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Effect of Argon-Oxygen Mixing Gas during Magnetron Sputtering on Ti[O.sub.2] Coatings.

1. Introduction

Over the last few years, a great attention has been focused on the titania. Ti[O.sub.2] coatings are extensively used in a wide range of applications such as gas sensor, high refractive index, nontoxicity, good mechanical properties, and the photocatalysts due to remarkable optical, electrical, and chemical properties [1-4]. Coatings such as Ti[O.sub.2], Si[O.sub.2], and [Al.sub.2][O.sub.3] with very low electronic conductance or insulating properties are known to effectively protect metals and alloys from corrosive environment. Titanium dioxide (Ti[O.sub.2]) exhibits wide band gap and possesses good passivating surface with low anodic dissolution rate making it one of the promising materials for corrosion protection [5-7]. Different deposition techniques, such as chemical vapor deposition [8], dip coating [9], magnetron sputtering [10], are used to deposit Ti[O.sub.2] coatings.

The objective of this study is to reveal the effects of oxygen partial pressure on the corrosion behavior properties of the Ti[O.sub.2] thin coating, deposited on unheated substrates by modifying the [O.sub.2] concentration in Ar/[O.sub.2] mixture of an r.f. magnetron sputtering discharge under two distinct sputtering powers.

2. Materials and Methods

2.1. Deposition ofTi[O.sub.2] Coating. Ti[O.sub.2] coatings were deposited by r.f. (13.56 MHz) magnetron sputtering onto stainless steel substrates (1 cm in diameter). The details of the deposition chamber can be found in our previous work [11, 12]. The distance between the target and the substrate holder is about 55 mm. The gases used are high-purity argon (99.99990%) as the working gas and oxygen (99.99%) as reactive gas. After evacuating the sputtering chamber down to a pressure of 1.33 x [10.sup.-7] Pa, the gases (Ar + [O.sub.2]) were introduced into the chamber.

The Ti[O.sub.2] thin films were deposited onto steel (cylindrical: thickness and diameter of 1 cm), where their working faces were mechanically polished to a mean roughness of about 20 nm. Thereafter the samples were ultrasonically cleaned in an acetone bath for 10 min, followed by rinsing with alcohol and then air dried prior to the deposition process. In our previous work [12, 13], we showed that the physical and chemical properties of Ti[O.sub.2] films are strongly influenced by the value of applied negative bias on the substrate in the magnetron sputtering. In the present work, we limit our investigation to the effect of oxygen partial pressure on the Ti[O.sub.2] films deposited by magnetron sputtering, while keeping the rest of the parameters constant (see Table 1). In order to improve the adhesion of the Ti[O.sub.2] on steel an intermediate layer of Ti of 200 mm thickness was deposited [14,15] which enhances the nucleation density and reduces the surface roughness of the coating.

2.2. Characterization. To investigate the structure of Ti[O.sub.2] films deposited on the stainless steel surface, a Bruker Axe D8 Advance diffractometer was used in a Bragg-Brentano geometry, at room temperature, with Cu[alpha] K radiation (Ka = 1.5406 [Angstrom]). The diffractometer acquiring range is between 0 and 90[degrees], with a 0.01[degrees] resolution and the angle of incidence minimum is 0.1[degrees]. The mechanical properties of the films, such as hardness (H) and Young's modulus (E), were investigated using the CSM Instrument Switzerland nanoindenter equipped with a Berkovich diamond indenter tip. In order to avoid the effect of nonuniformity of the coating, a series of 10 indents were performed and the results were averaged. The indenter was operated in the continuous stiffness mode with a maximum load of 100 mN. The applied load is 3 mN. The indents were separated by about 10 [micro]m for preventing overlapping effects. Fourier transform infrared (FTIR) analysis has been done in reflection mode in the setting (70, polarized light) with wavenumbers in the range 4000-400 [cm.sup.-1] using a (Thermo Nicolet Nexus) spectrometer equipped with a deuterated triglycine sulphate detector.

The corrosion resistance of Ti[O.sub.2] coatings was evaluated by potentiodynamic polarization test using a PARSTAT 4000. The measurement was conducted using a conventional three-electrode electrochemical cell in 3.5 wt. % NaCl solution: a saturated calomel electrode (SCE) as the reference electrode, a carbon as the counter electrode (CE), and the samples with 1 [cm.sup.2] exposed area as the working electrode (WE).

