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Article

Fabrication of Novel Chitosan–Hydroxyapatite Nanostructured Thin Films for Biomedical Applications

by
Carmen Steluta Ciobanu
1,
Simona Liliana Iconaru
1,
Daniela Predoi
1,
Roxana-Doina Trușcă
2,
Alina Mihaela Prodan
3,4,
Andreea Groza
5,
Mariana Carmen Chifiriuc
6,7,8 and
Mircea Beuran
3,4,*
1
National Institute of Materials Physics, Atomistilor Street, No. 405A, P.O. Box MG 07, 077125 Magurele, Romania
2
National Centre for Micro and Nanomaterials and National Centre for Food Safety, Faculty of Applied Chemistry and Materials Science, University POLITEHNICA of Bucharest, Splaiul Independentei 313, 060042 Bucharest, Romania
3
Emergency Hospital Floreasca Bucharest, 8 Calea Floresca, Sector 1, 014461 Bucharest, Romania
4
Department of Surgery, Carol Davila University of Medicine and Pharmacy, 8 Eroii Sanitari, Sector 5, 050474 Bucharest, Romania
5
National Institute for Laser, Plasma and Radiation Physics, 409 Atomistilor Street, P.O. Box MG 36, 077125 Magurele, Romania
6
Life, Environmental and Earth Sciences Division, Research Institute of the University of Bucharest (ICUB), University of Bucharest, 060023 Bucharest, Romania
7
Academy of Romanian Scientists, 54 Spl. Independentei St., District 5, 050085 Bucharest, Romania
8
Biological Sciences Division, The Romanian Academy, 25, Calea Victoriei, Sector 1, District 1, 010071 Bucharest, Romania
*
Author to whom correspondence should be addressed.
Coatings 2021, 11(12), 1561; https://doi.org/10.3390/coatings11121561
Submission received: 31 August 2021 / Revised: 30 September 2021 / Accepted: 17 December 2021 / Published: 19 December 2021
(This article belongs to the Special Issue Biomaterials and Antimicrobial Coatings)
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Abstract

:
In this study, we develop chitosan–hydroxyapatite (CS–HAp) composite layers that were deposited on Si substrates in radio frequency (RF) magnetron sputtering discharge in argon gas. The composition and structure of CS–HAp composite layers were investigated by analytical techniques, such as Fourier transform infrared spectroscopy (FT-IR), scanning electron microscopy (SEM), metallographic microscopy (MM), and atomic force microscopy (AFM). On the other hand, in the present study the second order derivative of FT-IR–ATR spectra, for compositional analyses of CS–HAp, were used. The SEM, MM, and AFM data have shown the formation of CS–HAp composite layers. The surface of CS–HAp composite layers showed uniform growth (at an Ar gas working pressure of p = 2 × 10−3 mbar). The surface of the CS–HAp composites coatings became more nanostructured, becoming granular as the gas pressure increased from 5 × 10−3 to 1.2 × 10−2 mbar. However, our studies revealed that the surface morphology of the CS–HAp composite layers varies with the Ar gas working pressure. At the same time, optical properties are slightly influenced by Ar pressure. Their unique physicochemical properties make them suitable for various applications in the biomedical field, if we consider the already proven antimicrobial properties of chitosan. The antifungal properties and the capacity of the CS–HAp composite layers to inhibit the development of fungal biofilms were also demonstrated using the Candida albicans ATCC 10231 (C. albicans) fungal strain.

