around 40%, 28%, and 21%, respectively). These authors reported an increase of around 12% in the refraction index and a decrease of 55% in the extinction coefficient with the increase of film thickness (λ = 550 nm) as determined from measurements carried out with samples deposited on a glass substrate, but thickness hardly affected the band gap value (increase of 2.5% for the whole range); moreover, electrical susceptibility (or the real part of the dielectric constant) also increased 38% with the film thickness.
The SE results also provide information on the real and imaginary parts of the dielectric constant taking into account that ε = (n + i·k)2 [42]. Table 5 shows the εr and εi values at the two selected wavelengths, where clear differences among the analyzed samples can be observed. Consequently, both geometrical parameters and material seemed to cause modification in the dielectric constant values of NPA-bSs.

4. Conclusions

The atomic layer deposition (ALD) technique seems to be an adequate way for the surface modification of nanoporous alumina structures (both external and pore walls) with a high aspect ratio (around 2000) by covering them with one or two layers of different metal oxides (SiO2, TiO2, Al2O3, or AZO). Surface coverage was analyzed by XPS measurements at a given take-off angle of 45° to extract information on the coating layer homogeneity; moreover, XPS depth-profile measurements demonstrated the superficial character of most of the sample impurities associated with fabrication and environmental contamination as well as the presence of coating materials along the pore-walls.
All of the studied samples exhibited high light transmittance (between 86% and 95%), but differences were obtained depending on the material coating layer for samples with a similar pore size or porosity, which seems to be an indication of the higher influence of the layer material on the geometrical parameters. As expected, differences in band gap values for the analyzed samples also existed, and the following sequence was determined: NPAS + SiO2 > NPAS + SiO2 + AZO ≈ NPAS + SiO2 + Al2O3 > NPAS + SiO2. The refraction index, n, of the different samples and its dependence on the wavelength in the visible and near IR regions (250–1000 nm) was determined by spectrometric ellipsometry measurements, and the obtained values showed rather adequate concordance with those referred for the corresponding pure ceramic oxides, although differences in the shape of the curve for samples with similar geometrical parameters were indicative of the repercussion of the particular material and layer characteristics (thickness, crystallinity…). Differences in other optical parameters depending on the coating layer material and nanostructure of the sample were also determined, which demonstrated the importance and interest in the appropriate selection of a coating layer material for specific optical applications of alumina-based nanoporous structures.

Supplementary Materials

The following are available online at https://www.mdpi.com/2079-6412/9/1/43/s1, Figure S1: (a) top-view SEM image of the NPAS + TiO2 sample. The inset shows a high magnification SEM image of the parallel aligned nanopores taken at the cross-section: (b) EDX spectrum of (a), indicating the presence of carbon, titanium, oxygen, and aluminum. The Au peaks arise from the sputtered conductive gold layer deposited prior to SEM characterization. (c) Cross-section SEM image of the whole thickness of the NPAS + TiO2 sample. (d) EDX line-scan of the Al, O, and Ti distribution measured along the dashed red line in (c). Figure S2: Core level spectra of elements found on the surface of the NPAS + TiO2 sample: (a) Ti 2p, (b) O 1s, (c) Al 2p, and (d) C 1s. Figure S3: Light transmittance (%) as a function of wavelength for NPAS (grey dotted line) and NPAS + TiO2 (black dense line) samples. Table S1: Chemicals employed in the different NPAM synthesis and ALD deposition steps.

Author Contributions

A.S.G. and V.V. synthesized the NPA support and carried out the ALD-coating process, under the supervision of V.M.P. V.V. performed electron microscopy analysis of the samples. J.B. was responsible of XPS and optical measurements, carried out by M.d.V.M.d.Y. and A.L.C., respectively. V.M.P. and J.B. conceived, designed and discussed the experiments. All authors contributed in co-writing of the manuscript and gave approval to the final revision.

Funding

The financial support is under the Spanish MINECO research project No. MAT2016-76824-C3-3 R.

Acknowledgments

The technical assistance of the SCTs’ common research services for the University of Oviedo is acknowledged.

Conflicts of Interest

The authors declare no conflict of interest.