3. Results and Discussion

3.1. Structure. Commonly, Ti[O.sub.2] is found in two stable crystalline phases, anatase and rutile, when it is deposited by reactive magnetron sputtering. The phase composition of the Ti[O.sub.2] films is shown in Figure 1. The patterns show that the deposited films exhibit a crystalline phase and the strong peak observed at 20 = 45[degrees] corresponds to (111) plane of iron generated by the substrate. The crystalline structure of Ti[O.sub.2] films changes from pure rutile (percentage of [O.sub.2] = 30%) to the mixture of anatase and rutile with decreasing content of oxygen in argon-oxygen gas mixture (percentage of [O.sub.2] = 20, 10 and 5%). The patterns show that the obtained films are crystalline and exhibited diffraction peaks at 27.5[degrees], 41.3[degrees], 44.1[degrees], and 54.4[degrees], corresponding, respectively, to (110), (111), (210), and (211) planes of rutile Ti[O.sub.2] phase. The planes of anatase (101), (112), (200), and (211) are localized at 25.3[degrees], 38.6[degrees], 48.1[degrees], and 55.1[degrees], respectively. Safeen et al. [16] and Majeed et al. [17] found that the Ti[O.sub.2] films have grown in amorphous phase. This is attributed to low-surface mobility of deposition particles, and hence, the deposition particles do not possess enough energy to crystallize [18]. Safeen et al. found a semicrystalline phase at higher substrate temperatures ([greater than or equal to]300[degrees]C) [16]. Majeed et al. [17] found that when a negative bias is applied to the substrate, it can lead to an increase in the energy of the surface atoms resulting in an enhanced surface diffusion, which can cause better adhesion, nucleation, and crystal structure. When the substrate is biased, more energy is transferred from ions driven by the substrate bias to the growing film, which can make the film more compact [19]. Nevertheless, in this work, the substrate was not heated but was biased at -20 V, enough to make the film crystallized (Figure 1).

Highest diffraction peak intensity indicates that rutile (111) is the preferential orientation from the broadening of diffraction peaks; the grain size was estimated using the Scherrer formula [20]: D = (K x [lambda])/[beta] cos [theta], where K = 0.89, [lambda] is the wavelength of X-ray, [theta] is the diffraction angle, and [beta] is the corrected half width. The grain size of the Ti[O.sub.2] thin films decreases from 16.2 to 6.7 nm as the oxygen flow rate decreases from 30 to 5% (Table 2). These results corresponded to the result of Safeen et al. [16] who deposited Ti[O.sub.2] films by radio-frequency magnetron sputtering, and they found that the grain size of the film prepared in 10% [O.sub.2] was smaller than the film grown in 20% [O.sub.2]. Also, similar result was reported by Zhao et al. [21] and Dannenberg and Greene [22]; they related this results to the oxygen atoms which are reflected from the target and hit the substrate with appreciable energy, thereby causing nucleation [21, 22]. However, Zhao et al. [21] have noticed that too much oxygen will decrease the presence of Ti atoms in the vapor phase, thereby hindering nucleation and the films become amorphous.

3.2. FTIR Spectra. Figure 2 shows the Fourier transform infrared (FTIR) spectra of the Ti[O.sub.2] coatings deposited under different flux rate of oxygen in range of 4000-400 [cm.sup.-1]. According to Chandra Sekhar et al. [23], the presence of absorption bands indicates that the Ti[O.sub.2] are crystalline for all conditions. It can be seen that the coatings exhibited broad and strong absorption peaks located in the range of 400 to 1000 [cm.sup.-1], which corresponded to stretching vibration of Ti-O and Ti-O-Ti bonds [13, 24-27]. The strong absorption bands at 1092 [cm.sup.-1] are attributed to the vibration of stretching and deformation of Si-O-Si bond stemming from the glass substrate [23].

3.3. Mechanical Properties. Figure 3 gives the variation of the hardness (Hi) and elastic modulus (Ei) values of Ti[O.sub.2] coatings. The results were given in Figure 5. The application of a negative bias to the substrate leads to an increase of the hardness and the elastic modulus. The maximum hardness and Young s modulus of H = 11.3 GPa and E = 84.3 GPa are obtained for a coating deposited under lower flux rate of oxygen. When the rate of oxygen increases the hardness decreases to lowest hardness of 6 GPa and lowest Young's modulus of 62 GPa. This result could be related to the same evolution of the grain size. Two other parameters are commonly used to evaluate the resistance to contact damage; they are expressed by two ratios: H/E and [H.sup.3]/[E.sup.2] [28,29], The higher ratios of H/E or [H.sup.3]/[E.sup.2] mean higher elastic and high resistance of coatings to plastic deformation and hence a higher wear resistance with low rigidity. The H/E is an indicator of film durability and is related to the elastic strain to failure capability (and resilience) in a surface contact, which is clearly important for the avoidance of wear [30]. The ratio [H.sup.3]/[E.sup.2] is commonly used to evaluate the resistance to plastic deformation during wear or abrasion [28, 30].

