# TiO2 and TiO2-Doped Films Able to Kill Bacteria by Contact: New Evidence for the Dynamics of Bacterial Inactivation in the Dark and under Light Irradiation

Authors: John Kiwi; Sami Rtimi; Rosendo Sanjines; Cesar Pulgarin
Journal: International Journal of Photoenergy
 (2014)

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## Abstract

This paper addresses recent developments in the design, evaluation, and characterization of flexible, uniform polyethylene-TiO2 (PE-TiO2), TiO2-In2O3, and TiO2-polyester able to inactivate bacteria under band gap irradiation and in the dark. The preparation of these bactericide films by sol-gel or by sputtering techniques is reported. The E. coli loss of viability kinetics under low intensity and actinic light is evaluated. Evidence for kinetics of the major steps leading to bacterial disinfection in the dark is presented by electron microscopy (TEM). The film surface properties were characterized by surface techniques like EM, DRS, XPS, ATR-IR, CA, AFM, XRD, and XRF. The surface characterization allows the correlation of the film surface morphology with the self-disinfection performance. The events taking place at the cell wall leading to bacterial inactivation when in contact with the TiO2 films are presented and the steps related to the bond stretching preceding bond scission identified by ATR-IR.


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## Body

## 1. Introduction

The ambient contamination by biofilms spreading bacteria for long times in hospitals, schools, and many public places requires the preparation of more effective adhesive antibacterial andantifungal films showing an improved kinetics/performance/stability. Antimicrobial nanoparticulate films preparation is a topic of increasing attention since they can reduce/eliminate the formation of infectious bacterial biofilms leading to hospital acquired infections (HAI) [1, 2]. These nosocomial infections are due to antibiotic resistant bacteria. They are becoming more frequent during the last decade and contribute to the increase in hospital care costs. Touching by hand a second person or touching surfaces and walls of hospital deposits bacteria that to a great extent disappear in about 5–8 hours since they do not find the surface humidity or residual C-compounds necessary to feed their metabolism. But there are many and resistant pathogenic bacteria that form stable and robust biofilms secreting proteins to cover/protect themselves and spread pathogenic bacteria like the Gram-positiveStaphylococcus. Biofilms are formed from a complex mixture of proteins, saccharides, amino acids, and other extracellular polymeric substances.The formation of these pathogenic biofilms may be avoided precluded by robust self-disinfecting films. Disinfecting surfaces have been shown to inhibit microbial growth, since bacterial concentrations found in hospital rooms are not high. Regrowth of bacteria was not observed on effective antibacterial films [1–3]. Therefore, the investigation of self-disinfecting surfaces as presented in this study is warranted [4–11].The colloidal deposition of TiO2 on textiles, polymers, glass, and steel plates is used to prepare self-disinfectant and self-cleaning surfaces showing a significant photocatalytic activity [12–14]. But the colloid or sol-gel preparations deposited films are not mechanically stable, nor reproducible, and present low uniformity and little adhesion since they can be wiped off by a cloth or thumb [15]. This shortcoming of the colloidal depositions moved us to work on the sputtering of antibacterial films to overcome the shortcomings of colloidal loaded films. The problem to fix colloids on surfaces encountered during CVD depositions is due to the heat needed for the film fixation on the substrate. The substrate has to be resistant to heat at temperatures that textiles, polymer films, polyethylene 3D, and polyurethane complex shaped objects do not withstand. Deposition by sputtering of metal/oxides/semiconductors on nonheat resistant substrates is possible since plastic/polymer thin films and textile fabrics can be heated for short times only up to 120–140°C.In a typical CVD process, the substrate is exposed to the volatile precursors. Due to the heat applied the precursor decomposes on the substrate surface depositing amorphous/polycrystalline coatings. The volatile species condense on the substrate having a lower temperature. The disadvantages of conventional CVD deposition are the high investment costs and the high temperatures needed besides the large amount of heat used requiring costly cooling systems. Recently, Foster et al. [16], Yates et al. [17], Dunlop et al. [18], and Brook et al. [19] have reported antibacterial TiO2, Ag, and Cu coatings on glass and polymer films depositing the metal/oxides by CVD.TiO2-films preparation and evaluation have gained much attention during the last decade since they have been reported to be effective in reducing hospital-acquired infections (HAI) [1–3, 20–23]. The particular interest in TiO2-textiles is based on the fact that the porous hydrophilic structure as found in cotton textiles provides a suitable environment for bacterial growth. TiO2-nanoparticles have shown recently to produce strong antibacterial effects in textiles designed for medical applications [3–18].The improvement in the performance and utility of antibacterial TiO2 and TiO2-doped films is to produce a film microstructure inducing an accelerated bacterial inactivation concomitant with a cytotoxicity within the accepted standards accepted in medical applications [24–26]. The film uniformity, stable structure, and adhesive properties are currently investigated by academic institutions and by pharmaceutical companies for medical devices and implants covered with antibacterial coatings [27]. The improvement on the microstructure of TiO2 films leading to thinner films inducing a faster bacterial inactivation kinetics (doped or not) compared with more traditional DC sputtering and DCP sputtering is being explored in our laboratory. The recent development of highly ionized pulsed plasma magnetron sputtering (HIPIMS) producing high-density plasma to deposit TiO2 films on polyester is presented in this study [28]. The development of HIPIMS in the last decade is due to the growing demand for high quality anticorrosive uniform films [29]. In the case of HIPIMS, pulses from one microsecond up to milliseconds generate current densities able to induce ~1018 e−/m3. This is 102–104 times higher than the electron density obtained by conventional DC-sputtering [30]. Until now, the deposition by direct current magnetron sputtering (DC) pulse sputtering (DCP) and HIPIMS of nanoparticles on surfaces has not been widely used to coat hospital textile clothing, glass, and metal-plates antibacterial surfaces.This study will describe results obtained in our laboratory addressing TiO2 self-disinfection due to (a) transparent nonscattering polyethylene (PE) sputtered TiO2 films, (b) TiO2-In2O3 polyester, and (c) nanoparticulate TiO2 polyester.


## 2. Materials and Methods

### 2.1. Sputtering Details, Support Materials, and XRF Determination of Film Loading

The HIPIMS sputtering unit [29, 30] with a CMS-18 Vacuum system from Kurt Lesker Ltd was evacuated to 5.8 × 10−3 mbar. The Ti target was 50 mm in diameter, 99.99% pure from K. Lesker Ltd. UK, and used in reactive O2 atmosphere. The HIPIMS installation was operated at 500 Hz with pulses of 100 microseconds separated by 1.9 ms, leading to a TiO2 layer of 15 nm after 60 s. The average power was 87.5 W (5 A × 350 V) and the power per pulse of 100 microseconds was 1750 W. The calibration of the Ti-film thickness sputtered by HIPIMS was carried out on Si-wafers by a profilometer (Alphastep500, TENCOR). The X-ray fluorescence (XRF) determination of the Ti content in the samples was performed in a PANalytical PW2400 spectrometer.The low density polyethylene (LDPE) consists of highly branched low crystalline semitransparent film with the formula H(CH2–CH2)nH. The (LDPE) 0.1 mm thick was obtained from Longfellow (ET3112019), had a density of 0.92 g/cm3, an upper working temperature of 90°C, and a flowing point of 185°C. The polyester used corresponds to the EMPA test cloth sample number 407. It is a polyester Dacron polyethylene terephthalate, type 54 spun, thickness 130 microns plain weave ISO 105-F04 used for color fastness determinations.


### 2.2. Surface XPS Analysis and ICP-MS of the Eluted Species during Bacterial Inactivation

An AXIS NOVA photoelectron spectrometer (Kratos Analytical, Manchester, UK) equipped with monochromatic AlKα(hν=1486.6eV) anode was used during the study. The electrostatic charge effects on the samples were compensated by means of the low-energy electron source working in combination with a magnetic immersion lens. The carbon C1s line with position at 284.6 eV was used as a reference to correct for charging effects. The XPS spectra for the Ti-species were analyzed by means of spectra deconvolution software (CasaXPS-Vision 2, Kratos Analytical UK). The percentage surface atomic concentration of some elements was determined by fitting of the peak areas using known sensitivity factors [31]. Spectrum background was subtracted according to the Shirley subtraction GL(30) program attached to the Kratos unit [32, 33].The polyethylene fabrics were pretreated in the cavity of the RF-plasma unit (Harrick Corp. 13.56 MHz, 100 W) at a pressure of 1 torr. Oxygen activated by RF-plasma reacts with the PE surface inducing functional PE-surface groups by (a) formation of oxygen containing hydrophilic surface groups and (b) scission of intermolecular PE-bonds due to localized heat segmenting the fibers [34]. PE was also functionalized by UVC irradiation using the 185 nm emission wavelengths from a low-pressure mercury lamp (Ebara Corp. Tokyo, Japan). UVC activation, having a lower energy than the RF-plasma, does not lead to cationic or anionic oxygen species but only to atomic (O) and excited oxygen (O*). The radiant energy at 185 nm provides energies above 241 nm equivalent to 495 kJ/mole or 6.70 eV, the energy required for the splitting of O2→ 2O* [12, 35].Inductively coupled plasma spectrometry (ICP-MS) was used to determine the Ti since it is a sensitive analytical technique because of the low background and high ion transmission. The Finnigan ICPS used was used with a resolution of 1.2 × 105 cps/ppb, detection limit of 0.2 ng/L.


### 2.3. Diffuse Reflectance Spectroscopy (DRS), Electron Microscopy (TEM and HAADF), and XRD of Samples

Diffuse reflectance spectroscopy (DRS) was carried out using a Perkin Elmer Lambda 900 UV-VIS-NIR spectrometer provided for with a PELA-1000 accessory. The absorption of the samples was plotted in Kubelka-Munk (KM) arbitrary unit versus wavelength. Irradiation of the samples was carried out in a tubular cavity of a Suntest Heraeus solar simulator, Hanau, Germany, or in the cavity of a reactor provided with indoor actinic light (white light).Transmission electron microscopy (TEM) was carried out in a Philips CM-12 (field emission gun, 300 kV, 0.17 nm resolution) microscope at 120 kV and was used to measure grain size of the TiO2. The textiles were embedded in epoxy resin 45359 Fluka and the fabrics were cross-sectioned with an ultramicrotome (Ultracut E) and at a knife angle of 35°. Crystal structures were characterized by X-ray diffraction (XRD) and recorded on an X’PertMPD PRO from PANalytical equipped with a secondary graphite (002) monochromator.


### 2.4. Contact Angle (CA) and ATR-IR Measurements

The hydrophilicity of the TiO2 films was determined by the water droplet contact angle (CA). The CA of TiO2 films on the substrate was determined by the sessile drop method on a DataPhysics OCA 35 unit. FTIR spectra were measured in a Portmann Instruments AG spectrophotometer equipped with a Specac attachment (the prim was a 45° one pass diamond crystal). Spectra were taken by 256 scans with a resolution of 2 cm−1 in the range 900–4000 cm−1. The position of the IR peaks was found by the second derivative of the spectra after Fourier deconvolution.


### 2.5.E. coli Loss of Viability Evaluation

The samples ofEscherichia coli (E. coli K12) were obtained from the Deutsche Sammlung von Mikroorganismen und Zellkulturen GmbH (DSMZ) ATCC23716, Braunschweig, Germany, to test the antibacterial activity of the TiO2-polyethylene and TiO2-polyester films according to previous work reported by our laboratory [9]. Serial solutions were prepared in tryptone solution and the samples plated on agar Plate-Count-Agar (PCA, Merck, Germany). The bacterial counting data reported were obtained by the replicate of 3 experimental runs.To verify that no regrowth ofE. coli occurs after the total inactivation observed in the first disinfection cycle, the samples were incubated for 24 hours at 37°C. After vortexing these samples in a 2 mL Eppendorf tube, the fabrics were placed on a PCA Petri dish, incubated overnight at 37°C to verify if still some bacteria remained adhered to the PE-TiO2 surface. No bacterial colonies were observed. This indicates that the bacteria inoculated on the PE-TiO2 surface remain in the Eppendorf tube. Then the bacterial 100 microliters suspensions were deposited on 3 Petri dishes to obtain replicates of the bacterial counting. No bacterial regrowth was observed.Statistical analysis of the results was performed for the decrease of the bacterial CFU values reporting the standard deviation values for the runs showing the fastest bacterial inactivation. The average values were compared by one-way analysis of variance and with the value of statistical significance.


## 2.1. Sputtering Details, Support Materials, and XRF Determination of Film Loading

The HIPIMS sputtering unit [29, 30] with a CMS-18 Vacuum system from Kurt Lesker Ltd was evacuated to 5.8 × 10−3 mbar. The Ti target was 50 mm in diameter, 99.99% pure from K. Lesker Ltd. UK, and used in reactive O2 atmosphere. The HIPIMS installation was operated at 500 Hz with pulses of 100 microseconds separated by 1.9 ms, leading to a TiO2 layer of 15 nm after 60 s. The average power was 87.5 W (5 A × 350 V) and the power per pulse of 100 microseconds was 1750 W. The calibration of the Ti-film thickness sputtered by HIPIMS was carried out on Si-wafers by a profilometer (Alphastep500, TENCOR). The X-ray fluorescence (XRF) determination of the Ti content in the samples was performed in a PANalytical PW2400 spectrometer.The low density polyethylene (LDPE) consists of highly branched low crystalline semitransparent film with the formula H(CH2–CH2)nH. The (LDPE) 0.1 mm thick was obtained from Longfellow (ET3112019), had a density of 0.92 g/cm3, an upper working temperature of 90°C, and a flowing point of 185°C. The polyester used corresponds to the EMPA test cloth sample number 407. It is a polyester Dacron polyethylene terephthalate, type 54 spun, thickness 130 microns plain weave ISO 105-F04 used for color fastness determinations.


## 2.2. Surface XPS Analysis and ICP-MS of the Eluted Species during Bacterial Inactivation

An AXIS NOVA photoelectron spectrometer (Kratos Analytical, Manchester, UK) equipped with monochromatic AlKα(hν=1486.6eV) anode was used during the study. The electrostatic charge effects on the samples were compensated by means of the low-energy electron source working in combination with a magnetic immersion lens. The carbon C1s line with position at 284.6 eV was used as a reference to correct for charging effects. The XPS spectra for the Ti-species were analyzed by means of spectra deconvolution software (CasaXPS-Vision 2, Kratos Analytical UK). The percentage surface atomic concentration of some elements was determined by fitting of the peak areas using known sensitivity factors [31]. Spectrum background was subtracted according to the Shirley subtraction GL(30) program attached to the Kratos unit [32, 33].The polyethylene fabrics were pretreated in the cavity of the RF-plasma unit (Harrick Corp. 13.56 MHz, 100 W) at a pressure of 1 torr. Oxygen activated by RF-plasma reacts with the PE surface inducing functional PE-surface groups by (a) formation of oxygen containing hydrophilic surface groups and (b) scission of intermolecular PE-bonds due to localized heat segmenting the fibers [34]. PE was also functionalized by UVC irradiation using the 185 nm emission wavelengths from a low-pressure mercury lamp (Ebara Corp. Tokyo, Japan). UVC activation, having a lower energy than the RF-plasma, does not lead to cationic or anionic oxygen species but only to atomic (O) and excited oxygen (O*). The radiant energy at 185 nm provides energies above 241 nm equivalent to 495 kJ/mole or 6.70 eV, the energy required for the splitting of O2→ 2O* [12, 35].Inductively coupled plasma spectrometry (ICP-MS) was used to determine the Ti since it is a sensitive analytical technique because of the low background and high ion transmission. The Finnigan ICPS used was used with a resolution of 1.2 × 105 cps/ppb, detection limit of 0.2 ng/L.


