Hydroxyapatite Thin Films of Marine Origin as Sustainable Candidates for Dental Implants

Novel biomaterials with promising bone regeneration potential, derived from rich, renewable, and cheap sources, are reported. Thus, thin films were synthesized from marine-derived (i.e., from fish bones and seashells) hydroxyapatite (MdHA) by pulsed laser deposition (PLD) technique. Besides the physical–chemical and mechanical investigations, the deposited thin films were also evaluated in vitro using dedicated cytocompatibility and antimicrobial assays. The morphological examination of MdHA films revealed the fabrication of rough surfaces, which were shown to favor good cell adhesion, and furthermore could foster the in-situ anchorage of implants. The strong hydrophilic behavior of the thin films was evidenced by contact angle (CA) measurements, with values in the range of 15–18°. The inferred bonding strength adherence values were superior (i.e., ~49 MPa) to the threshold established by ISO regulation for high-load implant coatings. After immersion in biological fluids, the growth of an apatite-based layer was noted, which indicated the good mineralization capacity of the MdHA films. All PLD films exhibited low cytotoxicity on osteoblast, fibroblast, and epithelial cells. Moreover, a persistent protective effect against bacterial and fungal colonization (i.e., 1- to 3-log reduction of E. coli, E. faecalis, and C. albicans growth) was demonstrated after 48 h of incubation, with respect to the Ti control. The good cytocompatibility and effective antimicrobial activity, along with the reduced fabrication costs from sustainable sources (available in large quantities), should, therefore, recommend the MdHA materials proposed herein as innovative and viable solutions for the development of novel coatings for metallic dental implants.


Introduction
The increase in life expectancy and the continuously ascending prevalence of bone injuries and diseases represent decisive triggers of the growing interest in devices dedicated to the dentistry and orthopedic domains. It is worth mentioning that the global implant market was evaluated in 2015 at USD 72,265 million, and is estimated to reach USD 116,300 million by 2022 [1].
Currently, implants made of titanium (Ti) or its alloys are most often used in the medical field due to some important properties, such as high corrosion resistance, low

Targets Preparation
The ground MdHA powders were next doped with 0.5 wt.% of Li 3 PO 4 , MgF 2 , and Ag. The mixed powders were pressed at~7 MPa for 2 min in a 20 mm diameter mold. The resulting cylindrical pellets (5 mm thickness) were sintered in an oven, in air, at 500 • C for 6 h. The as-obtained hard pellets were used as targets in the PLD experiments.
For an easy identification, in Table 1, the codes for all samples mentioned in the manuscript are summarized.

PLD Experiment
Unlike wet synthesis techniques, plasma-assisted methods offer numerous advantages, as follows: (i) a superior deposition process, (ii) stoichiometric removal of the material from the target in the deposited films, (iii) improved morpho-compositional uniformity, (iv) a low degree of porosity, (v) a reduced disposition of the synthesized films to crack or delaminate, (vi) operational safety, and (vii) low production costs. In the biomedical domain, for the manufacturing of CaP thin films for bone implant applications, one of the most used techniques is pulsed laser deposition (PLD) [30][31][32][33]. Due to the possibility of independent variation of a wide number of parameters (e.g., wavelength, laser fluence, pulse repetition rate, beam energy, target-substrate separation distance, gaseous atmosphere and substrate temperature), PLD is a versatile technique used to obtain thin layers with a great diversity of morphological, compositional and structural characteristics.
For the PLD experiments, a KrF* excimer laser source, model COMPex Pro205 (λ = 248 nm, τ FWHM ≤ 25 ns), was used. The experiments were performed in water vapor atmosphere with~50 Pa residual pressure. The laser beam was incident at 45 degrees on the target's surface. The target-to-substrate separation distance was 5 cm. The laser pulse energy was set at 360 mJ (which corresponded to a fluence of 3.5 J/cm 2 ), and was monitored by a Coherent system.
The ablated materials were transferred and collected onto medical grade Ti substrates and silicon wafers with dimensions of 10 × 10 × 0.2 and 10 × 10 × 0.4 mm 3 , respectively. Prior to introduction into the deposition chamber, to remove micro-impurities, the substrates were cleaned using a three-step protocol (in the order of acetone, ethyl alcohol, and deionized water, for~20 min/step [42]) with an ultrasonic bath (model Elmasonic X-tra 30H). The cleaned substrates were dried by means of a jet of synthetic air (5.0 purity).
During the deposition process, the targets were continuously rotated (with a frequency of 0.75 Hz) and translated along two orthogonal axes to avoid piercing or the formation of craters, which have a negative influence on the quality of the synthesized layer as they deflect the laser plasma. To ensure the films' uniformity, the exposure of a "fresh" surface to the action of each laser pulse was intended.
Using a PID-EXCEL controller, all substrates were maintained during the experiments at a constant temperature of 500 • C (heating and cooling rates of 20 and 10 • C/min, respectively).
Prior to the experiments, to eliminate the possibility of any contamination, a residual pressure of 10 −3 -10 −4 Pa was attained in the reaction chamber. In addition, to clean the micro-impurities from the target surfaces,~1500-2000 consecutive laser pulses were applied before each experiment. During this process, a screen-collector was positioned between the target and the substrate on the surface of which the ablated material condensed.
The number of laser pulses applied for the synthesis of each film was 5000, at a repetition rate of υ = 10 Hz.
After the deposition process, the fabricated thin films were submitted to thermal treatments (500 • C for 6 h), in ambient water vapors.