1. Introduction

Hybrid coatings based on hydroxyapatite are of interest in research areas such as biomedicine or biomedical applications [1,2,3]. Hydroxyapatite ((HAp), Ca10(PO4)6(OH)2) is a calcium phosphate mineral widely present in human body [4], bioactive and biocompatible, and with the ability to accelerate the regeneration process of bones. It is extensively used to cover metal implants in order to increase their bioactivity and bone formation and regeneration. As it has a Ca/P ratio similar to human bone, it can promote the formation of chemical bonds with the bone [4].
The biological properties, as well as the physicochemical ones, of HAp can be improved by it synthesis with chitosan [4,5,6]. Chitosan ((C6H11NO4)n) is a natural polysaccharide with biofunctionality, non-toxicity, and antibacterial and biocompatible properties, with medical applications for scaffolds or coatings [4,5,6,7]. Chitosan has a broad antimicrobial activity against bacteria and fungi, the efficiency depending on the microorganism type [8]. Chitosan acts against microbes at the extracellular level, intracellular level [8], or both. High-molecular-weight chitosan acts only at the extracellular level, while low-molecular-weight chitosan can also act at the intracellular level. Chitosan has antimicrobial action on both Gram-positive and Gram-negative bacteria [8].
The antifungal activity of chitosan against plant and human fungal pathogens has been proven to be attributed to its interaction with the cell wall and cell membranes [8,9,10], disrupting the cell structure or chelating ions or nutrients. Nevertheless, other methods that could be successfully used to treat bacterial contamination in various fields are represented by low-temperature plasma (LTP) physics, as previously reported [11,12,13,14,15,16].
The combination of hydroxyapatite with chitosan leads to an organic–inorganic composite material with improved biocompatibility and bone regeneration and antimicrobial properties [17,18,19,20]. By micro-arc oxidations chitosan–hydroxyapatite samples have been obtained with antimicrobial activity against Escherichia coli [9]. Scaffolds of mesoporous hydroxyapatite/chitosan produced by a hydrothermal method were helpful in periodontal regeneration and against periodontal pathogens [10]. Hybrid chitosan–hydroxyapatite (CS–HAp) coatings on different substrates were synthetized by: electrophoretic deposition [21], spin coating technique [22], plasma spraying [23], electrochemical deposition [21], or radio frequency magnetron sputtering discharges [24].
In [24,25], the synthesis of hydroxyapatite-based coatings on metal or dielectric substrates was reported, as well as hybrid chitosan–hydroxyapatite coatings produced by magnetron sputtering technique [24]. This technique can be used for the fabrication of composite, inorganic, or polymer layers [1,3,24,25]. The hydroxyapatite or hydroxyapatite-chitosan layers produced by this plasma method have good adhesion to the substrate, preserving the apatite structure of the sputtering target [24,25]. The addition of chitosan into the sputtering target conduces to the formation of surfaces with grain-like structures of variable sizes, from nanometers to microns. In our previous paper [24], we showed that the patterning of the surface of chitosan–hydroxyapatite coatings can be controlled by plasma deposition parameters.
The plasma polymers are of great interest for different biomedical applications [26], as their presence in a composite coating leads to the formation of nanoporous and nanostructured films. The physicochemical features of composite coatings generated by plasma-based methods cannot be reproduced by other chemical methods [26,27]. In the paper [9] it was proved that the microstructuring or nanostructuring of the surface topography of the prosthesis material interlayer promoted a better bone regeneration.
It is well known that one of the most implicated fungi in postoperative and nosocomial infections is Candida albicans [28]. Previous studies conducted by Iconaru S.L. and coworkers have shown that hydroxyapatite coatings deposited on various substrates do not protect from C. albicans colonization and biofilm development [29]. Therefore, we chose to use chitosan as proven large spectrum antimicrobial agent [30]. There have been many studies conducted on hydroxyapatite-chitosan composite powders/scaffolds [17,18,19,20] but only few on CS–HAp coatings (especially on the influence of the Ar gas working pressure on the physicochemical properties) [24]. Due to the lack of studies on the hydroxyapatite-chitosan coatings, we chose to conduct, for the first time, complex studies regarding the influence of Ar gas working pressure on the surface topography of novel CS–HAp coatings for biomedical application. Moreover, the use of these new coatings in applications such as implantology could improve host cells adhesion and simultaneously reduce the risk of microbial infection compared to hydroxyapatite-chitosan composite powders [24]. The present study attempted to obtain the CS–HAp composite layers and analyze their morphological and optical properties. The major objective of the present work is to use chitosan–hydroxyapatite as a starting material for the fabrication of CS–HAp composite layers by radio frequency (RF) magnetron sputtering discharge in argon gas. Thus, for obtaining the coatings, chitosan was selected as a biopolymer and an antimicrobial agent. The CS–HAp coatings were obtained by radio frequency magnetron sputtering at various argon (Ar) gas working pressures. The obtained composite coatings were investigated from the physicochemical point of view by Fourier transform infrared spectroscopy (FT-IR), scanning electron microscopy (SEM), atomic force microscopy (AFM), and metallographic microscopy (MM).

2. Materials and Methods

2.1. Materials

Chitosan-coated hydroxyapatite (CS–HAp) powders were obtained by an adapted coprecipitation method using Ca(NO3)2∙4H2O (calcium nitrate tetrahydrate, Sigma Aldrich, St. Louis, MO, USA, ≥99.0%), (NH4)2HPO4 (ammonium hydrogen phosphate, Sigma Aldrich, St. Louis, MO, USA, ≥99.0%), NH4OH (ammonium hydroxide, Sigma Aldrich, St. Louis, MO, USA, 25% NH3 in H2O), chitosan (Sigma Aldrich, St. Louis, MO, USA) polymer of low (CSL) molecular weight, CH3COOH (acetic acid, Sigma Aldrich, St. Louis, MO, USA, ≥99.7%) C2H5OH (ethanol absolute, Merck, NJ, USA, ≥99.5%), and deionized water. All products were used in synthesis without any further purification. Deionized water was used in order to prepare all of the reactive solutions.

2.2. Synthesis of Chitosan–Hydroxyapatite Composites and Deposited Layers

To synthesize the chitosan–hydroxyapatite composites (CS–HAp, Ca/P ratio was equal to 1.67), the chitosan solutions were obtained by dissolving 0.4 g of chitosan powder in acetic acid solution (2 wt.%). In the first step, the aqueous solution of Ca(NO3)2∙4H2O was mixed with chitosan solution in the ratio 3:2. In the second step, (NH4)2HPO4 solution was added drop by drop. The ammonium hydroxide solution was used to maintain the pH at 10. Further, the resulting precipitate was filtered and washed five times and finally dried at 150 °C to obtain CS–HAp composite powders. The CS–HAp composite powders were used to produce a target of 2 inches in diameter by mechanical pressing. The target was dried for 2 h at 150 °C.
The CS–HAp composite layers were obtained accordingly with previous studies [24]. The Ar working pressure and the name of the samples are presented in Table 1 [24]. The composite layers were deposited on Si substrates in radio frequency (RF) magnetron sputtering discharge in argon gas [31].