## 2.3. Diffuse Reflectance Spectroscopy (DRS), Electron Microscopy (TEM and HAADF), and XRD of Samples

Diffuse reflectance spectroscopy (DRS) was carried out using a Perkin Elmer Lambda 900 UV-VIS-NIR spectrometer provided for with a PELA-1000 accessory. The absorption of the samples was plotted in Kubelka-Munk (KM) arbitrary unit versus wavelength. Irradiation of the samples was carried out in a tubular cavity of a Suntest Heraeus solar simulator, Hanau, Germany, or in the cavity of a reactor provided with indoor actinic light (white light).Transmission electron microscopy (TEM) was carried out in a Philips CM-12 (field emission gun, 300 kV, 0.17 nm resolution) microscope at 120 kV and was used to measure grain size of the TiO2. The textiles were embedded in epoxy resin 45359 Fluka and the fabrics were cross-sectioned with an ultramicrotome (Ultracut E) and at a knife angle of 35°. Crystal structures were characterized by X-ray diffraction (XRD) and recorded on an X’PertMPD PRO from PANalytical equipped with a secondary graphite (002) monochromator.


## 2.4. Contact Angle (CA) and ATR-IR Measurements

The hydrophilicity of the TiO2 films was determined by the water droplet contact angle (CA). The CA of TiO2 films on the substrate was determined by the sessile drop method on a DataPhysics OCA 35 unit. FTIR spectra were measured in a Portmann Instruments AG spectrophotometer equipped with a Specac attachment (the prim was a 45° one pass diamond crystal). Spectra were taken by 256 scans with a resolution of 2 cm−1 in the range 900–4000 cm−1. The position of the IR peaks was found by the second derivative of the spectra after Fourier deconvolution.


## 2.5.E. coli Loss of Viability Evaluation

The samples ofEscherichia coli (E. coli K12) were obtained from the Deutsche Sammlung von Mikroorganismen und Zellkulturen GmbH (DSMZ) ATCC23716, Braunschweig, Germany, to test the antibacterial activity of the TiO2-polyethylene and TiO2-polyester films according to previous work reported by our laboratory [9]. Serial solutions were prepared in tryptone solution and the samples plated on agar Plate-Count-Agar (PCA, Merck, Germany). The bacterial counting data reported were obtained by the replicate of 3 experimental runs.To verify that no regrowth ofE. coli occurs after the total inactivation observed in the first disinfection cycle, the samples were incubated for 24 hours at 37°C. After vortexing these samples in a 2 mL Eppendorf tube, the fabrics were placed on a PCA Petri dish, incubated overnight at 37°C to verify if still some bacteria remained adhered to the PE-TiO2 surface. No bacterial colonies were observed. This indicates that the bacteria inoculated on the PE-TiO2 surface remain in the Eppendorf tube. Then the bacterial 100 microliters suspensions were deposited on 3 Petri dishes to obtain replicates of the bacterial counting. No bacterial regrowth was observed.Statistical analysis of the results was performed for the decrease of the bacterial CFU values reporting the standard deviation values for the runs showing the fastest bacterial inactivation. The average values were compared by one-way analysis of variance and with the value of statistical significance.


## 3. Results and Discussion

### 3.1. TiO2-PE Bactericide Thin Films Obtained by Sputtering IncreasingE. coli LPS Cell Wall Fluidity and Leading to CellLysis

#### 3.1.1. Support Choice for TiO2 Deposition

This first study addresses the sputtering of TiO2 transparent, uniform, nonscattering films on polyethylene (PE). Sol-gel commercial methods are used to prepare TiO2 thin films on heat resistant substrates. But on nonthermal resistant substrates the thickness of the TiO2 films is not reproducible and they are not mechanically stable [6–10, 15].Polyethylene (PE) is a low cost and is widely available material. It is chemically inert, mechanically stable and flexible, and UV-resistant and does not oxidize in air under sunlight. In addition, the hydrophobic nature of PE allows the deposition of predominantly hydrophobic pathogens. Bacterial hydrophobic outer cell walls will adhere preferentially on hydrophobic surfaces promoting bacterial inactivation. PE-TiO2 films intend to overcome the use of TiO2 powders or suspensions for bacterial disinfection. Suspensions of TiO2 need a long-settlement time after each disinfection cycle being applied with significant loss of catalyst mass [6, 7]. The PE-TiO2 transparent films are designed to increase the quantum yield of the TiO2 radical species in addition to the direct bactericide action of sunlight [11, 14]. TiO2 sputtering does not lead to the deposition of enough TiO2 on the PE due to the low binding capacity of the PE surface. RF-plasma pretreatment induces oxygen negatively charged functional groups, for example, carboxylic, percarboxylic, epoxide, and peroxide groups by the atomic O, excited O, and anionic and cationic O generated in the RF-plasma chamber [12–14]. The PE functionalized negative sites bind the slightly positive sputtered Ti4+(TiO2) through electrostatic attraction involving chelation/complexation [34, 35]. The TiO2 was sputtered immediately after the RF-plasma pretreatment due to the short lifetimes of the surface polar hydrophilic surface sites.


#### 3.1.2. PE Pretreatment, TiO2 Surface Sputtered PE, Sample Absorption, and TiO2 Crystalline Phases

The amount of TiO2 on the pretreated PE fabrics was determined by X-ray fluorescence XRF using the nonpretreated fabric as the blank. For the sample pretreated in air for 15 min by RF plasma and sputtered for 8 min, a TiO2 thickness of ~58 nm was attained on PE equivalent to 290 layers. Taking one layer with 1015 atoms/cm2 and the thickness of one layer as 0.2 nm, the rate of TiO2 deposition was of 6×1014 atoms/cm2s. Self-cleaning TiO2 films up to 10 microns thick have been reported [1–5], but in the case of antibacterial coatings TiO2 thicknesses of 1 nm–20 nm have been reported to be effective [3, 6, 7]. TiO2 films DC sputtered for 8 min consist of nanoparticles 10–30 nm in size [36] and the films were reproducible.The RF-plasma induced functional groups only on the PE topmost layers since no color changes occurred destroying the PE structure indicative of PE-degradation [37].The DRS spectra of the PE-TiO2 films are shown in Figure 1 for samples pretreated by RF and UVC light. Sputtering for 1 to 3 min leads to transparent TiO2 films with no significant absorbance and very low antibacterial activity. A decrease of ~5% or more in optical transmittance has been reported for RF-plasma pretreated PE [38]. The decrease in transmittance for the sputtered films in Figure 1 was due to the inherent high refractive index of TiO2.Figure 1
DRS in Kubelka-Munk units versus wavelength of TiO2 sputtered (8 min) on polyethylene: (1) pretreated with UVC 1 torr, (2) pretreated with RF air plasma, (3) pretreated with RF plasma, and (4) TiO2 sputtered on PE for 1 min.The TiO2 crystal phases on PE show by XRD a high anatase (A) peak at 2θ = 21.5° [34] for a PE-TiO2 with and without RF-plasma pretreatment. But XRD peaks of rutile (R) at temperatures ≤130°C found in the DC-magnetron chamber were also observed. The generation of rutile at low temperatures is due to the structure forming function of the PE film on the TiO2 as reported for polyamide and other sputtered TiO2 textiles [12].


#### 3.1.3. Antibacterial Kinetics Evaluation and Sample Recycling

Figure2 showsE. coli inactivation on PE-TiO2 films under simulated solar light with an integrated light dose of 52 mW/cm2. The fastest bacterial inactivation was found for pretreated PE samples TiO2 sputtered for 8 min in Figure 2(a). Bacterial inactivation on PE-TiO2 samples is presented in Figure 2 for RF-pretreated PE for different times. No significant bacterial inactivation was observed for bacteria on uncoated PE (Figure 2(a), trace (4)). Only trace (1) was subjected to statistical analyses since it describes the results for the most favorable kinetics and presents the highest amount of TiO2 sites in exposed positions to interact with bacteria [39]. PE-TiO2 sputtered samples for 1 up to 5 min were not loaded with sufficient TiO2 to drive a fast bacterial inactivation. The Ti-loading on PE-TiO2 was determined by XRF for sputtering times of 1, 3, and 5 min and the values found were, respectively, 0.009, 0.019, and 0.031 TiO2 wt%/wt PE.E. coli inactivation on TiO2 sputtered on PE for 8 min irradiated with simulated solar light (52 mW/cm2).
(a)
TiO2 sputtered for different times without RF-plasma pretreatment for (1) 8 min, (2) 10 min, (3) 5 min, and (4) polyethylene alone
(b)
TiO2 sputtered for 8 min with surface RF-plasma pretreatment at 1 torr for (1) 15 min, (2) 20 min, (3) 30 min, and (4) 5 min
(c)
TiO2 sputtered 8 min RF air plasma pretreatment for (1) 15 min, (2) 20 min, (3) 30 min, and (4) 5 min
(d)
TiO2 sputtered 8 min with UVC pretreatment in air for (1) 20 min, (2) 15 min, (3) 10 min, and (4) 5 minSamples sputtered for times >8 min in Figure2(b) led to layer thickness >45 nm. This thickness leads to charge bulk inward diffusion decreasing the charge transfer between the PE-TiO2 and bacteria [40]. TiO2 sputtering for 8 min led to a TiO2 loading with the most suitable thickness for the charge diffusion able to reach bacteria. Figure 2(c), trace (1) shows the fastest bacterial inactivation for PE-TiO2 films. No significant bacterial inactivation was observed for bacteria on PE in the dark.To verify that no regrowth ofE. coli occurs after the first bacterial inactivation cycle, the PE-TiO2 film was incubated on an agar Petri dish for 24 hours at 37°C. No bacterial regrowth was observed meaning that there was no bacteria adhered to the surface after the inactivation cycle.The bacterial inactivation by PE-TiO2 samples sputtered for 8 min and pretreated with RF-plasma in air for 15 min was investigated up to the 6th cycle. The recycling of the samples showed stable inactivation kinetics up to the 5th-cycle; then the recycling kinetics became slower by ~20%. After each cycle, the samples were washed with distilled water and dried. Then, the samples were kept in an oven at 60°C to avoid bacterial contamination. After washing PE-TiO2 the samples were left standing for 24 h before to regain the initial sample hydrophobicity. This aspect will be discussed below in Section 3.1.4 when discussing the hydrophilic-hydrophobic transformation on PE-TiO2 in the dark and shown in Figures 3(a) and 3(b).(a) Photoinduced superhydrophilicity followed by water droplet contact angle during light irradiation at times: (A)t=0 min, (B) 15 min, (C) 30 min, (D) 45 min, and (E) 60 min. (b) Restoration of the hydrophilicity in the dark after times (A) 6 h, (B) 12 h, (C) 18 h, and (D) 24 h.
(a)
(b)


#### 3.1.4. Contact Angle (CA) and Hydrophobic Reversible Photoswitching

Figure3(a) presents the hydrophobic to hydrophilic transformation occurring on the PE-TiO2 sample induced by simulated solar light. A decrease of the CA from 121° to less than 5° within 60 min is shown in Figure 3(a) (traces (A)–(E)) concomitant with the time of bacterial inactivation. The recovery from the PE-TiO2 superhydrophilic surface to a hydrophobic initial surface proceeded within 24 hours in the dark as shown in Figure 3(b).The transformation of the initial hydrophobic TiO2 under light irradiation involves the dissociative chemisorption of water on the PE-TiO2 generating Ti-OH groups [41, 42]. Under light irradiation, the PE-TiO2 generates electrons (e−) and holes (h+) producing OH* and O2- radicals. The photogenerated h+ are the precursors of OH*. The structural changes in the TiO2 surface due to hydrophilicity are associated with the generation of these radicals. This process does not require high quantum efficiency in comparison to theE. coliphotocatalytic oxidation. A second mechanism has been suggested for the hydrophobic to hydrophilic transformation and would be due to TiO2 generated charges leading to oxygen vacancies reducing Ti4+ to Ti3+ [43].Figure3(b) shows the hydrophilic to hydrophobic reversible transformation in the dark reinstating the initial TiO2 hydrophobicity within 24 hours. The hydrophilic samples were kept in the dark and the contact angles (CA) were measured at preselected times to follow the back reaction to the initial hydrophobic state. This second process involves the destruction of airborne bacteria or hydrocarbons adsorbed on the PE-TiO2 surface along TiO2 surface dehydration and the back conversion of Ti3+/Ti4+ [42].Figure4(a) illustrates the rate of photoinduced hydrophilicity and Figure 4(b) the restoration rate of the hydrophobicity in the dark as a function of “cos θ”. According to Young’s theory the “cos θ” of a liquid droplet on a solid surface is a function of the interfacial energy between the solid and the liquid. The rate of the hydrophobic to hydrophilic conversion and for the reverse reaction in Figures 4(a) and 4(b) was 0.277 min−1 and was 8.71 × 10−3 min−1, respectively. These rates were calculated by integrating “cos θ” in Young’s equation (1).(a) Kinetics of the hydrophobic-hydrophilic transformation under solar simulated light and (b) kinetics of the dark reverse reaction towards the initial state for PE-TiO2 (8 min) RF air plasma pretreated for 15 min.
(a)
(b)The contact angle (CA) conventionally measures the angle where the liquid meets the solid quantifying the wettability of a solid surface via the Young equation. The Young equation (1) involves solid-vapor, liquid-vapor, and solid-liquid interfacial energies. The solid-vapor interfacial energy is denoted by γSG, the solid-liquid interfacial energy by γSL, and the liquid-vapor interfacial energy (i.e., the surface tension) by γLG; then the equilibrium contact angle θC is determined from these quantities by Young’s equation:
(1)0=γSG-γSL-γLGcos⁡θC.Upon illumination the surface TiO2 energy increases since the TiO2 surface is transformed into a metastable state as shown in (2) decreasing the initial contact angle of 121° (Figure 3(a)) to a value of <5° after 60 min irradiation (Figure 3(b)). Equation (2) shows the TiOH metastable hydrophilic intermediate induced under light:
(2)
The hydrophobic properties of the PE-TiO2 surface are important in antibacterial films.E. coli andStaphylococcus aureus present a preferential adhesion to hydrophilic surfaces [44]. Bacteria with hydrophobic surface properties likeS. epidermidis adhere preferentially to hydrophobic surfaces [45]. Hydrophobic bacteria adhere to a variety of surfaces forming biofilms to a greater extent than hydrophilic bacteria [46]. Recently, R. Amal recently has reported the reversible photoswitching behavior under light by TiO2/Ag nanoparticles [47, 48]. This study shows that UV-A irradiation of brownish Ag/TiO2 changed the surface Ag2O to violet black, the characteristic color of Ag-plasmon. Nano-Ag particles are responsive to visible light due to the enhanced surface plasmon resonance (SPR) absorption band at ~550 nm. As a result of visible light excitation a reverse electron flow from Ag0 to the TiO2cb occurs along the oxidation of metallic Ag0 back to Ag2O. A reversible antimicrobial photoswitching of nano-Ag/TiO2 particles was reported in this study when irradiating the Ag-nanoparticles in two different wavelength regions [48].