Physical-Chemical Characterization Methods of the Synthesized PLD Films
(a) The surface morphology of the MdHA thin films was investigated using a Gemini 500 field emission scanning electron microscope (Zeiss, Oberkochen, Germany). To determine the thickness of the synthesized thin films, Si (100) wafers were used. The reason for using Si substrates was both their flat surface and lack of any porosity. Moreover, they facilitate the preparation of samples for the cross-sectional microscopy as they can be easily cut according to a particular crystallographic direction.
(b) The chemical composition of the synthesized MdHA thin films was investigated using energy-dispersive X-ray spectroscopy (EDS). For these measurements, a Quatax EDS detector (Bruker, Billerica, MA, USA) attached to the Gemini 500 equipment was used. The elemental analyses were carried out in triplicate, in different, arbitrarily-selected areas of 200 × 140 µm 2 on the surface of the deposited layers. (c) The crystalline structures of the PLD targets and derived films were analyzed by X-ray diffraction (XRD), with CuK α radiation. The targets were investigated in Bragg-Brentano geometry using a Bruker D8 Advance diffractometer (Bruker AXS Advanced X-Ray Solutions GmbH, Karlsruhe, Germany) equipped with a high-efficiency LynxEye TM 1D detector. The thin films were analyzed in grazing incidence geometry (GIXRD) using a Rigaku SmartLab 3 kW equipment (Rigaku Corporation, Tokyo, Japan) set up in a parallel beam mode at an incidence angle (α) of 2 • . The XRD patterns of both the targets and the films were collected in the range of 2θ = 10-60 • .
(d) To highlight the presence of functional groups and their structural arrangement in the synthesized thin films, Fourier transform infra-red (FTIR) spectroscopy investigations were carried out with a PerkinElmer BX Spectrum-Pike system in attenuated total reflectance (ATR) mode, using a Pike-MIRacle ZnSe/diamond crystal attachment with a diameter of 0.18 cm. The measurements were performed on Ti substrates at RT, with a resolution of 4 cm −1 and 64 scans/experiment.
(e) Microscopic characteristics, in terms of the surface roughness and surface energy of materials, have a key role in determining wetting behavior. By contact angle (CA) measurements, the hydrophobic/hydrophilic characteristics of the synthesized films were investigated. Static CAs were measured with a drop shape analysis system, model DSA100 (Krüss GmbH, Hamburg, Germany). The samples were placed onto a flat platform under the tip of a blunt-ended, stainless steel needle (outer diameter of 0.5 mm). The needle was attached to a syringe pump controlled by the DSA3 ® PC software and used to drip precise volumes of liquid onto the test surface, for CA assessment. The volume and diameter of a single liquid droplet were~1-3 µL and~1-2 mm, respectively. For each individual sample, the analysis was performed on two different areas of the film's surface. For the CA measurements, the experimental profile of the droplet was fitted with a second-degree polynomial, or with the equation of the circle. Next, the slope of the tangent to the droplet at the point of intersection with the line separating the liquid-solid-vapor interface was inferred. The angle between the video camera and the sample plane was~2 • . All wettability tests were performed at RT, in duplicate. Based on the measured CA values, the value of the surface free energy (SFE) was assessed. Two standard liquids (i.e., water and diiodomethane) were used, for which the surface tension (γ water = 72.8 mN/m; γ diiodomethane = 50.8 mN/m), the dispersion component, and the polar (γ water d = 21.8 mN/m, γ water p = 51 mN/m, γ diiodomethane = 48.5 mN/m, and γ diiodomethane p = 2.3 mN/m) values were known. Using the inferred CA values, both the polar and dispersion parts of the synthesized films, as well as the total SFE, were estimated by applying the Owens-Wendt method [49].
(f) The bonding strength (tensile) at the interface between the biofunctional film and the substrate is considered to be of key importance for the fabrication of high-quality implants and the long-term functioning and stability of these medical devices [6] in situ. Consequently, it is included as quality factor in the ISO 13779-2/2018 [50], which regulates the fabrication of load-bearing implant coatings. The adherence of the synthesized MdHA thin films on Ti substrates was estimated by the pull-out method. For these tests, a DFD Instruments ® PAThandy MICRO AT101 (maximum pull force of 1 kN) adherence instrument, equipped with stainless steel test elements (dollies) with diameters of 0.28 cm, was used. The dollies were glued to the thin films' surface with a special E1100S single-part epoxy glue with a certified breaking strength of~85 MPa. The stub surface was polished first, then ultrasonically cleaned with acetone and ethanol and dried in a nitrogen flow. After gluing, the MdHA thin films were dried in an oven (130 • C for 1 h). Prior to the investigations, four quality tests to control the bonding adhesive strength were performed using uncoated Ti substrates. The value of the adhesive strength, measured at the stainless-steel test element-Ti control interface, was 63 ± 0.5 MPa. Each dolly was pulled out vertically using a calibrated hydraulic pump. The extraction force was gradually increased until detachment occurred. For each thin film, the measurements were performed in quadruplicate and were in accordance with the ASTM D4541 and ISO 4624 standards. The mechanical adherence strength was determined from the measured failure force value divided by the area of the detached film surface. Mean values and standard deviation (SD) were computed.