2.3. Characterization of CS–HAp Composite Layers

2.3.1. Fourier Transform Infrared Spectroscopy (FT-IR)

The functional groups presented in the synthesized CS–HAp coatings were identified using a Perkin Elmer SP-100 spectrometer (Waltham, MA, USA) operating in “attenuated total reflection” (ATR) mode. The transmittance spectra were acquired in the 400–4000 cm−1 spectral range and with a resolution of 4 cm−1 and 256 scans. The obtention of second derivative spectra is described in detail in [32]. The second derivative spectra were used, mainly to increase the separation of the overlapped bands and to better highlight the chemical links between hydroxyapatite and chitosan.

2.3.2. Scanning Electron Microscopy (SEM-EDX)

The surface morphology and elemental analysis of the obtained coatings were characterized using a Quanta Inspect F (Thermo Fisher, Waltham, MA, USA) equipped with an energy-dispersive X-ray spectrometer (EDAX). The 3D reconstruction of the 2D SEM micrographs was performed using Image J software (ImageJ 1.51j8, National Institutes of Health, Bethesda, MD, USA) [33].

2.3.3. Metallographic Microscopy

More information about the morphology of the CS–HAp coatings was obtained by metallographic microscopy. Metallographic images at 10× magnification were obtained with the aid of an inversed trinocular metallographic microscope OX.2153-PLM (Euromex, Arnhem, The Netherlands). The 3D representation of the 2D metallographic images was performed using Image J software (ImageJ 1.51j8, National Institutes of Health, Bethesda, MD, USA) [33].

2.3.4. Atomic Force Microscopy (AFM)

The surface topography of the obtained CS–HAp coatings was also studied by atomic force microscopy (AFM). A NT-MDT NTEGRA Probe Nano Laboratory instrument (NT-MDT, Moscow, Russia) operating in non-contact mode (at room temperature) using a silicon NT-MDT NSG01 cantilever (NT-MDT, Moscow, Russia) coated with a 35 nm gold layer was used in order to obtain the AFM images. The AFM topography was acquired on a surface area of 5 × 5 µm2. All of the obtained AFM images were processed with the Gwyddion 2.59 software (Department of Nanometrology, Czech Metrology Institute, Brno, Czech Republic) [34], and the root mean square roughness (RRMS) was also determined.

2.3.5. In Vitro Antifungal Activity

The qualitative antifungal activity of the obtained composite layers was evaluated determined using Candida albicans ATCC 10231 (C. albicans) fungal strain. For this purpose, 500 μL of microbial suspension of C. albicans, having ~5 × 106 colony forming units (CFU)/mL obtained from 24 h microbial cultures, was grown on the composite layers immersed in 4 mL culture medium (liquid yeast peptone glucose, YPG). After 24, 48, and 72 h, the composite thin films were removed from the culture medium, washed using sterile saline solution for the removal of unattached fungal cells, then fixed in cold methanol and prepared for scanning electron microscopy (SEM) and confocal laser scanning microscopy (CLSM) studies. For CLSM visualization, the specimens were stained before visualization for 5 min with ethidium bromide and visualized in reflection and fluorescence modes using a TCS SP confocal microscope (Leica, Wetzlar, Germany) equipped with a 10X HCX PL FLUORITE objective with a numerical aperture NA of 0.3. An Ar-ion laser (488 nm) was also used to simultaneously acquire both reflection and fluorescence images. The quantitative antifungal properties were determined with the aid of fungal suspensions of a known fungal density (~5 × 106 colony forming units (CFU)/mL) obtained from 24 h fungal cultures. The samples were incubated at 37 °C for 72 h with the fungal suspensions in order to evaluate the temporal dynamics of the fungal cells’ development after 24, 48, and 72 h. For this purpose, for each intended incubation time (24, 48, and 72 h) the microbial suspensions were collected and incubated for 24 h on LB agar medium. A free microbial suspension was used as positive control (C+). The number of colony forming units per milliliter (CFU/mL) was determined and presented graphically as LogCFU.ml function of time. The experiments were performed in triplicate, and the results were expressed as mean ± standard deviation (SD). The statistical analysis of the data was performed using ANOVA single factor test. Furthermore, a viable cell count (VCC) assay of the fungal cells was also performed in order to assess the viable fungal cells. For this purpose, the composite layers were added in a sterile saline solution inoculated with microbial suspensions having a ~5 × 106 CFU/mL concentration. The samples were incubated under stirring at 37 °C for 72 h. The number of viable fungal cells was determined using 10 µL of fungal suspension at 24, 48, and 72 h. For this purpose, the fungal suspensions were further diluted, and 10 µL of each serial dilution was plated in duplicate on LB agar. After 24 h of incubation at 37 °C, viable cell counts were performed, and the number of CFU/mL for each sample was evaluated.