#### 3.1.5. FTIR Analysis and Bacterial Inactivation on PE-TiO2

FTIR spectroscopy is used in the present study to monitor the changes in the structure/dynamics in theE. coli lipopolysaccharide (LPS) bilayer induced by PE-TiO2 under solar simulated light. LPS amphiphiles constitute the outer cell wall ofE. coli and consist of LPS units. The LPS are made up of fluid chains [49]. (CH2)- and (CH3)-groups make up 70% of the lipopolysaccharide (LPS), phosphatidyl-ethanolcholine (PE), and peptidoglycan (PGN), the main groups making theE. coli cell envelope [49, 50].The characteristic bands of the methylene (–CH2) stretching vibrations in the 2800–2900 cm−1 spectral region are shown in Figure 5. Figure 5(a) shows the shift of the asymmetric methylene stretching vibrations at νa(CH2) 2922.2 cm−1 and of the symmetric stretching vibrations of νs(CH2) at 2849.2 cm−1 for RF-plasma pretreated samples for 15 min and sputtered for 8 min and then irradiated up to 60 min. The shifts in the peaks for RF-plasma pretreated PE-TiO2 samples in Figures 5(a) and 5(b) are seen to be more important compared to the nonpretreated samples shown in Figures 5(c) and 5(d). This is due to the lower amount of TiO2 on the nonpretreated PE leading to longer bacteria inactivation times. The shifts presented in Figure 5 reflect the structural/conformation changes in LPS during lipid peroxidation involving the production of peroxides, alcohols, and carboxyl type functionalities associated to the bacteriallysis and bacterial dead.Shift of the stretching vibrations as a function of time detected by ATR-FTIR for the asymmetricνa(CH2) vibrational bands and the symmetric νs(CH2) vibrational bands forE. coli up to 60 min under solar simulated irradiation. (a) and (b) show the shifts of νa(CH2) vibrational bands on PE-TiO2 samples pretreated with RF air plasma for 15 min and then sputtered for 8 min. (c) and (d) show the IR shifts of νs(CH2) vibrational bands on nonpretreated PE-sputtered for 8 min.
(a)
(b)
(c)
(d)The decrease in the amplitude observed for the stretching vibrations in the ATR-IR-spectra in Figures5(a)–5(d) was due to isolated double bonds in the LPS. The discontinuous shifts towards the blue in Figures 5(a) and 5(b) suggest an increased mobility of the LPS units in the LPS chain-packing [49]. The increased disorder modifies the frequencies of the –CH2 symmetric and antisymmetric bands, shifting the peak positions during the irradiation time [51]. Figure 2(c), trace (1) shows thatE. coli inactivation is complete within 60 min on PE-TiO2 and this time coincides with the time in which the LPS stretching vibrations attain the highest fluidity. This time coincides with the time to attain the intermolecular distances leading to –CH2 scission (60 min) [52–54].


#### 3.1.6. TiO2 Films Sputtered by HIPIMS Leading to AcceleratedE. coli

Figure6 shows the bacterial inactivation kinetics by the HIPIMS TiO2 sputtered samples [28]. As shown in Figure 6, no bacterial inactivation takes place in the dark, but the bacterial inactivation becomes faster for HIPIMS sputtering times between 1 min (trace (5)) and 4 min (trace (2)). Longer deposition times between 10 and 30 min did not accelerate the loss of viability kinetics due to the fact that an increased TiO2 thickness >12 nm sputtered within 4 min leads to (a) bulk inward diffusion of the charge carriers generated on TiO2 under light leading to highly oxidative radicals [6–10] and (b) longer sputtering times facilitate the TiO2 interparticle growth decreasing the TiO2 contact surface with bacteria.Figure 6
E. coli survival on TiO2 HIPIMS-sputtered (5 A) on polyester for different times in the dark and under solar simulated irradiation (50 mW/cm2).The bacterial inactivation time shown in Figure6 for polyester surface sputtered by HIPIMS is faster compared to DC and DCP TiO2-polyester sputtered surfaces [36].


#### 3.1.7. DCP and HIPIMS Sputtering of Samples, Electronic Density, and Voltage Considerations

Figure7, left hand side presents a scheme for the DC sputtering and in the middle section Figure 7 shows the sputtering of DCP proceeding with a higher ionization of Ti at higher e-densities (~1016-17 e−/m3) [55]. The HIPIMS with 5A and consequently a much higher energy than the HIPIMS pulses increases the ionization percentage Ti0→Ti3+/Ti4+ with a concomitant increase in the e-densities (~1018-19 e−/m3).Scheme for the magnetron chamber induced M+ ionization by (a) DC, (b) DCP, and (c) HIPIMS sputtering of metal-ions (M+) on 3D substrates showing the higher density ionization induced by HIPIMS.
(a)
(b)
(c)This increased arrival energy of the Ti-ions on the substrate allows the alignment of the Ti-ions on the polyester irregular (rugous) surface enabling a uniform coverage of the 3D polyester, oximeters, and pressure blood measuring devices as usually used in medical facilities. These artifacts are sources of infections, since they are not TiO2 coated. The HIPIMS sputtering shown on the right hand side in Figure 7 allows the uniform sputtering of objects with complex 3D geometry due to their increased e-density interacting more favorably with the negatively biased substrate compared to the less dense production of ionized species shown in Figures 7(a) and 7(b) [29, 55, 56].


### 3.2. Uniform TiO2-Doped In2O3 Films Increasing the Bacterial Inactivation Kinetics with Respect to TiO2-Films under Low Intensity Solar Simulated Light

#### 3.2.1. TiO2 Sputtered on Pretreated PE

This study shows that the surface modification of TiO2 by doping with In2O3 is an effective route to increase the TiO2 absorption into the visible region. A photoinduced interfacial charge transfer (IFCT) between TiO2 and In2O3 takes place and couples the charge generation/separation between these two oxides. In2O3 has an absorption band in the visible between 400 nm and 500 nm [57].The TiO2 and TiO2-In2O3 thin films were deposited onto polyester in the magnetron chamber by sputtering Ti by DC in a reactive O2 atmosphere followed by DCP sputtering of In, in the presence of mixture of Ar and O2 gases. The total working pressure P=(PAr+PO2) was fixed at 0.5 Pa and the ratio PO2/Ptotal = 4.5%. The sputtering current on the Ti target was 280 mA providing a power of 120 W (U=-450V) and a current density of 12.7 mA/cm2. Pulsed magnetron sputtering (DCP) was used to sputter the In2O3 and was operated at 50 kHz with 15% reversed voltage. The sputtering power was fixed at 50 W providing a negative voltage of −500 V and a power of 140 W.


#### 3.2.2. Evaluation of the Bacterial Inactivation ofE. coli in the Dark and under Light

The counting of the bacterial inactivation ofE. coli was performed as described above in Section 2.4 [28, 36]. An actinic irradiation lamp Osram Lumilux T8-L 18 W (4.0 mW/cm2) was used in Figure 8 as a source of white light. This light is used for the indoors lightning in health facilities. The solar simulator (Heraeus, Hanau, Germany) emitting between 200 and 800 nm from a 100 W Xe-light resembling the solar spectrum and set at 50 mW/cm2. The value of 50 mW/cm2 is the average light dose reaching central European countries. Figure 8 shows the inactivation ofE. coli by TiO2, TiO2-In2O3, and In2O3 samples.E. coli inactivation under solar simulated light for (1) TiO2/In2O3 (sputtered for 10 min/10 s), (2) TiO2 (sputtered for 10 min), (3) In2O3 (sputtered for 10 s) samples, respectively, and (4) a bare polyester sample, at light intensities: (a) 30 mW/cm2 and (b) 50 mW/cm2.
(a)
(b)A synergic interaction of TiO2 is required to lead to fast bacterial inactivation in Figure 8(a), trace (1). Figure 8(b), trace (4) shows that no bacterial inactivation was possible under light on bare polyester. Figure 8(a) reports the effect of the light intensity on the amount of charges in the coupled semiconductors at 30 mW/cm2 and 50 mW/cm2. A higher light intensity increases the amount of semiconductor charges interacting with bacteria leading to a faster bacterial inactivation. The accelerated bacterial inactivation by the TiO2-In2O3 photocatalysts compared to bare TiO2 samples is favoured by the electrostatic attraction existing between the positive charged Ti and the negativeE. coli cell wall at pH 6-7. TheE. coli is negatively charged between pH 3–9 due to the excess of carboxylic groups compared to the amide I and amide II cell wall positively charged groups [3, 58]. The TiO2 bacterial inactivation under light has been widely reported and will not be discussed in this study [6–10].Figure9 shows repetitive disinfection cycles by a TiO2-In2O3 sputtered for 10 min from a TiO2 target and 10 s from an In target in a reactive O2 atmosphere, up to the 5th cycle. The 8th cycle shows a loss of bacterial inactivation kinetics when actinic light was used in Figure 9(a) and when a solar simulator with a dose of 50 mW/cm2 was applied. The slower kinetics shown in Figure 9(b) in the last cycle was due possibly to the leaching of In and Ti-nanoparticles detected by ICP-Ms (data not shown).E. coli inactivation recycling experiments on TiO2/In2O3 sputtered for 10 min/10 s on polyester under irradiation by: (a) Osram Lumilux T8-L 18 W (4.0 mW/cm2, 360 to 800 nm) and (b) Suntest solar simulator 50 mW/cm2.
(a)
(b)


#### 3.2.3. Diffuse Reflectance Spectroscopy (DRS) and X-Ray Diffraction (XRD) Investigation of TiO2 and TiO2-In2O3 Films

Figure10 shows the UV-Vis reflectance spectra of TiO2 sputtered as a function of time. The Kubelka-Munk (KM/S) relations convert reflectance measurements into absorption spectra units. K and S are the absorption and scattering coefficients, respectively, of TiO2 in Figure 10(a). The KM/S values for the samples were found proportional to the TiO2 sputtering time. The faster bacterial inactivation induced by TiO2-In2O3 and shown in Figure 8 suggests an electron transfer from In2O3 to TiO2.Diffuse reflectance spectra (DRS) of TiO2 and TiO2/In2O3 samples in Kubelka-Munk units: (a) TiO2 1 min, TiO2 5 min, and TiO2 10 min. (b) TiO2 10 min/In2O3 5 s, TiO2 10 min/In2O3 10 s, TiO2 10 min/In2O3 20 s, and TiO2 10 min/In2O340 s, In2O3 10 s.
(a)
(b)Figure10(b) shows a progressive increase in optical absorption (KM/S spectra) in the region 350 nm. Samples sputtered with In2O3 for 5–20 s show lower absorption intensities. Figure 10(b) shows a weak absorption band from 400 to 500 nm, attributed to the interfacial charge transfer (IFCT) from the TiO2 to In2O3. The weak absorption between 500 and 600 nm is due to the In2O3 interband indirect transitions at potential levels 2.09 eV [25]. These electronic transitions occur from the In2O3 valence band to two levels near the conduction band ≥2 eV [59]. The TiO2-In2O3 transition seems to originate from the In2O3 (In5s5p orbital) to the conduction band of TiO2. The light green color In2O3 samples with band-gap of 2.5–2.8 eV (absorption edge ~470–500 nm) became darker at longer sputtering times [60, 61].Figure11 shows the TiO2 XRD of TiO2 and In2O3/TiO2 films, respectively. Figure 11 presents the XRD diffraction for the TiO2 DC sputtered on polyester for 10 min. The intense anatase peak at 24.6° is due to the presence of anatase. No specific signal due to In2O3 was detected due to its very low loading (<0.2%). Only a slight decrease in intensity of the 24.6° (101) anatase peak was observed in the In2O3/TiO2 samples. No modification in the TiO2 diffraction peaks due to In2O3 was observed, suggesting that no lattice modification due to In-doping takes place in the TiO2 network.Figure 11
XRD diffraction data for(1) TiO2 sputtered for 10 min on polyester and (2) TiO2 10 min/In2O3 10 s sputtered on polyester: (a) diffraction patterns of anatase (b), rutile (c), and (d) cubic In2O3.


#### 3.2.4. Interfacial Charge Transfer Mechanism (IFCT) in TiO2-In2O3 Composite Films

Coupling TiO2-In2O3 induced a significant increase in the photocatalytic activity compared to TiO2 alone and In2O3 as shown in Figure 8. This significant increase can be rationalized by the relative positions of the conduction band (cb) and valence band (vb) in In2O3 and TiO2. The cb of In2O3 at −0.62 versus NHE [60, 61] transfers the cb electrons to TiO2 (cb at 0.2 eV versus NHE for anatase). The UV component of sunlight generates TiO2 holes able to transfer to In2O3 vb as shown in Figure 12(a). The subsequent spatial separation of photogenerated charge carries and the e− and h+ injection limit the e−/h+ recombination on TiO2.(a) Scheme of the charge injection during the interfacial charge transfer (IFCT) between In2O3 and TiO2 under simulated sunlight. (b) Radical(s) reaction generated from O2 reduction on TiO2 (R: bacteria degradation or species produced during the bacterial degradation).
(a)
(b)The highly dispersed In2O3 on the TiO2 layers builds a Schottky barrier at the TiO2/In2O3 interface. This precludes partly the recombination of electrons and holes in TiO2. The scheme in Figure 12(a) suggests an IFCT to take place in the TiO2-In2O3 assuming that the generated charges have a sufficient lifetime to diffuse to the photocatalyst surface inactivating bacteria. The TiO2 is the main photocatalyst and the In2O3 acts as a visible light sensitizer. In Figure 12(a) a detrimental effect may be due to the cross interparticle recombination of the e-cb of TiO2 with the h+vb of In2O3 [62].Figure12(b) shows schematically the e-cb in the TiO2 and In2O3 particles reacting with the adsorbed O2 on the TiO2 surface to yield O2-∙ radical anion and subsequently other highly oxidative protonated radicals active in the bacterial inactivation.