Preliminary In Vitro Testing of the PLD FILMS
(a) The degradation of the MdHA films, derived from biogenic resources, was tested in accordance with the recommendations of the ISO 10993-14/2009: "Biological evaluation of medical devices-Part 14: Identification and quantification of degradation products from ceramics". However, instead of the suggested Tris-HCl testing solution, the same medium as the one used for the further cytocompatibility tests was preferred-i.e., Dulbecco's modified eagle medium (DMEM, Thermo Fisher Scientific, Waltham, MA, USA) supplemented with 10% fetal bovine serum (FBS, Thermo Fisher Scientific, Waltham, MA, USA)-since it enables a more homogeneous assessment across various in vitro evaluation protocols. Furthermore, the degradation testing was performed under homeostatic temperature (37 • C), pH (7.4), and (humidified) atmosphere conditions (5% of CO 2 ). This is known to mitigate the medium evaporation and the necessity of its timely replacement/refreshing [51]. Sterile samples (obtained by dry-heating at 180 • C/1 h) were immersed in sealed vials with 0.5 mL of DMEM-FBS solution for 3, 7, and 28 days. After each time period, the samples were extracted, gently washed with distilled water, and then dried in an oven for 24 h at 37 • C. Each tested MdHA sample was weighted before and after the degradation testing with an analytical microbalance (Radwag, model MYA0.8/3.3Y, 1 µg readability). The mass variation in the MdHA thin films was thus evaluated and reported correspondingly as a mass loss or mass gain. Furthermore, the morphology changes of the thin film surfaces were inspected by scanning electron microscopy (SEM). All tests were performed in triplicate for each time interval.
(b) The apatite-forming ability of the MdHA thin films was evaluated in Kokubo's simulated body fluid (SBF) solution by complying with the instructions of the ISO 23317/2014: "Implants for surgery: In vitro evaluation for apatite-forming ability of implant materials" [52][53][54]. The SBF solution was prepared in our laboratory by dissolving the chemical reagents (Sigma Aldrich, St. Louis, MI, USA) in 1000 mL of deionized water, and we obtained the following ion concentrations ( (c) The cytocompatibility of the simple and doped FB and SS thin films was tested in accordance with the ISO 10993-5/2009: "Biological evaluation of medical devices-Part 5: Tests for in vitro cytotoxicity", on three cell lines. Thus, osteoblasts (G292) were used to test the osteogenic potential, whilst fibroblasts (NCTC L929) and epithelial (HeLa) cells were used to investigate their biocompatibility, according to the UNI EN ISO 10993 regulation for testing medical devices intended for human use [55]. In this respect, the use of epithelial cells was also important for the purpose of ensuring that the application range of these materials could be further extended to antimicrobial coatings for wound dressings and medical cloths. Osteoblasts were grown in McCoy s 5a + 2 mM glutamine + 10% fetal bovine serum (FBS), according to the ATCC guidelines. Epithelial and fibroblast cells were grown in DMEM medium and supplemented with 10% fetal bovine serum (Sigma-Aldrich) and 1% Pen/Strep (penicillin/streptomycin solution, 50 µg/mL, Sigma-Aldrich) for 24 h at 37 • C and 95% humidity with 5% CO 2 . All cells were seeded at a density of 2 × 10 4 cells/cm 2 in 24-well plates onto the coated samples, previously sterilized under UV light, for 1 h. Cells were washed with saline solution (Sigma-Aldrich) and trypsin (trypsin-EDTA 0.25%, Thermo Fisher Scientific, Waltham, MA, USA), then counted using trypan blue and a hemocytometer. The MdHA thin films were co-cultured with the cells (seeding density of 5 × 10 5 cells/well) for 24 h (37 • C, 95% humidity, 5% CO 2 ). density that could be read at 550 nm. The MTT test allowed us to evaluate the viability and proliferation of living cells in the culture in the presence of the synthesized MdHA thin films. Cells were incubated with MTT reagent for 4 h at 37 • C and 95% humidity with 5% CO 2 . After incubation, the formazan crystals were solubilized with sodium dodecyl phosphate-chlorohydric acid for 18 h at 37 • C and 95% humidity with 5% CO 2 . The absorbance was measured using Mulsiskan FC (Thermo Fisher Scientific) at λ = 570 nm.
(c2) LDH: the cytotoxicity of the materials was evaluated using the lactate dehydrogenase (LDH) cytotoxicity detection kit (Roche, Basel, Switzerland). LDH is an enzyme which is present in the cytoplasm of all living animal cells. In the case of cell death, LDH was released into the culture medium; thus, the number of dead cells was directly proportional to the LDH activity. The LDH activity was measured in the supernatant using a Mulsiskan FC instrument (Thermo Fisher Scientific) at λ = 490 nm, with a wavelength reference of λ = 600 nm. After 24 h of incubation, the cell morphology was evaluated using an Olympus IX73 inverted fluorescence microscope (λex/em 488 nm/515 nm and λex/em 570 nm/602 nm).
(c3) ALP: the effect of biomaterials on the secretion of alkaline phosphatase (ALP) was investigated on the G292 cell line. The detection and quantification of ALP were performed using a colorimetric enzymatic assay (Thermo Fisher Scientific, Cat. No. ALP TR11320). The G292 osteoblasts were grown on the surface of Ti, as well as simple and doped FB and SS coatings, for 48 h. The cell supernatant was removed, and the samples covered with cells were placed into a new 24-well plate for measurements of the ALP activity. Cells were incubated with 4-nitrophenylphosphate substrate buffer to initiate the conversion into 4-nitrophenoxide. The absorbance of the yellow-colored product p-nitrophenol produced in the reaction was proportional to the amount of ALP present in the samples, and it was read at 405 nm on a Mulsiskan FC spectrophotometer (Thermo Fisher Scientific). Epithelial cells co-cultured with simple and doped FB and SS thin films were fixed with methanol (20 min at 4 • C) and subjected to staining for DNA (DAPI, 1 µg/mL) and plasma membranes (Cell Mask Deep Red, 8 µg/mL).
(c4) Osteocalcin concentration was measured using the Human Osteocalcin ELISA kit (cat no. RAB1073), following the manufacturer's instructions, after 48 h of incubation of the osteoblasts with the tested materials.
(d) The investigation of the antimicrobial activity of simple and doped MdHA thin films was performed on standard microbial strains, i.e., Staphylococcus aureus (S. aureus, ATCC 25923), Enterococcus faecalis (E. faecalis, ATCC 29212), Escherichia coli (E. coli, ATCC 25922), Pseudomonas aeruginosa (P. aeruginosa, ATCC 27853), and Candida albicans (C. albicans, ATCC 26790). The simple and doped MdHA thin films, previously sterilized by UV exposure (30 min on each side), were put in contact with microbial suspensions with densities of 10 6 CFU/mL (colony-forming units) in a liquid medium that maintained bacterial viability, but did not allow for its development. After different time intervals, i.e., initially (T 0 ) and after 2, 4, 24, and 48 h, microbial viability was determined by performing serial dilutions and seeding on agar medium (i.e., Mueller-Hinton for bacteria and Saboraud for fungi) to calculate the number of CFUs after incubation for 18 h at 37 • C. All tests were performed in triplicate.

Statistical Analysis
All experiments were carried out in triplicate, in order for the statistical significance to be investigated. Data are shown as mean ± SD and were represented using GraphPad Prism software, version 9.4.1. The differences in biocompatibility measurements were calculated using the "Unpaired t-test". The results of the microbiology testing were analyzed using the one-way ANOVA test with post hoc Bonferroni correction. The statistical significance levels were * p ≤ 0.05, ** p ≤ 0.01, and *** p ≤ 0.001.

SEM
Top-view SEM morphologies of simple and doped FB and SS thin films are comparatively presented in Figure 1, at a magnification of 5000×. One can observe that the films consisted of matrices with rough and irregular morphologies, made up of spheroidal particles, known as droplets, with different size distributions. The origin of these droplets and their relationship with the targets' composition represent well-known characteristics of the PLD process [46]. Figure 1 shows that the density and diameters of the particles were much larger for the SS thin films in comparison to the FB ones. In the literature, it has been demonstrated that the random distribution and varied sizes of these particles determine a beneficial roughness for cell cultures by promoting the colonization of osteogenic cells in their microcavities, followed by their intense proliferation [56,57]. It is important to mention that no delamination phenomena or microcracks were observed in the synthesized films. culated using the "Unpaired t-test". The results of the microbiology testing were analyzed using the one-way ANOVA test with post hoc Bonferroni correction. The statistical significance levels were * p ≤ 0.05, ** p ≤ 0.01, and *** p ≤ 0.001.

SEM
Top-view SEM morphologies of simple and doped FB and SS thin films are comparatively presented in Figure 1, at a magnification of 5000×. One can observe that the films consisted of matrices with rough and irregular morphologies, made up of spheroidal particles, known as droplets, with different size distributions. The origin of these droplets and their relationship with the targets' composition represent well-known characteristics of the PLD process [46]. Figure 1 shows that the density and diameters of the particles were much larger for the SS thin films in comparison to the FB ones. In the literature, it has been demonstrated that the random distribution and varied sizes of these particles determine a beneficial roughness for cell cultures by promoting the colonization of osteogenic cells in their microcavities, followed by their intense proliferation [56,57]. It is important to mention that no delamination phenomena or microcracks were observed in the synthesized films. The cross-sectional SEM images ( Figure 1) showed, in all cases, uniform coverage with columnar growth. The coatings' thickness values (and, implicitly, the deposition rates) are presented in Table 2. The deposition rate can also be influenced by the density and crystallinity of the target [58]. It has also been demonstrated that the addition of different ions influences both the properties of the coatings and the deposition rates [59]. Thus, the thickness variations observed in the case of the synthesized structures can be attributed mainly to the nature of the pristine material, but also to the different ablation rates of Li, Mg, and Ag. In general, when using the PLD technique, pure metals have higher ablation rates [60], which can justify a slightly higher deposition rate in the case of FB:Ag structures in comparison to simple FB ones.