3. Results and Discussions

The presence of functional groups in the obtained CS-HAp_1, CS-HAp_2, and CS-HAp_3 coatings was investigated using Fourier transform infrared spectroscopy (FT-IR). The results of FT-IR studies are presented in Figure 1a–c. In the obtained FT-IR spectra, there could be noticed the presence of the vibrational bands characteristic of the hydroxyapatite (HAp) structure (OH− and PO43− groups) as well as those specific to the chitosan structure (N–H, C–H, C–O, and C=O). Thus, because the Ar gas working pressure induced a slight displacement of the vibrational bands, below are presented only the results obtained for CS–HAp (p = 2 × 10−3 mbar), the other obtained FT-IR spectra being similar. Therefore, in the vibrational band present at around 3551 cm−1, two bands specific to OH vibration from HAp structure and to amine symmetric vibration from chitosan structure, respectively, are overlapping [24,35,36]. The main vibrational bands present in the 2800–2970 cm−1 spectral region were characteristic of CH stretching vibration [6,24,35,36]. The presence of ν3 CO32− vibrational groups in the samples was highlighted by the presence in the FT-IR spectra of a band at around 1461 cm−1 (Figure 1a–c). In addition, in the spectral region 400–1100 cm−1 could be noticed vibrational bands specific to phosphate groups (ν3, ν4, and ν1 (PO43−)) from HAp structure [35]. Thus, the peaks at around 1020 and 938 cm−1 are specific to ν3 (PO43−) and ν1 (PO43−), respectively (Figure 1a–c) [24]. Moreover, the presence of ν4 (PO43−) in the samples was demonstrated by the presence of peaks at around 558 and 674 cm−1 [24,32]. Furthermore, it can be observed that in the case of layers deposited at 2 × 10−3 mbar Ar gas working pressure, the peaks are slightly displaced and broadened compared to the peaks obtained in the case of samples obtained at 1 × 10−2 mbar Ar gas working pressure (Figure 1a–c). On the other hand, the FT-IR results confirmed the presence of bonds between the phosphate/hydroxyl groups specific to HAp structure and those characteristic of chitosan (amine, etc.) (Figure 1a–c).
It is well known that second derivative spectra can bring valuable information regarding the change in structure of studied samples. Therefore, for a better observation of overlapped bands, the second derivative spectra (in the 450–1100 cm−1 and 1300–3000 cm−1 spectral regions) of CS-HAp_1, CS-HAp_2, and CS-HAp_3 are presented in Figure 2. The second derivative spectra obtained between 450–1100 cm−1 (Figure 2a,c,e) clearly highlight the presence of the vibrational bands (at 450–700 cm−1 and 900–1100 cm−1) associated with ν4, ν1, and ν3 (PO43−) from HAp structure [32]. The bands present at around 1377, 1460, 2856, and 2956 cm−1 are attributed to C–H vibration from chitosan structure (Figure 2b,d,f) [35,36]. The bending vibration of ν NH2 observed around 1520 cm−1 belongs to that of a main group from the chitosan structure—glucosamide [6,35]. Other vibrational bands from 700–500 cm−1 and 1100–1000 cm−1, which could belong either to C–H/C–O bonds or to PO43−, may indicate the interaction bonds between HAp and chitosan [6,24,35,36]. Therefore, we notice that the increase in Ar gas working pressure from 2 × 10−3 mbar to 1.2 × 10−2 mbar induced a slight displacement of the vibrational bands present in the analyzed coatings.
Therefore, we can conclude that our results are in good agreement with the studies reported by Dreghici B.D. and colleagues [24].
Scanning electron microscopy (SEM) was used in order to study the influence of Ar gas working pressures on the surface morphology of CS–HAp coatings. The 2D SEM micrographs specific to the obtained CS–HAp coatings, along with their 3D representation, are presented in Figure 3. In the case of the CS–HAp coatings obtained at an Ar gas working pressure of p = 2 × 10−3 mbar, there could be noticed a smooth surface which showed a uniform growth (Figure 3a). Moreover, as the working gas pressure increased, it was observed that the surface of the coatings became more nanostructured, becoming granular. Therefore, at high pressures (p = 1.2 × 10−2 mbar), the surface morphology of the coatings is granular (Figure 3e). According to previous studies, these variations in the surface morphology of the coatings may be due to the polymerization process [24]. The 3D reconstruction of SEM images revealed the increase of granular structure with the increase of Ar gas working pressure (Figure 3b,d,f). Moreover, SEM micrographs do not show the presence of fractures, cracks, or other discontinuities on the surface of the analyzed samples.
The chemical composition of CS–HAp coatings was investigated by EDX studies. Also, elemental mapping of the coatings’ surfaces was recorded. The results of EDX studies along with the specific elemental mapping are revealed in Figure 4, Figure 5 and Figure 6. In all the studied samples in the obtained EDX spectra, the following main chemical elements are present: carbon, nitrogen, oxygen, phosphorous, and calcium. All these elements are characteristic of the CS–HAp coatings. The Si line from the EDX spectra is produced by the substrate on which the coatings were deposited. On the other hand, the elemental mapping revealed the uniform and homogeneous distribution of Ca, P, O, N, and C on the samples. Furthermore, no additional chemical elements could be noticed in the EDX spectra, which suggests purity of the analyzed samples. It could be observed that the Ar gas working pressure slightly influenced the chemical composition of the analyzed samples.