### 3.3. New Evidence for the Inactivation of TiO2 Films with Bacteria in the Dark

This study addresses the design, preparation, and bacterial counting of the bacterial inactivation kinetics and characterization of TiO2-polyester surfaces inducing cell wall damage with concomitant loss of bacterial viability in the dark. In 1985, Matsunaga et al., [63] reported that TiO2 suspensions inactivate bacteria. After Matsunaga many studies have reported on the TiO2 photocatalytic bacterial cell wall damage [64–66]. The bacterial inactivation by agents permeating into the cell structure has also been widely reported [5, 6, 67]. Few articles have reported cell wall damages by the photocatalysis by electron microscopy (EM) [5].P. aeruginosa outer cell wall damages due to TiO2 photocatalysis have been reported recently by P. Amezaga-Madrid et al. [68–74]. The TiO2 interaction with the bacteria was reported to cause damages/disorganization in the cell wall morphology modifying its permeability and the capacity to regulate the outer layers osmotic pressures. The importance of the present study on antimicrobial surfaces relates to the fact that bacteria survive for long times in hospital facilities increasingly leading to hospital acquired infections (HAI). Precluding the infectious biofilm formation by the TiO2-polyester surfaces in the dark is an effective way to reduce/suppress infections as will be reported in this study.


#### 3.3.1. Preparation of TiO2-Polyester by the Hydrothermal Route andE. coli Loss of Viability in the Dark and under White Light

The TiO2 on the polyester deposition by the hydrothermal route (HT) was carried out as follows: titanium tetraisopropoxide (TTIP) Sigma Aldrich p.a. was dissolved in isopropanol in a 1 : 3 volume ratio (1 : 3 molar ratio). This solution was poured into a beaker with 50 mL of 0.1 M HNO3. The polyester samples 6 × 4 cm were immersed into the acid TiO2 precursor suspension and heated under stirring in a reflux condenser for 2 hours at 80°C. The polyester fabric was removed from the suspension, rinsed with demineralized water, and treated in ultrasound bath for 2 min to remove unbound TiO2 particles. The last operation was repeated three times and the TiO2-polyester fabric were subsequently dried for 2 hours at 70°C in air [75]. The inactivation ofEscherichia coli (E. coli K12) on TiO2 polyester samples was evaluated according to Section 2.4.In Figure12 no significant bacterial loss of viability was observed for bacteria on uncoated samples (Figure 13, trace (1)). A loading of 0.05% TiO2 on the TiO2-polyester in Figure 13, trace (2) did not contain enough TiO2 to induce bacteria loss of viability. TiO2 loadings between 0.1% and 5% led to similar bacterial loss of viability within 120 min. This indicates that the number of cells capable of forming colonies in contact with the cell wall surface attained a stable value for TiO2-polyester surfaces loaded between 0.1% and 5.0%.Figure 13
Loss of bacterial viability in the dark mediated by TiO2-polyester (HT) prepared samples with different TiO2 loadings: (1) polyester alone, (2) 0.05%, (3) 0.1%, (4) 0.5%, (5)1% and (6) 5%.Figure14 shows the loss of bacterial viability under light irradiation within 60 min for TiO2-polyester at loadings above TiO2 0.1%. The insert in Figure 14 shows the spectral emission of the actinic Osram Lumilux 18 W/827 light used with a dose of 4.0 mW/cm2. The mechanism leading to bacterial inactivation under light has been reported by Foster et al., [4] and Tung and Daoud, [10]. More recently, our EPFL laboratory has reported in a detailed way the partial damage/degradation of theE. coli outer cell functional groups during TiO2 photocatalysis by ATR-IR spectroscopy [50, 66].Figure 14
Loss of bacterial viability ofE. coli under Osram Lumilux 18 W/827 irradiation mediated by TiO2-polyester HT prepared samples with a TiO2 loading: (1) polyester alone, (2) 0.05% (3) 0.1% (4) 0.5%, (5)1% and (6) 5%.By X-ray diffraction spectroscopy (XRD) the TiO2 crystalline phases on the 5% TiO2-polyester prepared by the HT-method show a significant anatase (A) peak at 2θ = 21.5° and a small rutile peak at 2θ = 37.3°. These XRD results showing the formation of anatase and rutile peaks are due to the structure forming function of the polyester at low temperatures when colloidal TiO2 suspensions were added. When heating TiO2 suspensions by themselves anatase was formed ~300°C and rutile at around 600°C in the absence of a structure forming surface like polyester [9, 12, 13]. These last temperatures are significantly higher compared to temperatures ~80°C required to prepare the TiO2 with anatase and rutile phases as detected by XRD.


#### 3.3.2. Transmission Electron Microscopy of theE. coli Cell Wall Interaction with TiO2-Polyester. Sample Preparation and Process Kinetics

The samples of the TiO2 polyester for the electron microscopy of theE. coli interaction with TiO2-polyester fabrics were prepared in the following way: suspensions orE. coli were fixed in paraformaldehyde 2% + glut 0.2% in phosphate buffer for 30 min and centrifuged and pellet resuspended in low melting point agarose. This was then cut into small cubes, dehydrated, and stained for 20 min in 2% uranyl acetate then dehydrated in a graded alcohol series. The samples were then embedded in LR white resin in Beam capsules and polymerized overnight at 55°C. The resin blocks containing theE. coli on TiO2-polyester were thin sectioned to a 70 nm thickness with an ultramicrotome (Leica UC7). The TiO2-polyester fibers were embedded in epoxy and thin sectioned at a thickness of 80 to 100 nm.The transmission electron microscopy (TEM) of the TiO2-polyester (HT) samples interacting withE. coli is shown in Figure 15. The TEM in the upper left corner in Figure 15 shows the interaction of TiO2-polyester (HT) sample with theE. coli K12 at time zero. TheE. coli intact cell wall is seen as well as the aggregates and coaggregates of TiO2 positioned at a distance from the cell wall in agreement with the DLVO theory of colloidal stability. TiO2 nanoparticle aggregation sets in at a pH close to the isoelectric point (IEP) of 6-7 due to the attractive Van der Waals forces leading to TiO2 aggregation within 30 min as shown in the TEM in the upper right corner [76]. The TiO2 single particles present sizes between 40 and 60 nm and the hydrodynamic diameter of the aggregates was found to be 170–240 nm equivalent to 3-4 primary TiO2 particles. After 30 min, the TiO2 aggregates accumulate on the cell wall surface due to their almost neutral charge at physiological pH and this is shown in the right upper hand side Figure 15. Damage in the cell wall is localized in the contact area between the TiO2 and bacteria due to (a) the weak attraction between the TiO2 (IEP ~6-7) and the negatively charged cell wall. Damage in the cell wall was observed at a pH close to the TiO2 IEP (charge zero). The TiO2 particles aggregate between themselves since they have an almost neutral charge. Concomitantly the Van der Waals attractive forces drive the interaction between the TiO2-aggregates and the bacterial cell wall and (b) damage to the cell wall is also possible due to the abrasion by the TiO2 rutile component of theE. coli envelope [77]. The effect of the cell wall in the dark after 30 minutes seems to be critical step in the loss of bacterial viability.Figure 15
TEM biomicroscopy of TiO2-polyester 5% (HT) interacting with theE. coli cell wall in the dark: (i) upper left hand side: time zero, (ii) upper right hand side: time 30 min, and (iii) central lower position: time 120 min. For more details see text.The lower central TEM in Figure15 shows the damage to theE. coli outer wall cell within 120 min. After 120 min the wall outer layers present discontinuities in some regions and vanished in other regions. Cell wall damages leading to cell inactivation involve changes in cell morphology, cell-wall microstructure, and local pH [78]. The extensive damage to the outer cell layers after 120 min coincides with the time required for the total loss of cell viability in the dark shown in Figure 13. The bacterial cell cannot function anymore as a membrane regulating the in and out osmotic pressure and material flow. Sunada et al. reportedE. coli inactivation by TiO2 films damaging the cell wall membrane due to the leakage of internal cell components [79].


## 3.1. TiO2-PE Bactericide Thin Films Obtained by Sputtering IncreasingE. coli LPS Cell Wall Fluidity and Leading to CellLysis

### 3.1.1. Support Choice for TiO2 Deposition

This first study addresses the sputtering of TiO2 transparent, uniform, nonscattering films on polyethylene (PE). Sol-gel commercial methods are used to prepare TiO2 thin films on heat resistant substrates. But on nonthermal resistant substrates the thickness of the TiO2 films is not reproducible and they are not mechanically stable [6–10, 15].Polyethylene (PE) is a low cost and is widely available material. It is chemically inert, mechanically stable and flexible, and UV-resistant and does not oxidize in air under sunlight. In addition, the hydrophobic nature of PE allows the deposition of predominantly hydrophobic pathogens. Bacterial hydrophobic outer cell walls will adhere preferentially on hydrophobic surfaces promoting bacterial inactivation. PE-TiO2 films intend to overcome the use of TiO2 powders or suspensions for bacterial disinfection. Suspensions of TiO2 need a long-settlement time after each disinfection cycle being applied with significant loss of catalyst mass [6, 7]. The PE-TiO2 transparent films are designed to increase the quantum yield of the TiO2 radical species in addition to the direct bactericide action of sunlight [11, 14]. TiO2 sputtering does not lead to the deposition of enough TiO2 on the PE due to the low binding capacity of the PE surface. RF-plasma pretreatment induces oxygen negatively charged functional groups, for example, carboxylic, percarboxylic, epoxide, and peroxide groups by the atomic O, excited O, and anionic and cationic O generated in the RF-plasma chamber [12–14]. The PE functionalized negative sites bind the slightly positive sputtered Ti4+(TiO2) through electrostatic attraction involving chelation/complexation [34, 35]. The TiO2 was sputtered immediately after the RF-plasma pretreatment due to the short lifetimes of the surface polar hydrophilic surface sites.


### 3.1.2. PE Pretreatment, TiO2 Surface Sputtered PE, Sample Absorption, and TiO2 Crystalline Phases

The amount of TiO2 on the pretreated PE fabrics was determined by X-ray fluorescence XRF using the nonpretreated fabric as the blank. For the sample pretreated in air for 15 min by RF plasma and sputtered for 8 min, a TiO2 thickness of ~58 nm was attained on PE equivalent to 290 layers. Taking one layer with 1015 atoms/cm2 and the thickness of one layer as 0.2 nm, the rate of TiO2 deposition was of 6×1014 atoms/cm2s. Self-cleaning TiO2 films up to 10 microns thick have been reported [1–5], but in the case of antibacterial coatings TiO2 thicknesses of 1 nm–20 nm have been reported to be effective [3, 6, 7]. TiO2 films DC sputtered for 8 min consist of nanoparticles 10–30 nm in size [36] and the films were reproducible.The RF-plasma induced functional groups only on the PE topmost layers since no color changes occurred destroying the PE structure indicative of PE-degradation [37].The DRS spectra of the PE-TiO2 films are shown in Figure 1 for samples pretreated by RF and UVC light. Sputtering for 1 to 3 min leads to transparent TiO2 films with no significant absorbance and very low antibacterial activity. A decrease of ~5% or more in optical transmittance has been reported for RF-plasma pretreated PE [38]. The decrease in transmittance for the sputtered films in Figure 1 was due to the inherent high refractive index of TiO2.Figure 1
DRS in Kubelka-Munk units versus wavelength of TiO2 sputtered (8 min) on polyethylene: (1) pretreated with UVC 1 torr, (2) pretreated with RF air plasma, (3) pretreated with RF plasma, and (4) TiO2 sputtered on PE for 1 min.The TiO2 crystal phases on PE show by XRD a high anatase (A) peak at 2θ = 21.5° [34] for a PE-TiO2 with and without RF-plasma pretreatment. But XRD peaks of rutile (R) at temperatures ≤130°C found in the DC-magnetron chamber were also observed. The generation of rutile at low temperatures is due to the structure forming function of the PE film on the TiO2 as reported for polyamide and other sputtered TiO2 textiles [12].


### 3.1.3. Antibacterial Kinetics Evaluation and Sample Recycling

Figure2 showsE. coli inactivation on PE-TiO2 films under simulated solar light with an integrated light dose of 52 mW/cm2. The fastest bacterial inactivation was found for pretreated PE samples TiO2 sputtered for 8 min in Figure 2(a). Bacterial inactivation on PE-TiO2 samples is presented in Figure 2 for RF-pretreated PE for different times. No significant bacterial inactivation was observed for bacteria on uncoated PE (Figure 2(a), trace (4)). Only trace (1) was subjected to statistical analyses since it describes the results for the most favorable kinetics and presents the highest amount of TiO2 sites in exposed positions to interact with bacteria [39]. PE-TiO2 sputtered samples for 1 up to 5 min were not loaded with sufficient TiO2 to drive a fast bacterial inactivation. The Ti-loading on PE-TiO2 was determined by XRF for sputtering times of 1, 3, and 5 min and the values found were, respectively, 0.009, 0.019, and 0.031 TiO2 wt%/wt PE.E. coli inactivation on TiO2 sputtered on PE for 8 min irradiated with simulated solar light (52 mW/cm2).
(a)
TiO2 sputtered for different times without RF-plasma pretreatment for (1) 8 min, (2) 10 min, (3) 5 min, and (4) polyethylene alone
(b)
TiO2 sputtered for 8 min with surface RF-plasma pretreatment at 1 torr for (1) 15 min, (2) 20 min, (3) 30 min, and (4) 5 min
(c)
TiO2 sputtered 8 min RF air plasma pretreatment for (1) 15 min, (2) 20 min, (3) 30 min, and (4) 5 min
(d)
TiO2 sputtered 8 min with UVC pretreatment in air for (1) 20 min, (2) 15 min, (3) 10 min, and (4) 5 minSamples sputtered for times >8 min in Figure2(b) led to layer thickness >45 nm. This thickness leads to charge bulk inward diffusion decreasing the charge transfer between the PE-TiO2 and bacteria [40]. TiO2 sputtering for 8 min led to a TiO2 loading with the most suitable thickness for the charge diffusion able to reach bacteria. Figure 2(c), trace (1) shows the fastest bacterial inactivation for PE-TiO2 films. No significant bacterial inactivation was observed for bacteria on PE in the dark.To verify that no regrowth ofE. coli occurs after the first bacterial inactivation cycle, the PE-TiO2 film was incubated on an agar Petri dish for 24 hours at 37°C. No bacterial regrowth was observed meaning that there was no bacteria adhered to the surface after the inactivation cycle.The bacterial inactivation by PE-TiO2 samples sputtered for 8 min and pretreated with RF-plasma in air for 15 min was investigated up to the 6th cycle. The recycling of the samples showed stable inactivation kinetics up to the 5th-cycle; then the recycling kinetics became slower by ~20%. After each cycle, the samples were washed with distilled water and dried. Then, the samples were kept in an oven at 60°C to avoid bacterial contamination. After washing PE-TiO2 the samples were left standing for 24 h before to regain the initial sample hydrophobicity. This aspect will be discussed below in Section 3.1.4 when discussing the hydrophilic-hydrophobic transformation on PE-TiO2 in the dark and shown in Figures 3(a) and 3(b).(a) Photoinduced superhydrophilicity followed by water droplet contact angle during light irradiation at times: (A)t=0 min, (B) 15 min, (C) 30 min, (D) 45 min, and (E) 60 min. (b) Restoration of the hydrophilicity in the dark after times (A) 6 h, (B) 12 h, (C) 18 h, and (D) 24 h.
(a)
(b)