EDS
In addition to the main constituents normally found in the chemical composition of HA (e.g., Ca, P, O), the existence of some trace elements present in the composition of the mineral phase of healthy bone, such as Mg, Si, and S, which play an important role in its functionality, was also highlighted. The presence of light elements (such as Li) could not be highlighted because of their low characteristic radiation energy, below the detection limit of this analysis technique. It is important to mention that no contaminating species were identified. The Ca/P ratio was also inferred, and the results are presented in Figure 2. The deposition rate can also be influenced by the density and crystallinity of the target [58]. It has also been demonstrated that the addition of different ions influences both the properties of the coatings and the deposition rates [59]. Thus, the thickness variations observed in the case of the synthesized structures can be attributed mainly to the nature of the pristine material, but also to the different ablation rates of Li, Mg, and Ag. In general, when using the PLD technique, pure metals have higher ablation rates [60], which can justify a slightly higher deposition rate in the case of FB:Ag structures in comparison to simple FB ones.

EDS
In addition to the main constituents normally found in the chemical composition of HA (e.g., Ca, P, O), the existence of some trace elements present in the composition of the mineral phase of healthy bone, such as Mg, Si, and S, which play an important role in its functionality, was also highlighted. The presence of light elements (such as Li) could not be highlighted because of their low characteristic radiation energy, below the detection limit of this analysis technique. It is important to mention that no contaminating species were identified. The Ca/P ratio was also inferred, and the results are presented in Figure  2. As one can observe (Figure 2), the deposited structures presented Ca/P values either higher (FB:Ag) or lower (the rest of the samples) than the theoretical value of stoichiometric HA (~1.67) (dashed line in Figure 2). It should be mentioned that these values were similar to those reported in the case of apatites of biological origin [37,56]. As one can observe (Figure 2), the deposited structures presented Ca/P values either higher (FB:Ag) or lower (the rest of the samples) than the theoretical value of stoichiometric HA (~1.67) (dashed line in Figure 2). It should be mentioned that these values were similar to those reported in the case of apatites of biological origin [37,56]. Figure 3 shows the diffractograms corresponding to the source FB and SS materials with respect to those of PLD-derived thin films. Marked differences were observed between the two CaP-based target materials: FB is well-crystallized and consists of a bi-phasic blend of HA (ICDD: 00-009-0432) and β-TCP (ICDD: 00-009-0169) phases, whilst SS is composed of single nanostructured (as indicated by the broad, less-defined diffraction maxima) HA phase. Biphasic calcium phosphate (BCP) materials are recognized for their superior osteoconduction potential with respect to pure, highly crystallized HA [57,61].

XRD
The GIXRD patterns of all PLD films were dominated by the intense maxima of the Ti substrate (indexed with reference file ICDD: 00-044-1294). The ubiquitous presence of a Ti oxidation product (i.e., TiO suboxide, ICDD: 01-086-2352) was noticed for all samples. The CaP-based PLD films yielded low-intensity broad peaks irrespective of the type of bioceramic matrix (i.e., FB or SS) or additive (i.e., Li 3 PO 4 , MgF 2 , or Ag), suggestive of their nano-structuring. Nevertheless, two important differences were noted between the FB and SS film series: (i) the FB films also contained, besides the dominant HA phase, traces of β-TCP; whilst (ii) the SS films, although they elicited higher-intensity HA peaks with respect to the FB films (due to the significantly higher thickness of the former), also presented an important amorphous (less-structured) component evidenced by the halo ranging between 2θ ≈ 23-33 • . Thus, it can be argued that the main compositional features of the source materials were preserved. Figure 3 shows the diffractograms corresponding to the source FB and SS materials with respect to those of PLD-derived thin films. Marked differences were observed between the two CaP-based target materials: FB is well-crystallized and consists of a bi-phasic blend of HA (ICDD: 00-009-0432) and β-TCP (ICDD: 00-009-0169) phases, whilst SS is composed of single nanostructured (as indicated by the broad, less-defined diffraction maxima) HA phase. Biphasic calcium phosphate (BCP) materials are recognized for their superior osteoconduction potential with respect to pure, highly crystallized HA [57,61]. Figure 3. Comparison of the X-ray diffractograms recorded for the FB and SS source target materials (collected in Bragg-Brentano geometry) and of the simple and doped FB and SS thin films (collected in grazing incidence geometry). Symbols: -hydroxyapatite; -β-tricalcium phosphate; -titanium; -TiO).

XRD
The GIXRD patterns of all PLD films were dominated by the intense maxima of the Ti substrate (indexed with reference file ICDD: 00-044-1294). The ubiquitous presence of Figure 3. Comparison of the X-ray diffractograms recorded for the FB and SS source target materials (collected in Bragg-Brentano geometry) and of the simple and doped FB and SS thin films (collected in grazing incidence geometry). Symbols: Figure 3 shows the diffractograms corresponding to the source FB and SS materials with respect to those of PLD-derived thin films. Marked differences were observed between the two CaP-based target materials: FB is well-crystallized and consists of a bi-phasic blend of HA (ICDD: 00-009-0432) and β-TCP (ICDD: 00-009-0169) phases, whilst SS is composed of single nanostructured (as indicated by the broad, less-defined diffraction maxima) HA phase. Biphasic calcium phosphate (BCP) materials are recognized for their superior osteoconduction potential with respect to pure, highly crystallized HA [57,61]. Figure 3. Comparison of the X-ray diffractograms recorded for the FB and SS source target materials (collected in Bragg-Brentano geometry) and of the simple and doped FB and SS thin films (collected in grazing incidence geometry). Symbols: -hydroxyapatite; -β-tricalcium phosphate; -titanium; -TiO).