The characteristic 2D metallographic microscopy images and their 3D reconstruction of the CS–HAp coatings are depicted in the metallographic Figure 7. By this technique, complementary information is obtained about the surface topography of the CS–HAp coatings. As well as SEM studies, the information obtained by metallographic microscopy (at 10× magnification) is similar. Thus, the absence of cracks, fissures, or other defects is also confirmed by metallographic microscopy images. Moreover, the change of the surface morphology is confirmed with the increase in working gas pressure. Thus, it is observed that in the case of the coatings obtained at a low pressure (p = 2 × 10−3 mbar, Figure 7a) the surface morphology is uniform and smooth, while in the case of coatings obtained at higher pressures a structuring of the surface is observed. Thus, in the case of the coatings obtained at p = 5 × 10−3 mbar (Figure 7c) and p = 1.2 × 10−2 mbar (Figure 7e), a granular morphology of the surface is observed, which increases with the increase of the gas (Ar) working pressure. The 3D representations of metallographic microscopy images underline the surface coating modification (from smooth to granular) with the increase in working gas (Ar) pressure and, on the other hand, their uniformity and continuity.
Additional information regarding the surface topography of the CS–HAp coatings obtained at various Ar gas working pressures (p = 2 × 10−3 mbar; p = 5 × 10−3 mbar; p = 1.2 × 10−2 mbar) was obtained by AFM investigation. Specific AFM topographies of the CS–HAp coatings are presented in Figure 8. Thus, for the CS–HAp coatings obtained at a p = 2 × 10−3 mbar, the AFM images show that they possess a smooth surface morphology (Figure 8a,b). A granular surface morphology was noticed in the case of the coatings deposited at higher Ar gas working pressures (p = 5 × 10−3 mbar and p = 1.2 × 10−2 mbar). An increase of granular structured could also be observed. On the other hand, the 3D representation of AFM topographies emphasizes similar modification, as previously noticed in the 2D representation.
On the other hand, the root mean square roughness (RRMS) values obtained for the analyzed samples are presented in Table 2. The obtained RRMS values confirm the results obtained by visual investigation of the samples surface regarding the increase in granular morphology (and, consequently, the surface roughness) as the working gas pressure increases. Therefore, it could be underlined that the results obtained by AFM studies are in good agreement with the results obtained by the complementary methods, such as SEM and metallographic microscopy. Thus, our results support and are in good agreement with the results previously reported by Dreghici D.B. et al. [24] on the surface morphology of hydroxyapatite–chitosan composite coatings.
Qualitative assays regarding the adhesion and development of fungal cells on the surface of CS–HAp coatings were undertaken using SEM studies. The development of C. albicans microbial cells on the surface of the CS–HAp layers obtained at various Ar gas working pressures (p = 2 × 10−3 mbarr; p = 5 × 10−3 mbarr; p = 1.2 × 10−2 mbarr) were investigated at three different time intervals by SEM visualization. The images obtained by SEM visualization of the C. albicans microbial cells adhered on the surface of CS–HAp coatings after 24, 48, and 72 h of incubation are depicted in Figure 9. The SEM visualization in the case of the CS–HAp coatings incubated for 24, 48, and 72 h with C. albicans ATCC 10231 highlighted that the morphology of the fungal cells adhered on the surface of CS–HAp coatings was characteristic of the C. albicans fungal strain, having an ovaloid “yeast” shape and sizes ranging from 2.5 to 4.8 µm. The SEM images also reflect that the CS–HAp coatings presented a good inhibitory effect against the development of C. albicans fungal cells at all tested time intervals. The SEM images indicated that a better antimicrobial activity was observed in the case of CS–HAp coatings obtained at an Ar gas working pressure of p = 1.2 × 10−2 mbarr for all tested time intervals. The SEM images accentuated that, for all of the time intervals, the CS–HAp coatings obtained at various Ar gas working pressures (p = 2 × 10−3 mbarr; p = 5 × 10−3 mbarr; p = 1.2 × 10−2 mbarr) had a strong inhibitory effect on the adherence and development of the C. albicans fungal cells. Nonetheless, a more substantial antibacterial activity of the CS–HAp coatings was identified after 72 h of incubation. Moreover, the data suggested that the CS-HAp_3 coatings were more effective in inhibiting cell adherence of C. albicans compared to CS-HAp_1 and CS-HAp_2 composite layers.
Furthermore, complementary information regarding the adhered fungal cells on the surface of CS–HAp composite layers was also obtained by CLSM visualization. The results of the CLSM studies are presented in Figure 10a–f. The results of the CLSM studies have emphasized that the fungal cells adhered on the surface of CS–HAp composite layers are sparsely distributed and do not present any major conglomerates, thus revealing that the composite layers were effective in inhibiting C. albicans biofilm formation. In addition, the CLSM images showed that the fungal cells attached to the CS–HAp coatings were distinctive to C. albicans fungal cell morphology, with sizes ranging from 2.37 to 4.72 µm and having ovaloid shape. The data obtained by CLSM studies also emphasized that the antifungal properties of the CS–HAp layers were influenced by both the incubation time and the samples. The results suggested that CS-HAp_3 composite layers were the most effective in inhibiting the cell development and adherence of the fungal cells. Furthermore, the CLSM visualization confirmed the SEM results and evidenced that the CS–HAp were effective in inhibiting C. albicans cell development on their surface and also were able to prevent fungal biofilm formation. In addition, the results have confirmed that after 72 h of incubation the number of fungal cells still adhered on the surface of CS–HAp coatings was diminished, almost to extinction in the case of the CS-HAp_3 sample. The results depicted by the qualitative antifungal assays suggested that these types of composite coatings could be of great interest in the future development of antifungal medical devices.