### 3.1.4. Contact Angle (CA) and Hydrophobic Reversible Photoswitching

Figure3(a) presents the hydrophobic to hydrophilic transformation occurring on the PE-TiO2 sample induced by simulated solar light. A decrease of the CA from 121° to less than 5° within 60 min is shown in Figure 3(a) (traces (A)–(E)) concomitant with the time of bacterial inactivation. The recovery from the PE-TiO2 superhydrophilic surface to a hydrophobic initial surface proceeded within 24 hours in the dark as shown in Figure 3(b).The transformation of the initial hydrophobic TiO2 under light irradiation involves the dissociative chemisorption of water on the PE-TiO2 generating Ti-OH groups [41, 42]. Under light irradiation, the PE-TiO2 generates electrons (e−) and holes (h+) producing OH* and O2- radicals. The photogenerated h+ are the precursors of OH*. The structural changes in the TiO2 surface due to hydrophilicity are associated with the generation of these radicals. This process does not require high quantum efficiency in comparison to theE. coliphotocatalytic oxidation. A second mechanism has been suggested for the hydrophobic to hydrophilic transformation and would be due to TiO2 generated charges leading to oxygen vacancies reducing Ti4+ to Ti3+ [43].Figure3(b) shows the hydrophilic to hydrophobic reversible transformation in the dark reinstating the initial TiO2 hydrophobicity within 24 hours. The hydrophilic samples were kept in the dark and the contact angles (CA) were measured at preselected times to follow the back reaction to the initial hydrophobic state. This second process involves the destruction of airborne bacteria or hydrocarbons adsorbed on the PE-TiO2 surface along TiO2 surface dehydration and the back conversion of Ti3+/Ti4+ [42].Figure4(a) illustrates the rate of photoinduced hydrophilicity and Figure 4(b) the restoration rate of the hydrophobicity in the dark as a function of “cos θ”. According to Young’s theory the “cos θ” of a liquid droplet on a solid surface is a function of the interfacial energy between the solid and the liquid. The rate of the hydrophobic to hydrophilic conversion and for the reverse reaction in Figures 4(a) and 4(b) was 0.277 min−1 and was 8.71 × 10−3 min−1, respectively. These rates were calculated by integrating “cos θ” in Young’s equation (1).(a) Kinetics of the hydrophobic-hydrophilic transformation under solar simulated light and (b) kinetics of the dark reverse reaction towards the initial state for PE-TiO2 (8 min) RF air plasma pretreated for 15 min.
(a)
(b)The contact angle (CA) conventionally measures the angle where the liquid meets the solid quantifying the wettability of a solid surface via the Young equation. The Young equation (1) involves solid-vapor, liquid-vapor, and solid-liquid interfacial energies. The solid-vapor interfacial energy is denoted by γSG, the solid-liquid interfacial energy by γSL, and the liquid-vapor interfacial energy (i.e., the surface tension) by γLG; then the equilibrium contact angle θC is determined from these quantities by Young’s equation:
(1)0=γSG-γSL-γLGcos⁡θC.Upon illumination the surface TiO2 energy increases since the TiO2 surface is transformed into a metastable state as shown in (2) decreasing the initial contact angle of 121° (Figure 3(a)) to a value of <5° after 60 min irradiation (Figure 3(b)). Equation (2) shows the TiOH metastable hydrophilic intermediate induced under light:
(2)
The hydrophobic properties of the PE-TiO2 surface are important in antibacterial films.E. coli andStaphylococcus aureus present a preferential adhesion to hydrophilic surfaces [44]. Bacteria with hydrophobic surface properties likeS. epidermidis adhere preferentially to hydrophobic surfaces [45]. Hydrophobic bacteria adhere to a variety of surfaces forming biofilms to a greater extent than hydrophilic bacteria [46]. Recently, R. Amal recently has reported the reversible photoswitching behavior under light by TiO2/Ag nanoparticles [47, 48]. This study shows that UV-A irradiation of brownish Ag/TiO2 changed the surface Ag2O to violet black, the characteristic color of Ag-plasmon. Nano-Ag particles are responsive to visible light due to the enhanced surface plasmon resonance (SPR) absorption band at ~550 nm. As a result of visible light excitation a reverse electron flow from Ag0 to the TiO2cb occurs along the oxidation of metallic Ag0 back to Ag2O. A reversible antimicrobial photoswitching of nano-Ag/TiO2 particles was reported in this study when irradiating the Ag-nanoparticles in two different wavelength regions [48].


### 3.1.5. FTIR Analysis and Bacterial Inactivation on PE-TiO2

FTIR spectroscopy is used in the present study to monitor the changes in the structure/dynamics in theE. coli lipopolysaccharide (LPS) bilayer induced by PE-TiO2 under solar simulated light. LPS amphiphiles constitute the outer cell wall ofE. coli and consist of LPS units. The LPS are made up of fluid chains [49]. (CH2)- and (CH3)-groups make up 70% of the lipopolysaccharide (LPS), phosphatidyl-ethanolcholine (PE), and peptidoglycan (PGN), the main groups making theE. coli cell envelope [49, 50].The characteristic bands of the methylene (–CH2) stretching vibrations in the 2800–2900 cm−1 spectral region are shown in Figure 5. Figure 5(a) shows the shift of the asymmetric methylene stretching vibrations at νa(CH2) 2922.2 cm−1 and of the symmetric stretching vibrations of νs(CH2) at 2849.2 cm−1 for RF-plasma pretreated samples for 15 min and sputtered for 8 min and then irradiated up to 60 min. The shifts in the peaks for RF-plasma pretreated PE-TiO2 samples in Figures 5(a) and 5(b) are seen to be more important compared to the nonpretreated samples shown in Figures 5(c) and 5(d). This is due to the lower amount of TiO2 on the nonpretreated PE leading to longer bacteria inactivation times. The shifts presented in Figure 5 reflect the structural/conformation changes in LPS during lipid peroxidation involving the production of peroxides, alcohols, and carboxyl type functionalities associated to the bacteriallysis and bacterial dead.Shift of the stretching vibrations as a function of time detected by ATR-FTIR for the asymmetricνa(CH2) vibrational bands and the symmetric νs(CH2) vibrational bands forE. coli up to 60 min under solar simulated irradiation. (a) and (b) show the shifts of νa(CH2) vibrational bands on PE-TiO2 samples pretreated with RF air plasma for 15 min and then sputtered for 8 min. (c) and (d) show the IR shifts of νs(CH2) vibrational bands on nonpretreated PE-sputtered for 8 min.
(a)
(b)
(c)
(d)The decrease in the amplitude observed for the stretching vibrations in the ATR-IR-spectra in Figures5(a)–5(d) was due to isolated double bonds in the LPS. The discontinuous shifts towards the blue in Figures 5(a) and 5(b) suggest an increased mobility of the LPS units in the LPS chain-packing [49]. The increased disorder modifies the frequencies of the –CH2 symmetric and antisymmetric bands, shifting the peak positions during the irradiation time [51]. Figure 2(c), trace (1) shows thatE. coli inactivation is complete within 60 min on PE-TiO2 and this time coincides with the time in which the LPS stretching vibrations attain the highest fluidity. This time coincides with the time to attain the intermolecular distances leading to –CH2 scission (60 min) [52–54].


### 3.1.6. TiO2 Films Sputtered by HIPIMS Leading to AcceleratedE. coli

Figure6 shows the bacterial inactivation kinetics by the HIPIMS TiO2 sputtered samples [28]. As shown in Figure 6, no bacterial inactivation takes place in the dark, but the bacterial inactivation becomes faster for HIPIMS sputtering times between 1 min (trace (5)) and 4 min (trace (2)). Longer deposition times between 10 and 30 min did not accelerate the loss of viability kinetics due to the fact that an increased TiO2 thickness >12 nm sputtered within 4 min leads to (a) bulk inward diffusion of the charge carriers generated on TiO2 under light leading to highly oxidative radicals [6–10] and (b) longer sputtering times facilitate the TiO2 interparticle growth decreasing the TiO2 contact surface with bacteria.Figure 6
E. coli survival on TiO2 HIPIMS-sputtered (5 A) on polyester for different times in the dark and under solar simulated irradiation (50 mW/cm2).The bacterial inactivation time shown in Figure6 for polyester surface sputtered by HIPIMS is faster compared to DC and DCP TiO2-polyester sputtered surfaces [36].


### 3.1.7. DCP and HIPIMS Sputtering of Samples, Electronic Density, and Voltage Considerations

Figure7, left hand side presents a scheme for the DC sputtering and in the middle section Figure 7 shows the sputtering of DCP proceeding with a higher ionization of Ti at higher e-densities (~1016-17 e−/m3) [55]. The HIPIMS with 5A and consequently a much higher energy than the HIPIMS pulses increases the ionization percentage Ti0→Ti3+/Ti4+ with a concomitant increase in the e-densities (~1018-19 e−/m3).Scheme for the magnetron chamber induced M+ ionization by (a) DC, (b) DCP, and (c) HIPIMS sputtering of metal-ions (M+) on 3D substrates showing the higher density ionization induced by HIPIMS.
(a)
(b)
(c)This increased arrival energy of the Ti-ions on the substrate allows the alignment of the Ti-ions on the polyester irregular (rugous) surface enabling a uniform coverage of the 3D polyester, oximeters, and pressure blood measuring devices as usually used in medical facilities. These artifacts are sources of infections, since they are not TiO2 coated. The HIPIMS sputtering shown on the right hand side in Figure 7 allows the uniform sputtering of objects with complex 3D geometry due to their increased e-density interacting more favorably with the negatively biased substrate compared to the less dense production of ionized species shown in Figures 7(a) and 7(b) [29, 55, 56].


## 3.1.1. Support Choice for TiO2 Deposition

This first study addresses the sputtering of TiO2 transparent, uniform, nonscattering films on polyethylene (PE). Sol-gel commercial methods are used to prepare TiO2 thin films on heat resistant substrates. But on nonthermal resistant substrates the thickness of the TiO2 films is not reproducible and they are not mechanically stable [6–10, 15].Polyethylene (PE) is a low cost and is widely available material. It is chemically inert, mechanically stable and flexible, and UV-resistant and does not oxidize in air under sunlight. In addition, the hydrophobic nature of PE allows the deposition of predominantly hydrophobic pathogens. Bacterial hydrophobic outer cell walls will adhere preferentially on hydrophobic surfaces promoting bacterial inactivation. PE-TiO2 films intend to overcome the use of TiO2 powders or suspensions for bacterial disinfection. Suspensions of TiO2 need a long-settlement time after each disinfection cycle being applied with significant loss of catalyst mass [6, 7]. The PE-TiO2 transparent films are designed to increase the quantum yield of the TiO2 radical species in addition to the direct bactericide action of sunlight [11, 14]. TiO2 sputtering does not lead to the deposition of enough TiO2 on the PE due to the low binding capacity of the PE surface. RF-plasma pretreatment induces oxygen negatively charged functional groups, for example, carboxylic, percarboxylic, epoxide, and peroxide groups by the atomic O, excited O, and anionic and cationic O generated in the RF-plasma chamber [12–14]. The PE functionalized negative sites bind the slightly positive sputtered Ti4+(TiO2) through electrostatic attraction involving chelation/complexation [34, 35]. The TiO2 was sputtered immediately after the RF-plasma pretreatment due to the short lifetimes of the surface polar hydrophilic surface sites.


## 3.1.2. PE Pretreatment, TiO2 Surface Sputtered PE, Sample Absorption, and TiO2 Crystalline Phases

The amount of TiO2 on the pretreated PE fabrics was determined by X-ray fluorescence XRF using the nonpretreated fabric as the blank. For the sample pretreated in air for 15 min by RF plasma and sputtered for 8 min, a TiO2 thickness of ~58 nm was attained on PE equivalent to 290 layers. Taking one layer with 1015 atoms/cm2 and the thickness of one layer as 0.2 nm, the rate of TiO2 deposition was of 6×1014 atoms/cm2s. Self-cleaning TiO2 films up to 10 microns thick have been reported [1–5], but in the case of antibacterial coatings TiO2 thicknesses of 1 nm–20 nm have been reported to be effective [3, 6, 7]. TiO2 films DC sputtered for 8 min consist of nanoparticles 10–30 nm in size [36] and the films were reproducible.The RF-plasma induced functional groups only on the PE topmost layers since no color changes occurred destroying the PE structure indicative of PE-degradation [37].The DRS spectra of the PE-TiO2 films are shown in Figure 1 for samples pretreated by RF and UVC light. Sputtering for 1 to 3 min leads to transparent TiO2 films with no significant absorbance and very low antibacterial activity. A decrease of ~5% or more in optical transmittance has been reported for RF-plasma pretreated PE [38]. The decrease in transmittance for the sputtered films in Figure 1 was due to the inherent high refractive index of TiO2.Figure 1
DRS in Kubelka-Munk units versus wavelength of TiO2 sputtered (8 min) on polyethylene: (1) pretreated with UVC 1 torr, (2) pretreated with RF air plasma, (3) pretreated with RF plasma, and (4) TiO2 sputtered on PE for 1 min.The TiO2 crystal phases on PE show by XRD a high anatase (A) peak at 2θ = 21.5° [34] for a PE-TiO2 with and without RF-plasma pretreatment. But XRD peaks of rutile (R) at temperatures ≤130°C found in the DC-magnetron chamber were also observed. The generation of rutile at low temperatures is due to the structure forming function of the PE film on the TiO2 as reported for polyamide and other sputtered TiO2 textiles [12].