XRD
The GIXRD patterns of all PLD films were dominated by the intense maxima of the Ti substrate (indexed with reference file ICDD: 00-044-1294). The ubiquitous presence of -hydroxyapatite; -β-tricalcium phosphate; -titanium; -TiO). Figure 4 represents the FTIR spectra of the simple and doped FB and SS thin films in a wave number range relevant for CaP (i.e., 1250-650 cm −1 ). The FB-and SS-samples elicited a major IR absorption maximum with definite shoulders characteristic of specific vibrational modes of orthophosphate functional units in CaPs, i.e., symmetric (ν 1 ) stretching (990-930 cm −1 ) and triply degenerated asymmetric stretching (1200-990 cm −1 ) modes [4,62]. The FB-based samples presented more convoluted spectral envelopes with shallower shoulders, hinting towards a lower structural ordering and/or juxtaposition of (PO 4 ) 3bands stemming from more than one type of CaP phase (in good agreement with the XRD data). Moreover, a supplemental, lower-intensity IR band was evidenced in the wave number range of 850-650 cm −1 , ascribed to vibrations of Ti-O bonds [43,63], furthermore confirming the XRD phase indexing. Figure 4 represents the FTIR spectra of the simple and doped FB and SS thin films in a wave number range relevant for CaP (i.e., 1250-650 cm −1 ). The FB-and SS-samples elicited a major IR absorption maximum with definite shoulders characteristic of specific vibrational modes of orthophosphate functional units in CaPs, i.e., symmetric (ν1) stretching (990-930 cm −1 ) and triply degenerated asymmetric stretching (1200-990 cm −1 ) modes [4,62]. The FB-based samples presented more convoluted spectral envelopes with shallower shoulders, hinting towards a lower structural ordering and/or juxtaposition of (PO4) 3-bands stemming from more than one type of CaP phase (in good agreement with the XRD data). Moreover, a supplemental, lower-intensity IR band was evidenced in the wave number range of 850-650 cm −1 , ascribed to vibrations of Ti-O bonds [43,63], furthermore confirming the XRD phase indexing.

CA and SFE
For comparison, the results of the CA measurements are presented in Figure 5  It was reported that a hydrophilic surface stimulated the adhesion of cells, along with their migration and proliferation, thus promoting a much faster bone regeneration process [57,64]. It is important to mention that the differences between the CA values recorded in It was reported that a hydrophilic surface stimulated the adhesion of cells, along with their migration and proliferation, thus promoting a much faster bone regeneration process [57,64]. It is important to mention that the differences between the CA values recorded in the cases of two consecutive measurements, performed in different areas of the surfaces, were not significant. This result suggests, in agreement with the SEM results, a good uniformity of the synthesized thin films.
The SFE values determined for the simple and doped FB and SS thin films are presented comparatively in Figure 6. It was reported that a hydrophilic surface stimulated the adhesion of cells, along with their migration and proliferation, thus promoting a much faster bone regeneration process [57,64]. It is important to mention that the differences between the CA values recorded in the cases of two consecutive measurements, performed in different areas of the surfaces, were not significant. This result suggests, in agreement with the SEM results, a good uniformity of the synthesized thin films.
The SFE values determined for the simple and doped FB and SS thin films are presented comparatively in Figure 6.

Substrates Adherence
From a macroscopic point of view, all synthesized MdHA layers (simple and doped FB and SS thin films), were very adherent to the Ti substrates, as demonstrated by preliminary adhesion tests such as the finger test and application/removal of an adhesive tape (i.e., scotch test).
The measured values of adherence of the simple and doped FB and SS thin films are presented comparatively in Figure 7; these were calculated as mean ± standard deviation  nary adhesion tests such as the finger test and application/removal of an adhesive tape (i.e., scotch test).

Substrates Adherence
The measured values of adherence of the simple and doped FB and SS thin films are presented comparatively in Figure 7; these were calculated as mean ± standard deviation (SD). It should be mentioned that an event was considered only if the fracturing was of an adhesive type, i.e., when it occurred at the interface between the thin film and the Ti substrate.
The adherence values recorded for simple and doped FB and SS thin films were similar to those reported in the literature for biological-origin films synthesized by PLD [37,56]. It is also important to note that only adherence values higher than that imposed by the ISO 13779-2/2018 (i.e., >15 MPa) are considered acceptable for coatings intended for applications with high biomechanical loads [50]. Taking this criterion into account, the adherence values measured for simple and doped FB and SS thin films should be considered remarkable. Table 3 shows both the mass losses (italic) and mass gains (bold) recorded for simple and doped FB and SS thin films after 3, 7, and 28 days of immersion in DMEM-FBS. By evaluating the values presented in Table 3, a mass loss can be observed in the cases of all simple and doped FB thin films at 3 days of immersion in DMEM-FBS. Moreover, the solubilization process proved to be more intense in the case of FB thin films (a loss of 27.2%), followed by FB:MgF, FB:Ag, and FB:LiP. At 7 days, the solubilization process continued, but it seemed to be accompanied by a precipitation of CaP, a behavior emerging from the evolution of mass values (lower mass losses being recorded with respect to those obtained after 3 days of immersion). This time, the mass losses were higher in the case of FB:LiP thin films (15.1%). After 28 days, for both simple and doped FB thin films, noteworthy mass increases were recorded, the most important one (31.5%) being observed for the FB thin films ( Table 3). The calculated values suggest, once again, the occurrence of the precipitation of CaP phases, which has previously been reported when testing in homeostatic conditions in such complex inorganic-organic synthetic physiological fluids [54,65].

Degradation Tests in Cell Culture Media
Regarding the simple and doped SS thin films, only mass increases were evident for all three time intervals, except for the SS:MgF films, for which a decrease of 0.9% was recorded after 3 days. Thus, after 3 and 7 days of immersion in DMEM-FBS, the most important mass increases were recorded for SS:LiP (10.1% vs. 14.8%). However, after 28 days, the highest value of the mass increase was evident in the case of SS thin films (41.7%)-the highest among all investigated MdHA layers. These results suggest that the SS thin films induced more pronounced CaP in-growths. This can be linked to the higher content of the HA phase in the SS-based samples, known to foster increased apatite-forming ability under biomimetic conditions [66].
The SEM investigations (Figure 8) indicated that morphological changes occur upon immersion in DMEM-FBS, the most marked being recorded in the case of simple FB and SS thin films, in good accordance with the mass loss/gain results (Table 3). These sample topographies were radically modified, with the films' surfaces consisting of blankets of very fine crystals (smaller (for SS) or much smaller (for FB) than in the case of the as-deposited films), which seemed to aggregate into randomly-distributed spherulites. This type of morphology is characteristic of biomimetically-grown CaP deposits [52,54], and it prompted the apatite-forming ability test, which was performed in agreement with the ISO 23317/2014 (the results of which are presented hereafter).   Figure 9 shows typical SEM images of simple and doped FB and SS thin films after 30 days of SBF immersion. With respect to the as-deposited films, all SBF-tested samples exhibited radically altered morphology, with the surface of the samples being covered by acicular nano-crystals which formed spherulite aggregates (seemingly more pronounced than those noticed in the case of DMEM-FBS testing at the 28-day timepoint). As previously highlighted, this is typical for biomimetic CaP-layers developed in physiological environments [52,54,57,67]).  Figure 9 shows typical SEM images of simple and doped FB and SS thin films after 30 days of SBF immersion. With respect to the as-deposited films, all SBF-tested samples exhibited radically altered morphology, with the surface of the samples being covered by acicular nano-crystals which formed spherulite aggregates (seemingly more pronounced than those noticed in the case of DMEM-FBS testing at the 28-day timepoint). As previously highlighted, this is typical for biomimetic CaP-layers developed in physiological environments [52,54,57,67]). One should note that the microcracks observed on the surfaces of thin films tested in both DMEM-FBS ( Figure 8) and SBF ( Figure 9) were induced by the drying process after the sample's extraction from the testing medium.