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Coatings 09 00043 g001 550
Figure 1. (a–c) Scheme of the NPAS fabrication and final structure; (d) nanoporous alumina-based structure (NPA-bS) after ideal single layer deposition; (e) NPA-bS after ideal double layer deposition.
Figure 1. (a–c) Scheme of the NPAS fabrication and final structure; (d) nanoporous alumina-based structure (NPA-bS) after ideal single layer deposition; (e) NPA-bS after ideal double layer deposition.
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Coatings 09 00043 g002 550
Figure 2. (a) Variation of the atomic concentration percentages of silicon, aluminum, carbon, and oxygen with the XPS sputtering time for the NPAS + SiO2 sample; (b) schemes of the XPS depth-profile analysis for: (i) the external surface, and (ii) during the argon etching process for the NPAS + SiO2 sample.
Figure 2. (a) Variation of the atomic concentration percentages of silicon, aluminum, carbon, and oxygen with the XPS sputtering time for the NPAS + SiO2 sample; (b) schemes of the XPS depth-profile analysis for: (i) the external surface, and (ii) during the argon etching process for the NPAS + SiO2 sample.
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Coatings 09 00043 g003 550
Figure 3. Variation of light transmittance with wavelength for: NPAS + SiO2 (cyan); NPAS + TiO2 (black); NPAS + SiO2 + Al2O3 (yellow); NPAS + SiO2 + AZO (pink) samples; and the NPAS support (grey dashed line). The inset shows the transmittance % for the lowest wavelength interval (200–500 nm).
Figure 3. Variation of light transmittance with wavelength for: NPAS + SiO2 (cyan); NPAS + TiO2 (black); NPAS + SiO2 + Al2O3 (yellow); NPAS + SiO2 + AZO (pink) samples; and the NPAS support (grey dashed line). The inset shows the transmittance % for the lowest wavelength interval (200–500 nm).
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Coatings 09 00043 g004 550
Figure 4. Scheme of spectroscopy ellipsometry measurement for: (a) the homogeneous sample; (b) the monolayer surface coated sample.
Figure 4. Scheme of spectroscopy ellipsometry measurement for: (a) the homogeneous sample; (b) the monolayer surface coated sample.
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Coatings 09 00043 g005a 550Coatings 09 00043 g005b 550
Figure 5. Wavelength dependence of cos(Δ) (a), tan(Ψ) (b), Δ (c) and Ψ (d) for: NPAS + SiO2 (cyan), NPAS + TiO2 (black), NPAS + SiO2 + Al2O3 (dark yellow), and NPAS + SiO2 + AZO (pink) samples. Comparison of the measured cos(Δ) (e) and tan(Ψ) (f) values for the NPAS + TiO2 sample at two different incident angles (65° and 70°).
Figure 5. Wavelength dependence of cos(Δ) (a), tan(Ψ) (b), Δ (c) and Ψ (d) for: NPAS + SiO2 (cyan), NPAS + TiO2 (black), NPAS + SiO2 + Al2O3 (dark yellow), and NPAS + SiO2 + AZO (pink) samples. Comparison of the measured cos(Δ) (e) and tan(Ψ) (f) values for the NPAS + TiO2 sample at two different incident angles (65° and 70°).
Coatings 09 00043 g005aCoatings 09 00043 g005b
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Figure 6. Wavelength dependence of (a) the refraction index, n, and (b) the extinction coefficient, k, for the NPAS + SiO2 (cyan), NPAS + TiO2 (black), NPAS + SiO2 + Al2O3 (dark yellow), and NPAS + SiO2 + AZO (pink) samples.
Figure 6. Wavelength dependence of (a) the refraction index, n, and (b) the extinction coefficient, k, for the NPAS + SiO2 (cyan), NPAS + TiO2 (black), NPAS + SiO2 + Al2O3 (dark yellow), and NPAS + SiO2 + AZO (pink) samples.
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Table
Table 1. Times and temperatures employed in the ALD processes for the different coating materials, where t1 is the precursor pulse time; t2 is the exposition time; and t3 is the purge lapse. For each material, the times used in the exposure to each precursor are shown by columns, whereas the precursor and substrate temperatures are indicated by lines.
Table 1. Times and temperatures employed in the ALD processes for the different coating materials, where t1 is the precursor pulse time; t2 is the exposition time; and t3 is the purge lapse. For each material, the times used in the exposure to each precursor are shown by columns, whereas the precursor and substrate temperatures are indicated by lines.
Material
(Substrate Temperature)		Precursors
(Precursor Temperature)		t1 (s)t2 (s)t3 (s)
ZnO (200 °C)H2O (60 °C)0.190180
(C2H5)2Zn (25 °C)0.0590180
Al2O3 (200 °C)H2O (60 °C)0.190180
Al2(CH3)6 (25 °C)0.0590180
TiO2 (200 °C)H2O (60 °C)160120
Ti[OCH(CH3)2]4 (75 °C)16060
SiO2 (150 °C)H2O (60 °C)160120
O3 (25 °C)0.160120
H2N(CH2)3Si(OC2H5)3 (100 °C)260120
Table
Table 2. Atomic concentration percentages (A.C.%) of the characteristic elements of each alumina-based nanoporous structure *.
Table 2. Atomic concentration percentages (A.C.%) of the characteristic elements of each alumina-based nanoporous structure *.
SampleO (%)Al (%)Si (%)Ti (%)Zn (%)
NPAS + SiO228.82.14.0––
NPAS + TiO252.21.5–21.4–
NPAS + SiO2 + Al2O329.16.50.3––
NPAS + SiO2 + AZO30.59.02.3–0.7
* Carbon, nitrogen, and other non-characteristic elements (P, Cl…) found on the surfaces of the analyzed samples are not indicated.
Table
Table 3. Values of light transmitted % at two wavelengths (550 and 950 nm) and the band gap for the studied nanoporous alumina based structures.
Table 3. Values of light transmitted % at two wavelengths (550 and 950 nm) and the band gap for the studied nanoporous alumina based structures.
SampleT (%) at 550 nmT (%) at 950 nmBand Gap (nm/eV)
NPAS + SiO292.094.6281.8/4.40
NPAS + TiO283.386.1346.8/3.58
NPAS + SiO2 + Al2O386.489.1308.8/4.02
NPAS + SiO2 + AZO78.090.1312.5/3.87
Table
Table 4. Values of the refractive index, n, and extinction coefficient, k, at two wavelengths (550 and 950 nm) for the studied nanoporous alumina based structures.
Table 4. Values of the refractive index, n, and extinction coefficient, k, at two wavelengths (550 and 950 nm) for the studied nanoporous alumina based structures.
Samplen (at 550 nm)k (at 550 nm)n (at 950 nm)k (at 950 nm)
NPAS + SiO21.3120.6751.3641.109
NPAS + TiO21.6930.6631.7040.837
NPAS + SiO2 + Al2O31.3980.3571.5270.592
NPAS + SiO2 + AZO0.8920.8001.5601.095
Table
Table 5. Real (εr) and imaginary (εi) component values of the dielectric constant at the two wavelengths of 550 and 950 nm for the studied nanoporous alumina based structures.
Table 5. Real (εr) and imaginary (εi) component values of the dielectric constant at the two wavelengths of 550 and 950 nm for the studied nanoporous alumina based structures.
Sampleεr (at 550 nm)εr (at 950 nm)εi (at 550 nm)εi (at 950 nm)
NPAS + SiO21.2820.6301.7793.025
NPAS + TiO22.4282.2052.2432.853
NPAS + SiO2 + Al2O31.8261.9820.9971.807
NPAS + SiO2 + AZO0.1561.2351.4273.418