## 3.1.3. Antibacterial Kinetics Evaluation and Sample Recycling

Figure2 showsE. coli inactivation on PE-TiO2 films under simulated solar light with an integrated light dose of 52 mW/cm2. The fastest bacterial inactivation was found for pretreated PE samples TiO2 sputtered for 8 min in Figure 2(a). Bacterial inactivation on PE-TiO2 samples is presented in Figure 2 for RF-pretreated PE for different times. No significant bacterial inactivation was observed for bacteria on uncoated PE (Figure 2(a), trace (4)). Only trace (1) was subjected to statistical analyses since it describes the results for the most favorable kinetics and presents the highest amount of TiO2 sites in exposed positions to interact with bacteria [39]. PE-TiO2 sputtered samples for 1 up to 5 min were not loaded with sufficient TiO2 to drive a fast bacterial inactivation. The Ti-loading on PE-TiO2 was determined by XRF for sputtering times of 1, 3, and 5 min and the values found were, respectively, 0.009, 0.019, and 0.031 TiO2 wt%/wt PE.E. coli inactivation on TiO2 sputtered on PE for 8 min irradiated with simulated solar light (52 mW/cm2).
(a)
TiO2 sputtered for different times without RF-plasma pretreatment for (1) 8 min, (2) 10 min, (3) 5 min, and (4) polyethylene alone
(b)
TiO2 sputtered for 8 min with surface RF-plasma pretreatment at 1 torr for (1) 15 min, (2) 20 min, (3) 30 min, and (4) 5 min
(c)
TiO2 sputtered 8 min RF air plasma pretreatment for (1) 15 min, (2) 20 min, (3) 30 min, and (4) 5 min
(d)
TiO2 sputtered 8 min with UVC pretreatment in air for (1) 20 min, (2) 15 min, (3) 10 min, and (4) 5 minSamples sputtered for times >8 min in Figure2(b) led to layer thickness >45 nm. This thickness leads to charge bulk inward diffusion decreasing the charge transfer between the PE-TiO2 and bacteria [40]. TiO2 sputtering for 8 min led to a TiO2 loading with the most suitable thickness for the charge diffusion able to reach bacteria. Figure 2(c), trace (1) shows the fastest bacterial inactivation for PE-TiO2 films. No significant bacterial inactivation was observed for bacteria on PE in the dark.To verify that no regrowth ofE. coli occurs after the first bacterial inactivation cycle, the PE-TiO2 film was incubated on an agar Petri dish for 24 hours at 37°C. No bacterial regrowth was observed meaning that there was no bacteria adhered to the surface after the inactivation cycle.The bacterial inactivation by PE-TiO2 samples sputtered for 8 min and pretreated with RF-plasma in air for 15 min was investigated up to the 6th cycle. The recycling of the samples showed stable inactivation kinetics up to the 5th-cycle; then the recycling kinetics became slower by ~20%. After each cycle, the samples were washed with distilled water and dried. Then, the samples were kept in an oven at 60°C to avoid bacterial contamination. After washing PE-TiO2 the samples were left standing for 24 h before to regain the initial sample hydrophobicity. This aspect will be discussed below in Section 3.1.4 when discussing the hydrophilic-hydrophobic transformation on PE-TiO2 in the dark and shown in Figures 3(a) and 3(b).(a) Photoinduced superhydrophilicity followed by water droplet contact angle during light irradiation at times: (A)t=0 min, (B) 15 min, (C) 30 min, (D) 45 min, and (E) 60 min. (b) Restoration of the hydrophilicity in the dark after times (A) 6 h, (B) 12 h, (C) 18 h, and (D) 24 h.
(a)
(b)


## 3.1.4. Contact Angle (CA) and Hydrophobic Reversible Photoswitching

Figure3(a) presents the hydrophobic to hydrophilic transformation occurring on the PE-TiO2 sample induced by simulated solar light. A decrease of the CA from 121° to less than 5° within 60 min is shown in Figure 3(a) (traces (A)–(E)) concomitant with the time of bacterial inactivation. The recovery from the PE-TiO2 superhydrophilic surface to a hydrophobic initial surface proceeded within 24 hours in the dark as shown in Figure 3(b).The transformation of the initial hydrophobic TiO2 under light irradiation involves the dissociative chemisorption of water on the PE-TiO2 generating Ti-OH groups [41, 42]. Under light irradiation, the PE-TiO2 generates electrons (e−) and holes (h+) producing OH* and O2- radicals. The photogenerated h+ are the precursors of OH*. The structural changes in the TiO2 surface due to hydrophilicity are associated with the generation of these radicals. This process does not require high quantum efficiency in comparison to theE. coliphotocatalytic oxidation. A second mechanism has been suggested for the hydrophobic to hydrophilic transformation and would be due to TiO2 generated charges leading to oxygen vacancies reducing Ti4+ to Ti3+ [43].Figure3(b) shows the hydrophilic to hydrophobic reversible transformation in the dark reinstating the initial TiO2 hydrophobicity within 24 hours. The hydrophilic samples were kept in the dark and the contact angles (CA) were measured at preselected times to follow the back reaction to the initial hydrophobic state. This second process involves the destruction of airborne bacteria or hydrocarbons adsorbed on the PE-TiO2 surface along TiO2 surface dehydration and the back conversion of Ti3+/Ti4+ [42].Figure4(a) illustrates the rate of photoinduced hydrophilicity and Figure 4(b) the restoration rate of the hydrophobicity in the dark as a function of “cos θ”. According to Young’s theory the “cos θ” of a liquid droplet on a solid surface is a function of the interfacial energy between the solid and the liquid. The rate of the hydrophobic to hydrophilic conversion and for the reverse reaction in Figures 4(a) and 4(b) was 0.277 min−1 and was 8.71 × 10−3 min−1, respectively. These rates were calculated by integrating “cos θ” in Young’s equation (1).(a) Kinetics of the hydrophobic-hydrophilic transformation under solar simulated light and (b) kinetics of the dark reverse reaction towards the initial state for PE-TiO2 (8 min) RF air plasma pretreated for 15 min.
(a)
(b)The contact angle (CA) conventionally measures the angle where the liquid meets the solid quantifying the wettability of a solid surface via the Young equation. The Young equation (1) involves solid-vapor, liquid-vapor, and solid-liquid interfacial energies. The solid-vapor interfacial energy is denoted by γSG, the solid-liquid interfacial energy by γSL, and the liquid-vapor interfacial energy (i.e., the surface tension) by γLG; then the equilibrium contact angle θC is determined from these quantities by Young’s equation:
(1)0=γSG-γSL-γLGcos⁡θC.Upon illumination the surface TiO2 energy increases since the TiO2 surface is transformed into a metastable state as shown in (2) decreasing the initial contact angle of 121° (Figure 3(a)) to a value of <5° after 60 min irradiation (Figure 3(b)). Equation (2) shows the TiOH metastable hydrophilic intermediate induced under light:
(2)
The hydrophobic properties of the PE-TiO2 surface are important in antibacterial films.E. coli andStaphylococcus aureus present a preferential adhesion to hydrophilic surfaces [44]. Bacteria with hydrophobic surface properties likeS. epidermidis adhere preferentially to hydrophobic surfaces [45]. Hydrophobic bacteria adhere to a variety of surfaces forming biofilms to a greater extent than hydrophilic bacteria [46]. Recently, R. Amal recently has reported the reversible photoswitching behavior under light by TiO2/Ag nanoparticles [47, 48]. This study shows that UV-A irradiation of brownish Ag/TiO2 changed the surface Ag2O to violet black, the characteristic color of Ag-plasmon. Nano-Ag particles are responsive to visible light due to the enhanced surface plasmon resonance (SPR) absorption band at ~550 nm. As a result of visible light excitation a reverse electron flow from Ag0 to the TiO2cb occurs along the oxidation of metallic Ag0 back to Ag2O. A reversible antimicrobial photoswitching of nano-Ag/TiO2 particles was reported in this study when irradiating the Ag-nanoparticles in two different wavelength regions [48].


## 3.1.5. FTIR Analysis and Bacterial Inactivation on PE-TiO2

FTIR spectroscopy is used in the present study to monitor the changes in the structure/dynamics in theE. coli lipopolysaccharide (LPS) bilayer induced by PE-TiO2 under solar simulated light. LPS amphiphiles constitute the outer cell wall ofE. coli and consist of LPS units. The LPS are made up of fluid chains [49]. (CH2)- and (CH3)-groups make up 70% of the lipopolysaccharide (LPS), phosphatidyl-ethanolcholine (PE), and peptidoglycan (PGN), the main groups making theE. coli cell envelope [49, 50].The characteristic bands of the methylene (–CH2) stretching vibrations in the 2800–2900 cm−1 spectral region are shown in Figure 5. Figure 5(a) shows the shift of the asymmetric methylene stretching vibrations at νa(CH2) 2922.2 cm−1 and of the symmetric stretching vibrations of νs(CH2) at 2849.2 cm−1 for RF-plasma pretreated samples for 15 min and sputtered for 8 min and then irradiated up to 60 min. The shifts in the peaks for RF-plasma pretreated PE-TiO2 samples in Figures 5(a) and 5(b) are seen to be more important compared to the nonpretreated samples shown in Figures 5(c) and 5(d). This is due to the lower amount of TiO2 on the nonpretreated PE leading to longer bacteria inactivation times. The shifts presented in Figure 5 reflect the structural/conformation changes in LPS during lipid peroxidation involving the production of peroxides, alcohols, and carboxyl type functionalities associated to the bacteriallysis and bacterial dead.Shift of the stretching vibrations as a function of time detected by ATR-FTIR for the asymmetricνa(CH2) vibrational bands and the symmetric νs(CH2) vibrational bands forE. coli up to 60 min under solar simulated irradiation. (a) and (b) show the shifts of νa(CH2) vibrational bands on PE-TiO2 samples pretreated with RF air plasma for 15 min and then sputtered for 8 min. (c) and (d) show the IR shifts of νs(CH2) vibrational bands on nonpretreated PE-sputtered for 8 min.
(a)
(b)
(c)
(d)The decrease in the amplitude observed for the stretching vibrations in the ATR-IR-spectra in Figures5(a)–5(d) was due to isolated double bonds in the LPS. The discontinuous shifts towards the blue in Figures 5(a) and 5(b) suggest an increased mobility of the LPS units in the LPS chain-packing [49]. The increased disorder modifies the frequencies of the –CH2 symmetric and antisymmetric bands, shifting the peak positions during the irradiation time [51]. Figure 2(c), trace (1) shows thatE. coli inactivation is complete within 60 min on PE-TiO2 and this time coincides with the time in which the LPS stretching vibrations attain the highest fluidity. This time coincides with the time to attain the intermolecular distances leading to –CH2 scission (60 min) [52–54].


## 3.1.6. TiO2 Films Sputtered by HIPIMS Leading to AcceleratedE. coli

Figure6 shows the bacterial inactivation kinetics by the HIPIMS TiO2 sputtered samples [28]. As shown in Figure 6, no bacterial inactivation takes place in the dark, but the bacterial inactivation becomes faster for HIPIMS sputtering times between 1 min (trace (5)) and 4 min (trace (2)). Longer deposition times between 10 and 30 min did not accelerate the loss of viability kinetics due to the fact that an increased TiO2 thickness >12 nm sputtered within 4 min leads to (a) bulk inward diffusion of the charge carriers generated on TiO2 under light leading to highly oxidative radicals [6–10] and (b) longer sputtering times facilitate the TiO2 interparticle growth decreasing the TiO2 contact surface with bacteria.Figure 6
E. coli survival on TiO2 HIPIMS-sputtered (5 A) on polyester for different times in the dark and under solar simulated irradiation (50 mW/cm2).The bacterial inactivation time shown in Figure6 for polyester surface sputtered by HIPIMS is faster compared to DC and DCP TiO2-polyester sputtered surfaces [36].


## 3.1.7. DCP and HIPIMS Sputtering of Samples, Electronic Density, and Voltage Considerations

Figure7, left hand side presents a scheme for the DC sputtering and in the middle section Figure 7 shows the sputtering of DCP proceeding with a higher ionization of Ti at higher e-densities (~1016-17 e−/m3) [55]. The HIPIMS with 5A and consequently a much higher energy than the HIPIMS pulses increases the ionization percentage Ti0→Ti3+/Ti4+ with a concomitant increase in the e-densities (~1018-19 e−/m3).Scheme for the magnetron chamber induced M+ ionization by (a) DC, (b) DCP, and (c) HIPIMS sputtering of metal-ions (M+) on 3D substrates showing the higher density ionization induced by HIPIMS.
(a)
(b)
(c)This increased arrival energy of the Ti-ions on the substrate allows the alignment of the Ti-ions on the polyester irregular (rugous) surface enabling a uniform coverage of the 3D polyester, oximeters, and pressure blood measuring devices as usually used in medical facilities. These artifacts are sources of infections, since they are not TiO2 coated. The HIPIMS sputtering shown on the right hand side in Figure 7 allows the uniform sputtering of objects with complex 3D geometry due to their increased e-density interacting more favorably with the negatively biased substrate compared to the less dense production of ionized species shown in Figures 7(a) and 7(b) [29, 55, 56].


## 3.2. Uniform TiO2-Doped In2O3 Films Increasing the Bacterial Inactivation Kinetics with Respect to TiO2-Films under Low Intensity Solar Simulated Light

### 3.2.1. TiO2 Sputtered on Pretreated PE

This study shows that the surface modification of TiO2 by doping with In2O3 is an effective route to increase the TiO2 absorption into the visible region. A photoinduced interfacial charge transfer (IFCT) between TiO2 and In2O3 takes place and couples the charge generation/separation between these two oxides. In2O3 has an absorption band in the visible between 400 nm and 500 nm [57].The TiO2 and TiO2-In2O3 thin films were deposited onto polyester in the magnetron chamber by sputtering Ti by DC in a reactive O2 atmosphere followed by DCP sputtering of In, in the presence of mixture of Ar and O2 gases. The total working pressure P=(PAr+PO2) was fixed at 0.5 Pa and the ratio PO2/Ptotal = 4.5%. The sputtering current on the Ti target was 280 mA providing a power of 120 W (U=-450V) and a current density of 12.7 mA/cm2. Pulsed magnetron sputtering (DCP) was used to sputter the In2O3 and was operated at 50 kHz with 15% reversed voltage. The sputtering power was fixed at 50 W providing a negative voltage of −500 V and a power of 140 W.