Figure 4 shows the ratios H/E and [H.sup.3] /[E.sup.2] for the various Ti[O.sub.2] deposited under different flux rate of oxygen. It shows that all of the Ti[O.sub.2] films present higher [H.sup.3]/[E.sup.2], which indicates that Ti[O.sub.2] films were characterized by good resistance to plastic deformation due to [H.sup.3]/[E.sup.2] > 0.1 [30]. It is clear that the largest resistance to plastic deformation (i.e., maximum H/E and [H.sup.3]/[E.sup.2]) of values 0.13 and 0.2 GPa is found for sample deposited under lower flux rate of oxygen (5% [O.sub.2]).

3.4. Electrochemical Polarization Analyses. Before each polarization test, the samples were immersed in aerated NaCl 3.5% at 25[degrees]C for a period of time for the OCP to stabilize. Figure 5 clearly shows that the presence of Ti[O.sub.2] coatings on the metal surface in NaCl solution shifts both the anodic and cathodic branches of the Tafel plots to lower values of current density. This suggests that the modified Ti[O.sub.2] coatings clearly retard the anodic dissolution process of stainless steel and increase its anticorrosion properties.

The electrochemical kinetic parameters in the polarization curves, such as the corrosion potential [E.sub.corr], corrosion current density [i.sub.corr], polarization resistance (Rp), corrosion rate ([C.sub.r]), porosity (P), and the anodic and cathodic Tafel slopes ([beta]a and [beta]c) are listed in Table 1. It reveals from Table 3 that the corrosion current density [i.sub.corr] was reduced in the presence of Ti[O.sub.2]. Additionally, as shown in Table 3, [E.sub.corr] values in the presence of the Ti[O.sub.2] coatings were less negative than that in the absence of the Ti[O.sub.2] coatings. On the other hand, the slight shifts of [E.sub.corr] values towards positive direction are found with the increase of oxygen partial pressure [O.sub.2].

The pitting corrosion which occurs mainly depends on the concentration of Cl ions on the electrode surface. When the coatings are immersed in the solution rich in Cl ions, Cl ions absorb and concentrate on the surfaces of the specimens. The metal is dissolved into the solute because of the replacement of oxygen ions in the oxides of the coating by Cl ions. This condition induces the pitting. With the process of pitting reactions, a microgalvanic cell is gradually formed between the bared substrate in the pitting spot and the coating around the pitting spot, in which the former and the latter can be regarded as the anode and the cathode, respectively. This process will further accelerate the concentration of Cl ions in the pitting spot [31]. Dense coating provides very low permeability for electrolytes to establish an ionic conduct. The decrease in current density can be ascribed to the compact surface structure [32] and improved adhesion after decrease in oxygen partial pressure; at a lower oxygen flow rate, the nature of the substrate and oxygen flow can be an important factor influencing the quality of the coating [33], thereby reducing solution penetration and consequent localized corrosion. According to the corrosion surface, it was concluded that, after immersion for a period, the failure of the coatings could be ascribed to the micropores in the surface of coatings [34].

In our work, the current density of Ti[O.sub.2] in 3.5% NaCl solution is (5.247 nA x [cm.sup.-2]) much lower than both values obtained for nearly the same electrochemical conditions [35, 36], deposited by atomic layer deposition. Supplementary, the coating's protective efficiency (Pe) was determined from the polarization curve using the following equation:

Pe = [1 - ([i.sub.corr,film]/[i.sub.corr,substrate])] X l00, where [i.sub.corr,film] and [1.sub.corr,substrate] are the corrosion current densities of the coating and substrate in that order [12]. The results show that all the films work as corrosion protective coatings on stainless steel and each coating gives protection efficiency near or greater than 99% for all conditions. This result could be related to the grain size (Table 2); the film exhibiting the lowest grain size gives a high protective efficiency and a good hardness.