Apatite-Forming Ability Assays
EDS investigations ( Figure S1) demonstrated that the Ca/P ratios in the case of chemically-grown apatite layers on the surface of the synthesized thin films presented values in the ~1.3-2.2 range, similar to values of biological origin HA [37,56]. It should be emphasized here that non-stoichiometric HA, which presents high solubility rates, is similar to biological apatite and, thus, is more suitable for use in implant coating applications [68]. In addition, these layers of porous HA have the role of improving both the osseointegration and the osteoinduction properties [69].
Further evidence in support of the SEM-and EDS-derived hypothesis was provided by the FTIR-ATR spectroscopy ( Figure 10). The spectra were recorded in the higher-intensity region of the symmetric and asymmetric stretching vibrational modes of phosphate units, in order to be able to discern structural changes (if any) with more ease. Furthermore, in the ATR mode, the FTIR spectroscopy analyses were more sensible to the sample surfaces and their superficial modifications (with respect to the transmission mode). In the case of all SBF-immersed samples, an evident narrowing of the absorption bands was noticed, indicating the formation of a CaP phase with improved structural ordering on the surfaces of the samples. The most radical modification was recorded for the simple SS sample, which agreed well with the weighting data, showing, in this case, the greatest mass gain. One should note that the microcracks observed on the surfaces of thin films tested in both DMEM-FBS ( Figure 8) and SBF ( Figure 9) were induced by the drying process after the sample's extraction from the testing medium.
EDS investigations ( Figure S1) demonstrated that the Ca/P ratios in the case of chemically-grown apatite layers on the surface of the synthesized thin films presented values in the~1.3-2.2 range, similar to values of biological origin HA [37,56]. It should be emphasized here that non-stoichiometric HA, which presents high solubility rates, is similar to biological apatite and, thus, is more suitable for use in implant coating applications [68]. In addition, these layers of porous HA have the role of improving both the osseointegration and the osteoinduction properties [69].
Further evidence in support of the SEM-and EDS-derived hypothesis was provided by the FTIR-ATR spectroscopy ( Figure 10). The spectra were recorded in the higher-intensity region of the symmetric and asymmetric stretching vibrational modes of phosphate units, in order to be able to discern structural changes (if any) with more ease. Furthermore, in the ATR mode, the FTIR spectroscopy analyses were more sensible to the sample surfaces and their superficial modifications (with respect to the transmission mode). In the case of all SBF-immersed samples, an evident narrowing of the absorption bands was noticed, indicating the formation of a CaP phase with improved structural ordering on the surfaces of the samples. The most radical modification was recorded for the simple SS sample, which agreed well with the weighting data, showing, in this case, the greatest mass gain. Pharmaceutics 2023, 15, x FOR PEER REVIEW 18 of 28 Figure 10. FTIR-ATR spectra of simple and doped FB and SS thin films immersed in SBF for 30 days.

Cytocompatibility Assays
Considering the targeted applications of these materials for dental implants, a cytocompatibility evaluation was performed using quantitative and qualitative assays on three types of cells, i.e., osteoblasts, fibroblasts, and epithelial cells, an implant material will interact with [70]. Thus, in contrast with orthopedic bone implants, oral ones must integrate not only into the surrounding bone, but also into the adjacent soft tissues [71].
Concerning the osteoblast cells, among all the tested structures, the FB thin films showed the best cytocompatibility, which was characterized by increased values of the MTT test correlating with low LDH level values (Figure 11a,b). Of all the tested samples, only SS:Ag induced a slight decrease in the cellular viability revealed by the MTT test (Figure 11a), which was also correlated with sub-confluent cellular monolayers evidenced by the phase contrast microscopic examination ( Figure S2). Besides SS:Ag, sub-confluent monolayers were obtained on the SS:MgF sample. These two materials were also associated with the most elevated levels of LDH (Figure 11b), suggesting the induction of cellular damage.

Cytocompatibility Assays
Considering the targeted applications of these materials for dental implants, a cytocompatibility evaluation was performed using quantitative and qualitative assays on three types of cells, i.e., osteoblasts, fibroblasts, and epithelial cells, an implant material will interact with [70]. Thus, in contrast with orthopedic bone implants, oral ones must integrate not only into the surrounding bone, but also into the adjacent soft tissues [71].
Concerning the osteoblast cells, among all the tested structures, the FB thin films showed the best cytocompatibility, which was characterized by increased values of the MTT test correlating with low LDH level values (Figure 11a,b). Of all the tested samples, only SS:Ag induced a slight decrease in the cellular viability revealed by the MTT test (Figure 11a), which was also correlated with sub-confluent cellular monolayers evidenced by the phase contrast microscopic examination ( Figure S2). Besides SS:Ag, sub-confluent monolayers were obtained on the SS:MgF sample. These two materials were also associated with the most elevated levels of LDH (Figure 11b), suggesting the induction of cellular damage.
As the LDH test results illustrate (Figure 11b), none of the simple or doped thin films derived from FB or SS were cytotoxic.
Regarding the NCTC fibroblasts (Figure 11c,d), the behavior of these cells on the surface of the obtained samples was different compared to that of osteoblasts. All samples induced a slight, albeit not statistically significant, decrease in the cellular viability assessed by MTT (Figure 11c). However, in the LDH assay (Figure 11d), all tested samples, except FB:Ag, showed increased cytocompatibility as compared to the Ti control. These results were also sustained by the fluorescence microscopy images using the Live/Dead staining, showing exclusively the presence of live (green) cells grown on the surface of the obtained samples, with morphological features similar to those of the control Ti ( Figure S3). Taken together, the results of the MTT and LDH assays suggest that the FB:LiP thin films are the most cytocompatible in relation with fibroblast cells, characterized by increased values of the MTT test and correlated with low values of LDH (Figure 11c,d).
Concerning the epithelial HeLa cells (Figure 11e,f), the samples containing Ag and MgF (i.e., FB:Ag and FB:MgF) were slightly cytotoxic, as revealed by the lower MTT (Figure 11e), which was correlated with higher LDH values (Figure 11f). Taken together, the results of the MTT and LDH tests indicate that the FB:LiP material exhibited the best cytocompatibility (Figure 11e,f). The cytocompatibility evaluation of HeLa epithelial cells was also confirmed by fluorescence microscopy using DAPI and Cell Mask DeepRed, showing that the cells developed on the tested samples exhibited morphological features similar to those developed on the control surface (i.e., polystyrene surface of the culture dish) ( Figure S4). 1 Figure 11. MTT (a,c,e) and LDH (b,d,f) biocompatibility tests (24 h) in the case of simple and doped FB and SS thin films, using osteoblast (a,b), fibroblast (c,d), and HeLa (e,f) cells.
3.9. Influence of the Obtained Samples on the Production of Osteogenic Markers 3.9.1. Alkaline Phosphatase ALP secreted by osteoblasts represents an early osteogenic marker for bone formation and bone calcification, inducing an elevated phosphate level at the cellular surface during bone mineralization [72]. Previous studies have shown that nanostructured surfaces can promote ALP production, improving the biocompatibility of the implant surface [73]. Therefore, we assessed the production of ALP by osteoblast cells grown on the obtained samples. Compared to uncoated Ti, all simple and doped FB and SS thin films stimulated the secretion of ALP after 48 h of incubation, with the highest levels being recorded for SS:Ag and SS:LiP ( Figure 12).