### 3.2.2. Evaluation of the Bacterial Inactivation ofE. coli in the Dark and under Light

The counting of the bacterial inactivation ofE. coli was performed as described above in Section 2.4 [28, 36]. An actinic irradiation lamp Osram Lumilux T8-L 18 W (4.0 mW/cm2) was used in Figure 8 as a source of white light. This light is used for the indoors lightning in health facilities. The solar simulator (Heraeus, Hanau, Germany) emitting between 200 and 800 nm from a 100 W Xe-light resembling the solar spectrum and set at 50 mW/cm2. The value of 50 mW/cm2 is the average light dose reaching central European countries. Figure 8 shows the inactivation ofE. coli by TiO2, TiO2-In2O3, and In2O3 samples.E. coli inactivation under solar simulated light for (1) TiO2/In2O3 (sputtered for 10 min/10 s), (2) TiO2 (sputtered for 10 min), (3) In2O3 (sputtered for 10 s) samples, respectively, and (4) a bare polyester sample, at light intensities: (a) 30 mW/cm2 and (b) 50 mW/cm2.
(a)
(b)A synergic interaction of TiO2 is required to lead to fast bacterial inactivation in Figure 8(a), trace (1). Figure 8(b), trace (4) shows that no bacterial inactivation was possible under light on bare polyester. Figure 8(a) reports the effect of the light intensity on the amount of charges in the coupled semiconductors at 30 mW/cm2 and 50 mW/cm2. A higher light intensity increases the amount of semiconductor charges interacting with bacteria leading to a faster bacterial inactivation. The accelerated bacterial inactivation by the TiO2-In2O3 photocatalysts compared to bare TiO2 samples is favoured by the electrostatic attraction existing between the positive charged Ti and the negativeE. coli cell wall at pH 6-7. TheE. coli is negatively charged between pH 3–9 due to the excess of carboxylic groups compared to the amide I and amide II cell wall positively charged groups [3, 58]. The TiO2 bacterial inactivation under light has been widely reported and will not be discussed in this study [6–10].Figure9 shows repetitive disinfection cycles by a TiO2-In2O3 sputtered for 10 min from a TiO2 target and 10 s from an In target in a reactive O2 atmosphere, up to the 5th cycle. The 8th cycle shows a loss of bacterial inactivation kinetics when actinic light was used in Figure 9(a) and when a solar simulator with a dose of 50 mW/cm2 was applied. The slower kinetics shown in Figure 9(b) in the last cycle was due possibly to the leaching of In and Ti-nanoparticles detected by ICP-Ms (data not shown).E. coli inactivation recycling experiments on TiO2/In2O3 sputtered for 10 min/10 s on polyester under irradiation by: (a) Osram Lumilux T8-L 18 W (4.0 mW/cm2, 360 to 800 nm) and (b) Suntest solar simulator 50 mW/cm2.
(a)
(b)


### 3.2.3. Diffuse Reflectance Spectroscopy (DRS) and X-Ray Diffraction (XRD) Investigation of TiO2 and TiO2-In2O3 Films

Figure10 shows the UV-Vis reflectance spectra of TiO2 sputtered as a function of time. The Kubelka-Munk (KM/S) relations convert reflectance measurements into absorption spectra units. K and S are the absorption and scattering coefficients, respectively, of TiO2 in Figure 10(a). The KM/S values for the samples were found proportional to the TiO2 sputtering time. The faster bacterial inactivation induced by TiO2-In2O3 and shown in Figure 8 suggests an electron transfer from In2O3 to TiO2.Diffuse reflectance spectra (DRS) of TiO2 and TiO2/In2O3 samples in Kubelka-Munk units: (a) TiO2 1 min, TiO2 5 min, and TiO2 10 min. (b) TiO2 10 min/In2O3 5 s, TiO2 10 min/In2O3 10 s, TiO2 10 min/In2O3 20 s, and TiO2 10 min/In2O340 s, In2O3 10 s.
(a)
(b)Figure10(b) shows a progressive increase in optical absorption (KM/S spectra) in the region 350 nm. Samples sputtered with In2O3 for 5–20 s show lower absorption intensities. Figure 10(b) shows a weak absorption band from 400 to 500 nm, attributed to the interfacial charge transfer (IFCT) from the TiO2 to In2O3. The weak absorption between 500 and 600 nm is due to the In2O3 interband indirect transitions at potential levels 2.09 eV [25]. These electronic transitions occur from the In2O3 valence band to two levels near the conduction band ≥2 eV [59]. The TiO2-In2O3 transition seems to originate from the In2O3 (In5s5p orbital) to the conduction band of TiO2. The light green color In2O3 samples with band-gap of 2.5–2.8 eV (absorption edge ~470–500 nm) became darker at longer sputtering times [60, 61].Figure11 shows the TiO2 XRD of TiO2 and In2O3/TiO2 films, respectively. Figure 11 presents the XRD diffraction for the TiO2 DC sputtered on polyester for 10 min. The intense anatase peak at 24.6° is due to the presence of anatase. No specific signal due to In2O3 was detected due to its very low loading (<0.2%). Only a slight decrease in intensity of the 24.6° (101) anatase peak was observed in the In2O3/TiO2 samples. No modification in the TiO2 diffraction peaks due to In2O3 was observed, suggesting that no lattice modification due to In-doping takes place in the TiO2 network.Figure 11
XRD diffraction data for(1) TiO2 sputtered for 10 min on polyester and (2) TiO2 10 min/In2O3 10 s sputtered on polyester: (a) diffraction patterns of anatase (b), rutile (c), and (d) cubic In2O3.


### 3.2.4. Interfacial Charge Transfer Mechanism (IFCT) in TiO2-In2O3 Composite Films

Coupling TiO2-In2O3 induced a significant increase in the photocatalytic activity compared to TiO2 alone and In2O3 as shown in Figure 8. This significant increase can be rationalized by the relative positions of the conduction band (cb) and valence band (vb) in In2O3 and TiO2. The cb of In2O3 at −0.62 versus NHE [60, 61] transfers the cb electrons to TiO2 (cb at 0.2 eV versus NHE for anatase). The UV component of sunlight generates TiO2 holes able to transfer to In2O3 vb as shown in Figure 12(a). The subsequent spatial separation of photogenerated charge carries and the e− and h+ injection limit the e−/h+ recombination on TiO2.(a) Scheme of the charge injection during the interfacial charge transfer (IFCT) between In2O3 and TiO2 under simulated sunlight. (b) Radical(s) reaction generated from O2 reduction on TiO2 (R: bacteria degradation or species produced during the bacterial degradation).
(a)
(b)The highly dispersed In2O3 on the TiO2 layers builds a Schottky barrier at the TiO2/In2O3 interface. This precludes partly the recombination of electrons and holes in TiO2. The scheme in Figure 12(a) suggests an IFCT to take place in the TiO2-In2O3 assuming that the generated charges have a sufficient lifetime to diffuse to the photocatalyst surface inactivating bacteria. The TiO2 is the main photocatalyst and the In2O3 acts as a visible light sensitizer. In Figure 12(a) a detrimental effect may be due to the cross interparticle recombination of the e-cb of TiO2 with the h+vb of In2O3 [62].Figure12(b) shows schematically the e-cb in the TiO2 and In2O3 particles reacting with the adsorbed O2 on the TiO2 surface to yield O2-∙ radical anion and subsequently other highly oxidative protonated radicals active in the bacterial inactivation.


## 3.2.1. TiO2 Sputtered on Pretreated PE

This study shows that the surface modification of TiO2 by doping with In2O3 is an effective route to increase the TiO2 absorption into the visible region. A photoinduced interfacial charge transfer (IFCT) between TiO2 and In2O3 takes place and couples the charge generation/separation between these two oxides. In2O3 has an absorption band in the visible between 400 nm and 500 nm [57].The TiO2 and TiO2-In2O3 thin films were deposited onto polyester in the magnetron chamber by sputtering Ti by DC in a reactive O2 atmosphere followed by DCP sputtering of In, in the presence of mixture of Ar and O2 gases. The total working pressure P=(PAr+PO2) was fixed at 0.5 Pa and the ratio PO2/Ptotal = 4.5%. The sputtering current on the Ti target was 280 mA providing a power of 120 W (U=-450V) and a current density of 12.7 mA/cm2. Pulsed magnetron sputtering (DCP) was used to sputter the In2O3 and was operated at 50 kHz with 15% reversed voltage. The sputtering power was fixed at 50 W providing a negative voltage of −500 V and a power of 140 W.


## 3.2.2. Evaluation of the Bacterial Inactivation ofE. coli in the Dark and under Light

The counting of the bacterial inactivation ofE. coli was performed as described above in Section 2.4 [28, 36]. An actinic irradiation lamp Osram Lumilux T8-L 18 W (4.0 mW/cm2) was used in Figure 8 as a source of white light. This light is used for the indoors lightning in health facilities. The solar simulator (Heraeus, Hanau, Germany) emitting between 200 and 800 nm from a 100 W Xe-light resembling the solar spectrum and set at 50 mW/cm2. The value of 50 mW/cm2 is the average light dose reaching central European countries. Figure 8 shows the inactivation ofE. coli by TiO2, TiO2-In2O3, and In2O3 samples.E. coli inactivation under solar simulated light for (1) TiO2/In2O3 (sputtered for 10 min/10 s), (2) TiO2 (sputtered for 10 min), (3) In2O3 (sputtered for 10 s) samples, respectively, and (4) a bare polyester sample, at light intensities: (a) 30 mW/cm2 and (b) 50 mW/cm2.
(a)
(b)A synergic interaction of TiO2 is required to lead to fast bacterial inactivation in Figure 8(a), trace (1). Figure 8(b), trace (4) shows that no bacterial inactivation was possible under light on bare polyester. Figure 8(a) reports the effect of the light intensity on the amount of charges in the coupled semiconductors at 30 mW/cm2 and 50 mW/cm2. A higher light intensity increases the amount of semiconductor charges interacting with bacteria leading to a faster bacterial inactivation. The accelerated bacterial inactivation by the TiO2-In2O3 photocatalysts compared to bare TiO2 samples is favoured by the electrostatic attraction existing between the positive charged Ti and the negativeE. coli cell wall at pH 6-7. TheE. coli is negatively charged between pH 3–9 due to the excess of carboxylic groups compared to the amide I and amide II cell wall positively charged groups [3, 58]. The TiO2 bacterial inactivation under light has been widely reported and will not be discussed in this study [6–10].Figure9 shows repetitive disinfection cycles by a TiO2-In2O3 sputtered for 10 min from a TiO2 target and 10 s from an In target in a reactive O2 atmosphere, up to the 5th cycle. The 8th cycle shows a loss of bacterial inactivation kinetics when actinic light was used in Figure 9(a) and when a solar simulator with a dose of 50 mW/cm2 was applied. The slower kinetics shown in Figure 9(b) in the last cycle was due possibly to the leaching of In and Ti-nanoparticles detected by ICP-Ms (data not shown).E. coli inactivation recycling experiments on TiO2/In2O3 sputtered for 10 min/10 s on polyester under irradiation by: (a) Osram Lumilux T8-L 18 W (4.0 mW/cm2, 360 to 800 nm) and (b) Suntest solar simulator 50 mW/cm2.
(a)
(b)


## 3.2.3. Diffuse Reflectance Spectroscopy (DRS) and X-Ray Diffraction (XRD) Investigation of TiO2 and TiO2-In2O3 Films

Figure10 shows the UV-Vis reflectance spectra of TiO2 sputtered as a function of time. The Kubelka-Munk (KM/S) relations convert reflectance measurements into absorption spectra units. K and S are the absorption and scattering coefficients, respectively, of TiO2 in Figure 10(a). The KM/S values for the samples were found proportional to the TiO2 sputtering time. The faster bacterial inactivation induced by TiO2-In2O3 and shown in Figure 8 suggests an electron transfer from In2O3 to TiO2.Diffuse reflectance spectra (DRS) of TiO2 and TiO2/In2O3 samples in Kubelka-Munk units: (a) TiO2 1 min, TiO2 5 min, and TiO2 10 min. (b) TiO2 10 min/In2O3 5 s, TiO2 10 min/In2O3 10 s, TiO2 10 min/In2O3 20 s, and TiO2 10 min/In2O340 s, In2O3 10 s.
(a)
(b)Figure10(b) shows a progressive increase in optical absorption (KM/S spectra) in the region 350 nm. Samples sputtered with In2O3 for 5–20 s show lower absorption intensities. Figure 10(b) shows a weak absorption band from 400 to 500 nm, attributed to the interfacial charge transfer (IFCT) from the TiO2 to In2O3. The weak absorption between 500 and 600 nm is due to the In2O3 interband indirect transitions at potential levels 2.09 eV [25]. These electronic transitions occur from the In2O3 valence band to two levels near the conduction band ≥2 eV [59]. The TiO2-In2O3 transition seems to originate from the In2O3 (In5s5p orbital) to the conduction band of TiO2. The light green color In2O3 samples with band-gap of 2.5–2.8 eV (absorption edge ~470–500 nm) became darker at longer sputtering times [60, 61].Figure11 shows the TiO2 XRD of TiO2 and In2O3/TiO2 films, respectively. Figure 11 presents the XRD diffraction for the TiO2 DC sputtered on polyester for 10 min. The intense anatase peak at 24.6° is due to the presence of anatase. No specific signal due to In2O3 was detected due to its very low loading (<0.2%). Only a slight decrease in intensity of the 24.6° (101) anatase peak was observed in the In2O3/TiO2 samples. No modification in the TiO2 diffraction peaks due to In2O3 was observed, suggesting that no lattice modification due to In-doping takes place in the TiO2 network.Figure 11
XRD diffraction data for(1) TiO2 sputtered for 10 min on polyester and (2) TiO2 10 min/In2O3 10 s sputtered on polyester: (a) diffraction patterns of anatase (b), rutile (c), and (d) cubic In2O3.


## 3.2.4. Interfacial Charge Transfer Mechanism (IFCT) in TiO2-In2O3 Composite Films

Coupling TiO2-In2O3 induced a significant increase in the photocatalytic activity compared to TiO2 alone and In2O3 as shown in Figure 8. This significant increase can be rationalized by the relative positions of the conduction band (cb) and valence band (vb) in In2O3 and TiO2. The cb of In2O3 at −0.62 versus NHE [60, 61] transfers the cb electrons to TiO2 (cb at 0.2 eV versus NHE for anatase). The UV component of sunlight generates TiO2 holes able to transfer to In2O3 vb as shown in Figure 12(a). The subsequent spatial separation of photogenerated charge carries and the e− and h+ injection limit the e−/h+ recombination on TiO2.(a) Scheme of the charge injection during the interfacial charge transfer (IFCT) between In2O3 and TiO2 under simulated sunlight. (b) Radical(s) reaction generated from O2 reduction on TiO2 (R: bacteria degradation or species produced during the bacterial degradation).
(a)
(b)The highly dispersed In2O3 on the TiO2 layers builds a Schottky barrier at the TiO2/In2O3 interface. This precludes partly the recombination of electrons and holes in TiO2. The scheme in Figure 12(a) suggests an IFCT to take place in the TiO2-In2O3 assuming that the generated charges have a sufficient lifetime to diffuse to the photocatalyst surface inactivating bacteria. The TiO2 is the main photocatalyst and the In2O3 acts as a visible light sensitizer. In Figure 12(a) a detrimental effect may be due to the cross interparticle recombination of the e-cb of TiO2 with the h+vb of In2O3 [62].Figure12(b) shows schematically the e-cb in the TiO2 and In2O3 particles reacting with the adsorbed O2 on the TiO2 surface to yield O2-∙ radical anion and subsequently other highly oxidative protonated radicals active in the bacterial inactivation.


## 3.3. New Evidence for the Inactivation of TiO2 Films with Bacteria in the Dark

This study addresses the design, preparation, and bacterial counting of the bacterial inactivation kinetics and characterization of TiO2-polyester surfaces inducing cell wall damage with concomitant loss of bacterial viability in the dark. In 1985, Matsunaga et al., [63] reported that TiO2 suspensions inactivate bacteria. After Matsunaga many studies have reported on the TiO2 photocatalytic bacterial cell wall damage [64–66]. The bacterial inactivation by agents permeating into the cell structure has also been widely reported [5, 6, 67]. Few articles have reported cell wall damages by the photocatalysis by electron microscopy (EM) [5].P. aeruginosa outer cell wall damages due to TiO2 photocatalysis have been reported recently by P. Amezaga-Madrid et al. [68–74]. The TiO2 interaction with the bacteria was reported to cause damages/disorganization in the cell wall morphology modifying its permeability and the capacity to regulate the outer layers osmotic pressures. The importance of the present study on antimicrobial surfaces relates to the fact that bacteria survive for long times in hospital facilities increasingly leading to hospital acquired infections (HAI). Precluding the infectious biofilm formation by the TiO2-polyester surfaces in the dark is an effective way to reduce/suppress infections as will be reported in this study.