4. Conclusion

Ti[O.sub.2] coatings have been successfully deposited on steel substrates by rf reactive magnetron sputtering a metallic target of titanium in an argon/oxygen atmosphere without heating. The X-ray diffraction results show that the coatings are crystalline. These coatings improve the corrosion resistance of stainless steel in NaCl solution with 3.5% Wt, but the protective properties of the coatings depend on the oxygen partial pressure. A Ti[O.sub.2] coating with lower oxygen partial pressure showed the best protective properties. The best corrosion resistance was found for stainless steel at 5% of oxygen partial pressure. The effective protection against corrosion is near 99% for all samples.

https://doi.org/10.1155/2017/4926543

Conflicts of Interest

The authors declare that they have no conflicts of interest.

Acknowledgments

This research was financially supported by Grant of the National Funding of Research (FNR) (Ministere de l'Enseignement Superieur de la Recherche Scientifique, Algerie).

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N. Madaoui, (1) L. Bait, (1) K. Kheyar, (2) and N. Saoula (1)

(1) Division Milieux Ionises et Lasers, Centre de Developpement des Technologies Avancees (CDTA), Cite du 20 Aout 1956, Baba Hassen, BP no. 17, Alger, Algeria

(2) Faculte de Physique Universite Des Sciences et de la Technologie Houari Boumediene, BP 32, El Alia, Bab Ezzouar, 16111 Alger, Algeria

Correspondence should be addressed to N. Saoula; nsaoula@yahoo.fr

Received 1 February 2017; Accepted 29 May 2017; Published 22 June 2017

Academic Editor: Fernando Lusquinos

Caption: Figure 1: XRD diffraction patterns of Ti[O.sub.2] films obtained for different oxygen flow rate (a: anatase, r: rutile, and Fe: iron).

Caption: Figure 2: FTIR spectra of Ti[O.sub.2] under different flow rate of oxygen.

Caption: Figure 3: Hardness and Young's modulus of Ti[O.sub.2] versus flux rate of oxygen.

Caption: Figure 4: Variation of H/E and [H.sup.3] /[E.sup.2] versus flux rate of oxygen.

Caption: Figure 5: Effect of oxygen flow on the polarization curves of the stainless steel coated and uncoated in 3.5% NaCl solution, obtained at 25[degrees] C.
Table 1: Sputtering conditions for the deposition of Ti[O.sub.2]
coatings.

Target                      Pure Ti metal ([PHI]76 x 5 mm) (99.95%)
Substrate                               Stainless steel
Target-substrate distance                     3 cm
Sputtering gas                                 Ar
Reactive sputtering gas                    [O.sub.2]
Flux rate of oxygen                    5,10, 20, and 30%
Sputtering gas pressure                     30 mTorr
Bias substrate                               -20 V
Deposition time                              60 min
Power sputtering                             200 W
Substrate temperature                      Not heated

Table 2: Grain size of rutile with (111) orientation at different
[O.sub.2] flow rate.

[O.sub.2]     Pos.          FWHM        D (nm)
(%)         (2[theta])    ([degrees])

30             40.14         0.091        16.2
20             40.14         0.120        12.3
10             40.10         0.112        13.2
5              40.10         0.221         6.7

Table 3: Electrochemical parameters obtained from the Tafel method
for stainless steel with and without coating of Ti[O.sub.2] (in the
operative conditions of the flow of oxygen) in 3.5% NaCl at
25[degrees]C.

Sample            [E.sub.corr]    [I.sub.corr]       Rp (M[OMEGA]
                      (mV)       (nA x [cm.sup.-2])  x [cm.sup.-2])

Stainless steel     -615.183           60709          0.000336301
  30%               -134.679           16.328            7.83
  20%               -188.135           17.69             5.777
  10%               -127.399           7.823            12.566
  5%                -187.274           5.247            17.508

Sample            [C.sub.r]    Porosity (%)    Pe (%)
                  (mm/year)

Stainless steel    35.01       1,091967969      --
  30%             0.0038309     9,128_E--06    99,97
  20%             0.0051917    8,03282E--06    99,97
  10%             0.0017132    2,83173_E--06   99,98
  5%              0.00093696   1,02758E--08    99,99
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Title Annotation:Research Article
Author:Madaoui, N.; Bait, L.; Kheyar, K.; Saoula, N.
Publication:Advances in Materials Science and Engineering
Date:Jan 1, 2017
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