Quantitative assays regarding the antifungal activity of the CS–HAp composite layers were also performed. The effects of the CS–HAp layers on C. albicans fungal cells were investigated at three different time intervals of incubation time (24, 48, and 72 h). For this purpose, the three CS–HAp layers obtained at various Ar gas working pressures (p = 2 × 10−3 mbarr; p = 5 × 10−3 mbarr; p = 1.2 × 10−2 mbarr) were incubated with the microbial suspensions, and the number of CFU/mL was determined for each of the contacts after 24, 48, and 72 h. The results of the in vitro antifungal assays demonstrated that all the CS–HAp coatings exhibited a strong inhibitory effect against the development of the tested microbial cells, even after 24 h of incubation, compared to the positive control (C+). Moreover, the results depicted in Figure 11 also suggested that the inhibitory effect of the samples increased with the incubation time and that the CS-HAp_3 coatings exhibited the strongest inhibitory effect against C. albicans fungal cells for all tested intervals.
In addition, a viable cell count (VCC) assay was performed to confirm the qualitative and quantitative investigations. The results of the VCC assay depicted in Figure 12 revealed a significant decrease in viable cells after 24 h of incubation with the CS–HAp composite layers. The number of VCCs was assessed only after 24 h of incubation, because after 48 and 72 h no viable cell counts could be recovered from the tested materials. Moreover, the VCC assay confirmed the results of the SEM and CLSM studies, and that emphasized that the layers did not allow C. albicans biofilm formation.
These results are also in good agreement with the qualitative antifungal assays, demonstrating that the CS-HAp_3 coatings presented a stronger inhibitory effect against C. albicans fungal cells. Furthermore, the SEM visualization has shown that the CS–HAp coatings obtained at various Ar gas working pressures (p = 2 × 10−3 mbarr; p = 5 × 10−3 mbarr; p = 1.2 × 10−2 mbarr) have successfully inhibited C. albicans cell proliferation, even after 24 h of incubation. Moreover, the SEM and CLSM images emphasized that on the surface of the coatings exposed to C. albicans microbial suspensions the remaining adhered microbial cells were isolated. In addition, both SEM and CLSM studies revealed that there was no indication of hyphal formation, which is a proof of inhibition of the first steps in biofilm formation. These results are in good agreement with previous reported studies regarding the antimicrobial properties of chitosan and chitosan/hydroxyapatite compounds [8,9,11,12,37,38,39,40,41,42,43,44]. Even though there have been many proposals of antimicrobial mechanisms in the literature, their understanding is still scarce. In terms of chitosan antimicrobial activity, several mechanisms of interaction between chitosan and microbial cells have been proposed. Firstly, one of the most well-known and accepted mechanisms is one based on the interaction between the positive charge surface of the studied materials and anionic components from the microbial strain structure (such as lipopolysaccharides and proteins), which leads to disruption and subsequent death of microbial cells [45,46]. Secondly, another proposed mechanism is based on the interaction between cytoplasmic membrane and chitosan, the latter modifying cell permeability and thus altering the transport of nutrients in the microbial cell, which finally leads to cell death due to lack of essential nutrients for the cell [45,46]. Another mechanism, less common, proposes intracellular targets of chitosan after penetrating the microbial cell wall and cytoplasmic membrane. This mechanism is based on the chitosan interaction with DNA, which ultimately leads to cell death due to the prevention of DNA replication and transcription [46]. Finally, another mechanism proposed in few studies is based on the chelating properties of metal ions by chitosan [46]. In addition, the antimicrobial properties of materials are also correlated with numerous factors, such as the type of microbial cell, the type of antimicrobial agent (powders, dispersion, nanoparticles, coatings, etc.), and other parameters that could influence the interaction between the microbial cell and the studied material, such as ambient temperature, pH value, etc. In addition, a considerable factor in antimicrobial properties, in the case of coatings, is the synergistic interactions that appear between the substrate and the coating, which could improve or generate new properties of the materials and/or substrate [47]. In our study, since hydroxyapatite was reported not to exhibit antifungal activity, the antifungal activity presented by the CS–HAp composite layers could be attributed to the chitosan or to the synergistic interaction that took place between the substrate and coating material. Nonetheless, these preliminary findings could lead to the premise that the CS–HAp coatings obtained at various Ar gas working pressures (p = 2 × 10−3 mbarr; p = 5 × 10−3 mbarr; p = 1.2 × 10−2 mbarr) might be suitable for the development of novel antimicrobial agents.