### 3.3.1. Preparation of TiO2-Polyester by the Hydrothermal Route andE. coli Loss of Viability in the Dark and under White Light

The TiO2 on the polyester deposition by the hydrothermal route (HT) was carried out as follows: titanium tetraisopropoxide (TTIP) Sigma Aldrich p.a. was dissolved in isopropanol in a 1 : 3 volume ratio (1 : 3 molar ratio). This solution was poured into a beaker with 50 mL of 0.1 M HNO3. The polyester samples 6 × 4 cm were immersed into the acid TiO2 precursor suspension and heated under stirring in a reflux condenser for 2 hours at 80°C. The polyester fabric was removed from the suspension, rinsed with demineralized water, and treated in ultrasound bath for 2 min to remove unbound TiO2 particles. The last operation was repeated three times and the TiO2-polyester fabric were subsequently dried for 2 hours at 70°C in air [75]. The inactivation ofEscherichia coli (E. coli K12) on TiO2 polyester samples was evaluated according to Section 2.4.In Figure12 no significant bacterial loss of viability was observed for bacteria on uncoated samples (Figure 13, trace (1)). A loading of 0.05% TiO2 on the TiO2-polyester in Figure 13, trace (2) did not contain enough TiO2 to induce bacteria loss of viability. TiO2 loadings between 0.1% and 5% led to similar bacterial loss of viability within 120 min. This indicates that the number of cells capable of forming colonies in contact with the cell wall surface attained a stable value for TiO2-polyester surfaces loaded between 0.1% and 5.0%.Figure 13
Loss of bacterial viability in the dark mediated by TiO2-polyester (HT) prepared samples with different TiO2 loadings: (1) polyester alone, (2) 0.05%, (3) 0.1%, (4) 0.5%, (5)1% and (6) 5%.Figure14 shows the loss of bacterial viability under light irradiation within 60 min for TiO2-polyester at loadings above TiO2 0.1%. The insert in Figure 14 shows the spectral emission of the actinic Osram Lumilux 18 W/827 light used with a dose of 4.0 mW/cm2. The mechanism leading to bacterial inactivation under light has been reported by Foster et al., [4] and Tung and Daoud, [10]. More recently, our EPFL laboratory has reported in a detailed way the partial damage/degradation of theE. coli outer cell functional groups during TiO2 photocatalysis by ATR-IR spectroscopy [50, 66].Figure 14
Loss of bacterial viability ofE. coli under Osram Lumilux 18 W/827 irradiation mediated by TiO2-polyester HT prepared samples with a TiO2 loading: (1) polyester alone, (2) 0.05% (3) 0.1% (4) 0.5%, (5)1% and (6) 5%.By X-ray diffraction spectroscopy (XRD) the TiO2 crystalline phases on the 5% TiO2-polyester prepared by the HT-method show a significant anatase (A) peak at 2θ = 21.5° and a small rutile peak at 2θ = 37.3°. These XRD results showing the formation of anatase and rutile peaks are due to the structure forming function of the polyester at low temperatures when colloidal TiO2 suspensions were added. When heating TiO2 suspensions by themselves anatase was formed ~300°C and rutile at around 600°C in the absence of a structure forming surface like polyester [9, 12, 13]. These last temperatures are significantly higher compared to temperatures ~80°C required to prepare the TiO2 with anatase and rutile phases as detected by XRD.


### 3.3.2. Transmission Electron Microscopy of theE. coli Cell Wall Interaction with TiO2-Polyester. Sample Preparation and Process Kinetics

The samples of the TiO2 polyester for the electron microscopy of theE. coli interaction with TiO2-polyester fabrics were prepared in the following way: suspensions orE. coli were fixed in paraformaldehyde 2% + glut 0.2% in phosphate buffer for 30 min and centrifuged and pellet resuspended in low melting point agarose. This was then cut into small cubes, dehydrated, and stained for 20 min in 2% uranyl acetate then dehydrated in a graded alcohol series. The samples were then embedded in LR white resin in Beam capsules and polymerized overnight at 55°C. The resin blocks containing theE. coli on TiO2-polyester were thin sectioned to a 70 nm thickness with an ultramicrotome (Leica UC7). The TiO2-polyester fibers were embedded in epoxy and thin sectioned at a thickness of 80 to 100 nm.The transmission electron microscopy (TEM) of the TiO2-polyester (HT) samples interacting withE. coli is shown in Figure 15. The TEM in the upper left corner in Figure 15 shows the interaction of TiO2-polyester (HT) sample with theE. coli K12 at time zero. TheE. coli intact cell wall is seen as well as the aggregates and coaggregates of TiO2 positioned at a distance from the cell wall in agreement with the DLVO theory of colloidal stability. TiO2 nanoparticle aggregation sets in at a pH close to the isoelectric point (IEP) of 6-7 due to the attractive Van der Waals forces leading to TiO2 aggregation within 30 min as shown in the TEM in the upper right corner [76]. The TiO2 single particles present sizes between 40 and 60 nm and the hydrodynamic diameter of the aggregates was found to be 170–240 nm equivalent to 3-4 primary TiO2 particles. After 30 min, the TiO2 aggregates accumulate on the cell wall surface due to their almost neutral charge at physiological pH and this is shown in the right upper hand side Figure 15. Damage in the cell wall is localized in the contact area between the TiO2 and bacteria due to (a) the weak attraction between the TiO2 (IEP ~6-7) and the negatively charged cell wall. Damage in the cell wall was observed at a pH close to the TiO2 IEP (charge zero). The TiO2 particles aggregate between themselves since they have an almost neutral charge. Concomitantly the Van der Waals attractive forces drive the interaction between the TiO2-aggregates and the bacterial cell wall and (b) damage to the cell wall is also possible due to the abrasion by the TiO2 rutile component of theE. coli envelope [77]. The effect of the cell wall in the dark after 30 minutes seems to be critical step in the loss of bacterial viability.Figure 15
TEM biomicroscopy of TiO2-polyester 5% (HT) interacting with theE. coli cell wall in the dark: (i) upper left hand side: time zero, (ii) upper right hand side: time 30 min, and (iii) central lower position: time 120 min. For more details see text.The lower central TEM in Figure15 shows the damage to theE. coli outer wall cell within 120 min. After 120 min the wall outer layers present discontinuities in some regions and vanished in other regions. Cell wall damages leading to cell inactivation involve changes in cell morphology, cell-wall microstructure, and local pH [78]. The extensive damage to the outer cell layers after 120 min coincides with the time required for the total loss of cell viability in the dark shown in Figure 13. The bacterial cell cannot function anymore as a membrane regulating the in and out osmotic pressure and material flow. Sunada et al. reportedE. coli inactivation by TiO2 films damaging the cell wall membrane due to the leakage of internal cell components [79].


## 3.3.1. Preparation of TiO2-Polyester by the Hydrothermal Route andE. coli Loss of Viability in the Dark and under White Light

The TiO2 on the polyester deposition by the hydrothermal route (HT) was carried out as follows: titanium tetraisopropoxide (TTIP) Sigma Aldrich p.a. was dissolved in isopropanol in a 1 : 3 volume ratio (1 : 3 molar ratio). This solution was poured into a beaker with 50 mL of 0.1 M HNO3. The polyester samples 6 × 4 cm were immersed into the acid TiO2 precursor suspension and heated under stirring in a reflux condenser for 2 hours at 80°C. The polyester fabric was removed from the suspension, rinsed with demineralized water, and treated in ultrasound bath for 2 min to remove unbound TiO2 particles. The last operation was repeated three times and the TiO2-polyester fabric were subsequently dried for 2 hours at 70°C in air [75]. The inactivation ofEscherichia coli (E. coli K12) on TiO2 polyester samples was evaluated according to Section 2.4.In Figure12 no significant bacterial loss of viability was observed for bacteria on uncoated samples (Figure 13, trace (1)). A loading of 0.05% TiO2 on the TiO2-polyester in Figure 13, trace (2) did not contain enough TiO2 to induce bacteria loss of viability. TiO2 loadings between 0.1% and 5% led to similar bacterial loss of viability within 120 min. This indicates that the number of cells capable of forming colonies in contact with the cell wall surface attained a stable value for TiO2-polyester surfaces loaded between 0.1% and 5.0%.Figure 13
Loss of bacterial viability in the dark mediated by TiO2-polyester (HT) prepared samples with different TiO2 loadings: (1) polyester alone, (2) 0.05%, (3) 0.1%, (4) 0.5%, (5)1% and (6) 5%.Figure14 shows the loss of bacterial viability under light irradiation within 60 min for TiO2-polyester at loadings above TiO2 0.1%. The insert in Figure 14 shows the spectral emission of the actinic Osram Lumilux 18 W/827 light used with a dose of 4.0 mW/cm2. The mechanism leading to bacterial inactivation under light has been reported by Foster et al., [4] and Tung and Daoud, [10]. More recently, our EPFL laboratory has reported in a detailed way the partial damage/degradation of theE. coli outer cell functional groups during TiO2 photocatalysis by ATR-IR spectroscopy [50, 66].Figure 14
Loss of bacterial viability ofE. coli under Osram Lumilux 18 W/827 irradiation mediated by TiO2-polyester HT prepared samples with a TiO2 loading: (1) polyester alone, (2) 0.05% (3) 0.1% (4) 0.5%, (5)1% and (6) 5%.By X-ray diffraction spectroscopy (XRD) the TiO2 crystalline phases on the 5% TiO2-polyester prepared by the HT-method show a significant anatase (A) peak at 2θ = 21.5° and a small rutile peak at 2θ = 37.3°. These XRD results showing the formation of anatase and rutile peaks are due to the structure forming function of the polyester at low temperatures when colloidal TiO2 suspensions were added. When heating TiO2 suspensions by themselves anatase was formed ~300°C and rutile at around 600°C in the absence of a structure forming surface like polyester [9, 12, 13]. These last temperatures are significantly higher compared to temperatures ~80°C required to prepare the TiO2 with anatase and rutile phases as detected by XRD.


## 3.3.2. Transmission Electron Microscopy of theE. coli Cell Wall Interaction with TiO2-Polyester. Sample Preparation and Process Kinetics

The samples of the TiO2 polyester for the electron microscopy of theE. coli interaction with TiO2-polyester fabrics were prepared in the following way: suspensions orE. coli were fixed in paraformaldehyde 2% + glut 0.2% in phosphate buffer for 30 min and centrifuged and pellet resuspended in low melting point agarose. This was then cut into small cubes, dehydrated, and stained for 20 min in 2% uranyl acetate then dehydrated in a graded alcohol series. The samples were then embedded in LR white resin in Beam capsules and polymerized overnight at 55°C. The resin blocks containing theE. coli on TiO2-polyester were thin sectioned to a 70 nm thickness with an ultramicrotome (Leica UC7). The TiO2-polyester fibers were embedded in epoxy and thin sectioned at a thickness of 80 to 100 nm.The transmission electron microscopy (TEM) of the TiO2-polyester (HT) samples interacting withE. coli is shown in Figure 15. The TEM in the upper left corner in Figure 15 shows the interaction of TiO2-polyester (HT) sample with theE. coli K12 at time zero. TheE. coli intact cell wall is seen as well as the aggregates and coaggregates of TiO2 positioned at a distance from the cell wall in agreement with the DLVO theory of colloidal stability. TiO2 nanoparticle aggregation sets in at a pH close to the isoelectric point (IEP) of 6-7 due to the attractive Van der Waals forces leading to TiO2 aggregation within 30 min as shown in the TEM in the upper right corner [76]. The TiO2 single particles present sizes between 40 and 60 nm and the hydrodynamic diameter of the aggregates was found to be 170–240 nm equivalent to 3-4 primary TiO2 particles. After 30 min, the TiO2 aggregates accumulate on the cell wall surface due to their almost neutral charge at physiological pH and this is shown in the right upper hand side Figure 15. Damage in the cell wall is localized in the contact area between the TiO2 and bacteria due to (a) the weak attraction between the TiO2 (IEP ~6-7) and the negatively charged cell wall. Damage in the cell wall was observed at a pH close to the TiO2 IEP (charge zero). The TiO2 particles aggregate between themselves since they have an almost neutral charge. Concomitantly the Van der Waals attractive forces drive the interaction between the TiO2-aggregates and the bacterial cell wall and (b) damage to the cell wall is also possible due to the abrasion by the TiO2 rutile component of theE. coli envelope [77]. The effect of the cell wall in the dark after 30 minutes seems to be critical step in the loss of bacterial viability.Figure 15
TEM biomicroscopy of TiO2-polyester 5% (HT) interacting with theE. coli cell wall in the dark: (i) upper left hand side: time zero, (ii) upper right hand side: time 30 min, and (iii) central lower position: time 120 min. For more details see text.The lower central TEM in Figure15 shows the damage to theE. coli outer wall cell within 120 min. After 120 min the wall outer layers present discontinuities in some regions and vanished in other regions. Cell wall damages leading to cell inactivation involve changes in cell morphology, cell-wall microstructure, and local pH [78]. The extensive damage to the outer cell layers after 120 min coincides with the time required for the total loss of cell viability in the dark shown in Figure 13. The bacterial cell cannot function anymore as a membrane regulating the in and out osmotic pressure and material flow. Sunada et al. reportedE. coli inactivation by TiO2 films damaging the cell wall membrane due to the leakage of internal cell components [79].


## 4. Conclusions

(i)
This study accounts on self-disinfecting and self-cleaning TiO2 films recently investigated in our laboratory. The design, preparation, evaluation, and characterization of uniform, adhesive, and innovative photocatalytic TiO2 coatings are described.
(ii)
It is possible by traditional DC, DCP, and HIPIMS sputtering to produce antibacterial films on 2D and 3D objects at low temperature on polymer films and textile fabrics not resisting higher temperatures.
(iii)
The microstructure of TiO2 films still has to be characterized to find the most suitable microstructure leading to disinfection in the minutes/seconds and not in hours.
(iv)
An interdisciplinary approach is necessary when working in the field of self-disinfecting coatings as presented in this study.
(v)
A considerable saving in Ti and deposition time (energy) was found with HIPIMS compared to conventional DC/DCP sputtering when coating surfaces.
(vi)
TiO2-polyester surfaces have been shown in this study to inactivate bacteria in the dark. This is an important point not addressed generally in bacterial inactivation studies addressing mainly TiO2 photocatalysis.



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*Source: 785037-2014-05-05.xml*