Osteocalcin
Osteocalcin (bone γ-carboxy glutamic acid), the most important non-collagen bone protein, which is also found in teeth, is an osteogenesis marker mainly produced by osteoblasts [74]. In order to quantify osteocalcin (a regulator of bone mineralization) levels after incubation with the materials, an additional experiment was performed and the obtained results are shown in Figure 13. mation and bone calcification, inducing an elevated phosphate level at the cellular surface during bone mineralization [72]. Previous studies have shown that nanostructured surfaces can promote ALP production, improving the biocompatibility of the implant surface [73]. Therefore, we assessed the production of ALP by osteoblast cells grown on the obtained samples. Compared to uncoated Ti, all simple and doped FB and SS thin films stimulated the secretion of ALP after 48 h of incubation, with the highest levels being recorded for SS:Ag and SS:LiP ( Figure 12).

Osteocalcin
Osteocalcin (bone γ-carboxy glutamic acid), the most important non-collagen bone protein, which is also found in teeth, is an osteogenesis marker mainly produced by osteoblasts [74]. In order to quantify osteocalcin (a regulator of bone mineralization) levels after incubation with the materials, an additional experiment was performed and the obtained results are shown in Figure 13.

Osteocalcin
Osteocalcin (bone γ-carboxy glutamic acid), the most important non-collagen bone protein, which is also found in teeth, is an osteogenesis marker mainly produced by osteoblasts [74]. In order to quantify osteocalcin (a regulator of bone mineralization) levels after incubation with the materials, an additional experiment was performed and the obtained results are shown in Figure 13.  One should emphasize that the results obtained after osteocalcin quantification ( Figure 13) were in good accordance with the ALP levels ( Figure 12).

Antimicrobial Activity
Peri-implantitis represents one of the most frequent complications leading to the loss of an implant. It requires the development of novel materials with improved resistance to microbial colonization and biofilm development [75]. Peri-implantitis is a polymicrobial infection produced by microbial species which are more diverse and different from those involved in periodontitis [76]. Among them, S. aureus plays an important role in the development of peri-implantitis [76], probably due to its high adhesion capacity to Ti surface [77]. Enteric bacteria, Pseudomonas sp., Enterococcus sp., and Candida sp. were also frequently found in peri-implantitis lesions, suggesting that these microorganisms could be involved in the infection of soft and hard tissues surrounding the implant [78][79][80][81]. Although anaerobic species are also key players in dental implant infections, due to technical difficulties in working with anaerobic species, the antimicrobial activity of the simple and doped FB and SS thin films was investigated in this study on facultatively anaerobic Gram-positive and Gram-negative bacteria and fungal strains known to be involved in the etiology of periprosthetic polymicrobial infections (Table 4, Figures S5 and S6).
In the case of the E. coli strain, the antibacterial effect of the tested materials became evident from T 0 , as indicated by the logCFU/mL values recovered from different samples, in comparison with the bare Ti used as the control (Table 4, Figure S5). Statistically significant inhibition was, however, noticed only for FB:LiP, FB:MgF, and SS:Ag. After 4 h, the majority of the tested materials, with the exception of FB:Ag, SS, and SS:LiP, and after 24 h, all of the tested materials, had significantly decreased the logCFU/mL, while at 48 h, the antibacterial protection had been reduced, with a significant decrease in viable cells noticed for FB:MgF, FB:Ag, FB:LiP, and SS:LiP (Table 4, Figure S5). Table 4. Representation of the statistically significant inhibitory effect exhibited by different samples against the adherence and growth of E. coli and P. aeruginosa (in bold) at different incubation times (* p < 0.05; ** p < 0.01; *** p < 0.0001). In the case of the P. aeruginosa strain, at T 0 , similar colonization values were obtained for all tested materials (Table 4, Figure S6). After 2 h, although a slight decrease in the logCFU/mL was noticed, the results were not statistically significant. After 4 h of incubation, all tested materials significantly decreased the levels of P. aeruginosa as compared to the control Ti (Table 4, Figure S6). The FB and FB:Ag thin films significantly inhibited the growth of P. aeruginosa after 24 h of incubation (a 3-4 log reduction as compared to the control Ti: Table 4, Figure S6). After 48 h of incubation, all of the tested materials indicated a lower degree of colonization with P. aeruginosa, but statistically significant values were recorded only in the case of FB:Ag, FB:LiP, FB:MgF, SS:MgF, and SS:Ag thin films (Table 4, Figure S6).

E. coli/P. aeruginosa
In the case of Gram-positive strains, less competitive behavior was recorded in the tested materials in comparison with the Gram-negative ones. For the S. aureus strain (Table 5, Figure S7), at T 0 and at 2 and 4 h, similar levels of colonization were obtained for all tested materials. Table 5. Representation of the statistically significant inhibitory effect exhibited by different samples against the Gram-positive (i.e., S. aureus) and fungal (i.e., C. albicans) (in bold) strains' adherence and growth at different incubation times (** p < 0.01; *** p < 0.0001). In the case of the fungal strain (Table 5, Figure S9), surprisingly, all of the tested materials had significantly inhibited the biofilm after 48 h in comparison with bare Ti, although no significant inhibition was recorded at the previous tested intervals (except for SS, at T 0 and 2 h).