4. Conclusions

CS–HAp composite layers deposited on Si substrates were developed in radio frequency (RF) magnetron sputtering discharge in argon gas. The important infrared bands allowed us to highlight the presence of CS and HAp in the deposited layers. Moreover, the analysis of CS–HAp layers was performed using second-order derivative spectra. Investigation of CS–HAp layers by SEM, MM, and AFM showed that they have a homogeneous surface. No cracks or discontinuities were observed on the surface of the coatings. SEM, MM, and AFM investigations have shown that the surface of CS–HAp composite layers is influenced by argon (Ar) gas working pressure. If at the lowest pressure (2 × 10−3 mbar) a uniform increase was observed, at the highest pressure (1.2 × 10−2 mbar) a granular surface was observed, while at the pressure of (5 × 10−3 mbar) the surface was well structured. The antifungal assay emphasized that the CS–HAp composite layers inhibited C. albicans biofilm formation and also had a goof inhibitory effect against the development of C. albicans fungal cells. Therefore, due to their unique physicochemical properties highlighted in our paper, the hydroxyapatite–chitosan composite coatings could be a suitable candidate for biomedical applications.

Author Contributions

Conceptualization, M.B., C.S.C. and D.P.; methodology, M.B., C.S.C., and D.P.; software, S.L.I. and C.S.C.; validation, M.B., C.S.C., S.L.I. and D.P.; formal analysis, M.B., C.S.C., S.L.I., D.P., A.M.P. and A.G.; investigation, A.M.P., R.-D.T., M.C.C. and A.G.; resources, M.B. and D.P.; data curation, M.B., C.S.C., D.P., and S.L.I.; writing—original draft preparation, M.B., C.S.C., S.L.I., D.P. and A.G.; writing—review and editing, M.B., C.S.C., S.L.I. and D.P.; visualization, M.B., C.S.C., S.L.I., D.P., R.-D.T., A.M.P., M.C.C. and A.G.; supervision, M.B., C.S.C. and D.P.; project administration, M.B. and C.S.C.; funding acquisition, M.B. and D.P. All authors have read and agreed to the published version of the manuscript.

Funding

This research was funded by the Romanian Ministry of Research and Innovation with the grant number PN-III-P1-1.2-PCCDI-2017-0629/contract No. 43PCCDI/2018 and grant number PN-III-P2-2.1-PED2019-0868/contract No. 467PED/2020, and the APC was funded by the Romanian Ministry of Research and Innovation project number PN-III-P1-1.2-PCCDI-2017-0629/contract No. 43PCCDI/2018 and grant number PN-III-P2-2.1-PED-2019-1375/contract No. 331PED/2020”.

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

Data is contained within the article.

Conflicts of Interest

The authors declare no conflict of interest.