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Cuevas, A.L.; Martínez de Yuso, M.d.V.; Vega, V.; González, A.S.; Prida, V.M.; Benavente, J. Influence of ALD Coating Layers on the Optical Properties of Nanoporous Alumina-Based Structures. Coatings 2019, 9, 43. https://doi.org/10.3390/coatings9010043

AMA Style

Cuevas AL, Martínez de Yuso MdV, Vega V, González AS, Prida VM, Benavente J. Influence of ALD Coating Layers on the Optical Properties of Nanoporous Alumina-Based Structures. Coatings. 2019; 9(1):43. https://doi.org/10.3390/coatings9010043

Chicago/Turabian Style

Cuevas, Ana L., María del Valle Martínez de Yuso, Víctor Vega, Ana Silvia González, Víctor M. Prida, and Juana Benavente. 2019. "Influence of ALD Coating Layers on the Optical Properties of Nanoporous Alumina-Based Structures" Coatings 9, no. 1: 43. https://doi.org/10.3390/coatings9010043

APA Style

Cuevas, A. L., Martínez de Yuso, M. d. V., Vega, V., González, A. S., Prida, V. M., & Benavente, J. (2019). Influence of ALD Coating Layers on the Optical Properties of Nanoporous Alumina-Based Structures. Coatings, 9(1), 43. https://doi.org/10.3390/coatings9010043

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