S. aureus/C. albicans
The obtained results indicated that the addition of LiP, MgF, or Ag to FB and SS thin films maintained-and, in many cases, even increased-their anti-biofilm characteristics, with the effect occurring in earlier steps of biofilm development and, in some cases, being extended to 48 h. Considering that the method used to investigate the microbial adhesion and biofilm evolution on the synthesized layers implicated the quantification of the viable cells that adhered to the films' surface, the hypothesis that the synthesized thin films exhibited microbicidal activity, therefore killing the cells before or after their contact with the coated surfaces, could explain the decreased number of biofilm-embedded cells. One should note that this hypothesis is supported by results showing the superior microbicidal activity of simple and doped FB and SS thin films in comparison to the control and Ti, mainly against the S. aureus, E. faecalis, and C. albicans strains.
Even though there are some papers which have reported on biological HA-type coatings obtained by PVD techniques, it should be emphasized that the current preliminary results were the first to be reported on MdHA structures fabricated by PLD. One major advantage of these MdHA coatings is related to the fact that they are synthesized from low-cost, sustainable resources, which are available in huge amounts. Taking into consideration some important demonstrated characteristics, such as hydrophilic behavior, high bonding strength values, low toxicity, and persistent protection against bacterial colonization and fungal biofilm development, these MdHA coatings should be advanced as viable alternatives to synthetic HA for dental implant applications. Even though excellent preliminary, short-term results were obtained, in dentistry, many complex problems might arise; therefore, long-term investigations should also be considered to be of keen importance.
HA was also demonstrated to possess an efficiency strong enough to capture heavy metals by changing cations or adsorbing unchangeable ones onto the crystal surface [82,83]. As a consequence, the amount of possible toxic elements which might be present in the inorganic components of fish bones and/or seashells should also be considered. In this respect, in the case of implants used for various medical applications, the presence of heavy metals (i.e., Cu, Cd, Pb, and/or Hg) in fish bones and/or seashells must be below the concentration limit allowed for inorganic bones [84].
Last, but not least, proper management of the oral microbiota can be considered one important factor that can positively influence the success rate of a dental implant. As proactive and home-based approaches, there are several minimally invasive protocols that must be followed/implemented by every patient to control eubiosis: the removal of bacterial plaque by toothbrushes and interdental subsidies; reducing the bacterial load using probiotics and paraprobiotics (i.e., chewing gum, toothpastes, and mousses); and healing inflammation with the help of natural substances [85,86].

Conclusions
In this study, we reported on the synthesis by PLD of thin layers of hydroxyapatite (HA) of marine origin (MdHA), derived from salmon fish bones (FB) and seashells (SS), both simple and doped (with Li 3 PO 4 , MgF 2 , or Ag, at a concentration of 0.5 wt.%). The fabricated thin films were investigated from morphological, compositional, structural, wettability, and mechanical points of view. In addition, all synthesized thin films were analyzed in vitro by immersion in biological fluids, cell culture assays, and antimicrobial tests.
SEM investigations indicated the existence of surfaces with rough and irregular morphologies, made of particulates (with dimensions of the order of hundreds of nm), which were reported as friendly environments for cells' attachment and growth. The results of the XRD and FTIR spectroscopy analyses evidenced different degrees of crystallinity for the synthesized structures, generally influenced by the dopant's nature and concentration, as well as by the pristine material. For Ti, hydrophobic behavior was observed in comparison to the simple and doped FB and SS thin films, for which strong hydrophilic behavior was detected. Pull-out tests indicated very adherent coatings with values more than three times higher than those imposed by current ISO recommendation.
After only three days of immersion in SBF, the surfaces of the synthesized thin films were uniformly covered by acicular formations. In addition, FTIR spectroscopy investigations indicated a change of the spectral envelopes by narrowing of the absorption bands, which was correlated with the in-growth of biomimetic HA (bio-mineralization capacity). The results of DMEM-FBS immersion suggested that the simple and doped FB and SS thin films were dominated by the CaP precipitation phenomenon, which was more pronounced in the case of films with higher contents of the bioactive HA phase.
The best cytocompatibility was obtained in the case of FB (on osteoblast cells) and FB:LiP (on fibroblast and epithelial cells) thin films. None of the tested layers was cytotoxic, and compared with control Ti, all materials stimulated the secretion of ALP after 48 h of incubation.
All investigated materials showed antimicrobial activity, the most intense effect being obtained in the case of FB:Ag structures. This was most likely due to the presence of the Ag dopant, which, when used in low concentrations, was reported to be a strong barrier against adhesion and contamination with micro-organisms.
The fabrication of competitive metal implant coatings from renewable resources proved to be efficient not only in ensuring a high adherence to the implant's surface and a good cytocompatibility, but also in representing protective barriers against microbial colonization along with proactive action for long-term maintenance. Thus, this process can constitute an important step in the successful development of a new generation of coatings for dental implants.
Supplementary Materials: The following supporting information can be downloaded at: https: //www.mdpi.com/article/10.3390/pharmaceutics15041294/s1, Figure S1: The values of the Ca/P ratio corresponding to the simple and doped FB si SS structures after immersion in SBF for 30 days. Figure S2: Contrast phase microscopy images of control Ti and simple and doped FB and SS thin films' biocompatibility, tested on osteoblast cells (G292). Magnification bar: 100 µm. Figure S3: Fluorescence microscopy images of "Live/Dead" test, performed with NCTC L929 fibroblast cells on control Ti and simple and doped FB and SS thin films. Magnification bar: 100 µm. Figure S4: Fluorescence microscopy images acquired for control Ti and simple and doped FB and SS thin films using epithelial cells (HeLa). Magnification bar: 100 µm. Figure S5: Number of microbial viable cells recovered from the biofilms developing on control Ti and simple and doped FB and SS thin films at T 0 (a), 2 h (b), 4 h (c), 24 h (d), and 48 h (e) using the E. coli strain (* p < 0.05; ** p < 0.01; *** p < 0.0001). Figure S6. Number of microbial viable cells recovered from the biofilms developing on control Ti and simple and doped FB and SS thin films at T 0 (a), 2 h (b), 4 h (c), 24 h (d), and 48 h (e) using the P. aeruginosa strain (** p < 0.01; *** p < 0.0001). Figure S7: Number of microbial viable cells recovered from the biofilms developing on control Ti and simple and doped FB and SS thin films at T 0 (a), 2 h (b), 4 h (c), 24 h (d), and 48 h (e) using the S. aureus strain (*** p < 0.0001). Figure S8: Number of microbial viable cells recovered from the biofilms developing on control Ti and simple and doped FB and SS thin films at T 0 (a), 2 h (b), 4 h (c), 24 h (d), and 48 h (e) using the E. faecalis strain (* p < 0.05; *** p < 0.0001). Figure S9: Number of microbial viable cells recovered from the biofilms developing on control Ti and simple and doped FB and SS thin films at T 0 (a), 2 h (b), 4 h (c), 24 h (d), and 48 h (e) using the C. albicans strain (** p < 0.01; *** p < 0.0001).