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Coatings 11 01561 g001 550
Figure 1. FT-IR spectra of CS–HAp coatings at: (a) p = 2 × 10−3 mbar; (b) p = 5 × 10−3 mbar; (c) p = 1.2 × 10−2 mbar.
Figure 1. FT-IR spectra of CS–HAp coatings at: (a) p = 2 × 10−3 mbar; (b) p = 5 × 10−3 mbar; (c) p = 1.2 × 10−2 mbar.
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Figure 2. Second derivative spectra of CS–HAp coatings obtained at: p = 2 × 10−3 mbar (a,b); p = 5 × 10−3 mbar (c,d); p = 1.2 × 10−2 mbar (e,f).
Figure 2. Second derivative spectra of CS–HAp coatings obtained at: p = 2 × 10−3 mbar (a,b); p = 5 × 10−3 mbar (c,d); p = 1.2 × 10−2 mbar (e,f).
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Figure 3. 2D SEM micrograph of CS–HAp coatings obtained at: p = 2 × 10−3 mbar (a); p = 5 × 10−3 mbar (c); p = 1.2 × 10−2 mbar (e). 3D representation of SEM images obtained on CS–HAp coatings: p = 2 × 10−3 mbar (b); p = 5 × 10−3 mbar (d); p = 1.2 × 10−2 mbar (f).
Figure 3. 2D SEM micrograph of CS–HAp coatings obtained at: p = 2 × 10−3 mbar (a); p = 5 × 10−3 mbar (c); p = 1.2 × 10−2 mbar (e). 3D representation of SEM images obtained on CS–HAp coatings: p = 2 × 10−3 mbar (b); p = 5 × 10−3 mbar (d); p = 1.2 × 10−2 mbar (f).
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Figure 4. Elemental mapping and typical EDX spectrum of CS–HAp coatings obtained at p = 1.2 × 10−2 mbar.
Figure 4. Elemental mapping and typical EDX spectrum of CS–HAp coatings obtained at p = 1.2 × 10−2 mbar.
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Figure 5. Elemental mapping and typical EDX spectrum of CS–HAp coatings obtained at p = 5 × 10−3 mbar.
Figure 5. Elemental mapping and typical EDX spectrum of CS–HAp coatings obtained at p = 5 × 10−3 mbar.
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Figure 6. Elemental mapping and typical EDX spectrum of CS–HAp coatings obtained at p = 2 × 10−3 mbar.
Figure 6. Elemental mapping and typical EDX spectrum of CS–HAp coatings obtained at p = 2 × 10−3 mbar.
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Figure 7. 2D Metallographic images (at 10× magnification) of CS–HAp coatings obtained at: p = 2 × 10−3 mbar (a); p = 5 × 10−3 mbar (c); p = 1.2 × 10−2 mbar (e). 3D representation of metallographic images obtained on CS–HAp coatings: p = 2 × 10−3 mbar (b); p = 5 × 10−3 mbar (d); p = 1.2 × 10−2 mbar (f).
Figure 7. 2D Metallographic images (at 10× magnification) of CS–HAp coatings obtained at: p = 2 × 10−3 mbar (a); p = 5 × 10−3 mbar (c); p = 1.2 × 10−2 mbar (e). 3D representation of metallographic images obtained on CS–HAp coatings: p = 2 × 10−3 mbar (b); p = 5 × 10−3 mbar (d); p = 1.2 × 10−2 mbar (f).
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Figure 8. 2D AFM topography of CS–HAp coatings obtained at: p = 2 × 10−3 mbar (a); p = 5 × 10−3 mbar (c); p = 1.2 × 10−2 mbar (e). 3D representation of AFM topography obtained on CS–HAp coatings: p = 2 × 10−3 mbar (b); p = 5 × 10−3 mbar (d); p = 1.2 × 10−2 mbar (f).
Figure 8. 2D AFM topography of CS–HAp coatings obtained at: p = 2 × 10−3 mbar (a); p = 5 × 10−3 mbar (c); p = 1.2 × 10−2 mbar (e). 3D representation of AFM topography obtained on CS–HAp coatings: p = 2 × 10−3 mbar (b); p = 5 × 10−3 mbar (d); p = 1.2 × 10−2 mbar (f).
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Figure 9. SEM images of Candida albicans ATCC 10231 cell development on the surface of CS-HAp_1 (a–c), CS-HAp_2 (d–f), and CS-HAp_3 (g–i) after 24 h (a,d,g), 48 h (b,e,h), and 72 h (c,f,i) of incubation.
Figure 9. SEM images of Candida albicans ATCC 10231 cell development on the surface of CS-HAp_1 (a–c), CS-HAp_2 (d–f), and CS-HAp_3 (g–i) after 24 h (a,d,g), 48 h (b,e,h), and 72 h (c,f,i) of incubation.
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Figure 10. CLSM images of Candida albicans ATCC 10231 cell development on the surface of CS-HAp_1 (a–c), CS-HAp_2 (d–f), and CS-HAp_3 (g–i) after 24 h (a,d,g), 48 h (b,e,h), and 72 h (c,f,i) of incubation.
Figure 10. CLSM images of Candida albicans ATCC 10231 cell development on the surface of CS-HAp_1 (a–c), CS-HAp_2 (d–f), and CS-HAp_3 (g–i) after 24 h (a,d,g), 48 h (b,e,h), and 72 h (c,f,i) of incubation.
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Figure 11. Antimicrobial activity of CS–HAp layers against Candida albicans ATCC 10231 at different time intervals. The results are presented as mean ± SD. Statistical analysis was performed by one-way ANOVA. The p-values indicated are the following: * p ≤ 0.003, ** p ≤ 0.0001.
Figure 11. Antimicrobial activity of CS–HAp layers against Candida albicans ATCC 10231 at different time intervals. The results are presented as mean ± SD. Statistical analysis was performed by one-way ANOVA. The p-values indicated are the following: * p ≤ 0.003, ** p ≤ 0.0001.
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Figure 12. Viable cell count assay of C. albicans fungal strain incubated with CS–HAp composite layers.
Figure 12. Viable cell count assay of C. albicans fungal strain incubated with CS–HAp composite layers.
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Table
Table 1. Ar working pressure and the associated name of the obtained coatings.
Table 1. Ar working pressure and the associated name of the obtained coatings.
Ar Gas Working Pressure (mbar)Sample Name
2 × 10−3CS-HAp_1
5 × 10−3CS-HAp_2
1.2 × 10−2CS-HAp_3
Table
Table 2. Root mean square roughness (RRMS) values for the CS–HAp coatings.
Table 2. Root mean square roughness (RRMS) values for the CS–HAp coatings.
SampleAr Gas Working PressureRRMS
CS-HAp_12 × 10−3 mbar0.112 nm
CS-HAp_25 × 10−3 mbar1.797 nm
CS-HAp_31.2 × 10−2 mbar6.051 nm
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Ciobanu, C.S.; Iconaru, S.L.; Predoi, D.; Trușcă, R.-D.; Prodan, A.M.; Groza, A.; Chifiriuc, M.C.; Beuran, M. Fabrication of Novel Chitosan–Hydroxyapatite Nanostructured Thin Films for Biomedical Applications. Coatings 2021, 11, 1561. https://doi.org/10.3390/coatings11121561

AMA Style

Ciobanu CS, Iconaru SL, Predoi D, Trușcă R-D, Prodan AM, Groza A, Chifiriuc MC, Beuran M. Fabrication of Novel Chitosan–Hydroxyapatite Nanostructured Thin Films for Biomedical Applications. Coatings. 2021; 11(12):1561. https://doi.org/10.3390/coatings11121561

Chicago/Turabian Style

Ciobanu, Carmen Steluta, Simona Liliana Iconaru, Daniela Predoi, Roxana-Doina Trușcă, Alina Mihaela Prodan, Andreea Groza, Mariana Carmen Chifiriuc, and Mircea Beuran. 2021. "Fabrication of Novel Chitosan–Hydroxyapatite Nanostructured Thin Films for Biomedical Applications" Coatings 11, no. 12: 1561. https://doi.org/10.3390/coatings11121561

APA Style

Ciobanu, C. S., Iconaru, S. L., Predoi, D., Trușcă, R. -D., Prodan, A. M., Groza, A., Chifiriuc, M. C., & Beuran, M. (2021). Fabrication of Novel Chitosan–Hydroxyapatite Nanostructured Thin Films for Biomedical Applications. Coatings, 11(12), 1561. https://doi.org/10.3390/coatings11121561

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