Electrochemical Surface Biofunctionalization of Titanium through Growth of TiO 2 Nanotubes and Deposition of Zn Doped Hydroxyapatite

: The current research aim is to biofunctionalize pure titanium (Ti, grade IV) substrate with titania nanotubes and Zn doped hydroxyapatite-based coatings by applying a duplex electrochemical treatment, and to evaluate the inﬂuence of Zn content on the physico-chemical properties of hydroxyapatite (HAp). The obtained nanostructured surfaces were covered with HAp-based coatings doped with Zn in different concentrations by electrochemical deposition in pulsed galvanostatic mode. The obtained surfaces were characterized in terms of morphology, elemental and phasic composition, chemical bonds, roughness, and adhesion. The nanostructured surface consisted of titania nanotubes (NT), aligned, vertically oriented, and hollow, with an inner diameter of ~70 nm. X-ray Diffraction (XRD) analysis showed that the nanostructured surface consists of an anatase phase and some rutile peaks as a secondary phase. The morphology of all coatings consisted of ribbon like-crystals, and by increasing the Zn content the coating became denser due to the decrement of the crystals’ dimensions. The elemental and phase compositions evidenced that HAp was successfully doped with Zn through the pulsed galvanostatic method on the Ti nanostructured surfaces. Fourier Transform Infrared spectroscopy (FTIR) and XRD analysis conﬁrmed the presence of HAp in all coatings, while the adhesion test showed that the addition of a high quantity leads to some delamination. Based on the obtained results, it can be said that the addition of Zn enhances the properties of HAp, and through proper experimental design, the concentration of Zn can be modulated to achieve coatings with tunable features.


Introduction
Generally, biomaterials play an important role in our society and have become a key element for human well-being, especially since the rate of elderly population is increasing rapidly [1]. Among these biomaterials, the metallic ones are extensively used in biomedical devices and components, such as hard tissue replacements, cardiac and cardiovascular stents, etc., due to their desirable mechanical properties and biocompatibility [2].
The fundamental requirement of a biomaterial is found to be in its interaction with its surrounding environment, with which it must coexist without either inducing any undesirable effect on the other [3]. Biomaterials are an important and integrated part of modern medicine and their development and improvement are important challenges [4]. character and to offer proper antibacterial efficiency. The conceptual design of this duplex electrochemical treatment applied to cp-Ti represent the novelty of the present study. To the best of our knowledge, there are only a few studies on the electrochemical deposition of Zn doped HAp and just Ref. [41] reports on Zn doped HAp deposited on TiO 2 NT (using other deposition parameters). Therefore, to achieve the proposed aim, two different quantities of Zn were used to establish the influence of Zn content on the properties of HAp in terms of morphology, elemental and phasic composition, chemical bonds, roughness, and adhesion of the coatings to the substrate.

Sample Preparation
A commercially pure titanium bar (cp-Ti), purchased from Bibus Metals AG, Essen, Germany, was cut into discs (φ = 20 mm, h = 2 mm), which were used as starting materials. The cp-Ti discs were metallographically prepared on silicon carbide paper of different grit (250-1200 grit) and then polished with 1 µm alumina slurry. The prepared discs were cleaned with ultra-pure water (ASTM I) and iso-propylic alcohol to remove the contaminants accumulated during surface preparation. Subsequently, the discs were ultrasonically degreased in acetone and cleaned with ultrapure water. After these steps, the samples had a mirror aspect, and the duplex electrochemical treatment could be applied.

Duplex Electrochemical Treatment 2.2.1. Anodization
The electrochemical setup of the anodizing experiment for a nanostructured surface with self-organized TiO 2 consisted of a two-electrode configuration with a stainless-steel sheet as a counter electrode and the sample (Ti discs) as working electrodes. The nanostructured surface was obtained in 0.5 wt.% HF electrolyte. The anodization potential was kept constant at 20 V with a DC power supply system (N5771A model, Keysight, Böblingen, Germany) for 30 min. The as-anodized samples were annealed for 2 h at 450 • C in air with a heat treatment furnace (N17/HR model, Nabertherm, Lilienthal, Germany).

Coating Deposition
Electrochemical deposition of hydroxyapatite was conducted in a typical three electrode electrochemical cell configured as follows: the working electrode (WE) was the cp-Ti disc with a nanostructured surface, the reference electrode (RE) was a calomel electrode, and the counter electrode (CE) was a platinum foil. The electrodeposition was controlled using a multichannel Potentiostat/Galvanostat (Parstat MC, Princeton Applied Research-Ametek, Oak Ridge, TN, USA) operating in pulsed galvanostatic mode. One pulse consisted of an activation stage (i ON = −0.85 mA/cm 2 for 1 s), followed by a relaxation stage (i OFF = 0 mA/cm 2 for 1 s) [42]. In total, 1200 pulses were applied.
The electrolyte was prepared by dissolving calcium nitrate tetrahydrate (Ca(NO3) 2 ·4H 2 O), ammonium dihydrogen phosphate (NH 4 H 2 PO 4 ), and zinc nitrate hexahydrate (Zn(NO 3 ) 2 ·6H 2 O) in ultra-pure water in different concentrations, which are presented in Table 1. All the chemicals were of reagent grade and were purchased from Sigma-Aldrich (Munich, Germany). The electrolyte's pH was measured and adjusted to 5 by the drop-wise of 1 M NaOH in the presence of a pH/ORP-meter (HI 4221, Hanna Instruments, Smithfield, RI, USA). To minimize the formation of CaCO 3 deposits, the electrolyte was de-aerated with nitrogen gas before deposition. During deposition, the temperature was controlled and kept constant to 75 • C using a basic magnetic hotplate stirrer (KA RCT Basic Safety Control Hotplate/Stirrer and ETS-D6 Temp, IKA, Staufen, Germany). To keep the concentration of the electrolyte uniform, during the deposition, the solution was continuously stirred with a magnetic bar. After the electrodeposition, the samples were rinsed with ultra-pure water and dried at room temperature in a desiccator.

Characterization
The nanostructured surface of cp-Ti, consisting of titania nanotubes (NT), was analyzed in terms of morphology with a field-emission scanning electron microscope (Scienta Omicron NanoSAM Lab system, Oxford Instruments, High Wycombe, UK), while the coating's surface morphology was investigated with a Scanning Electron Microscope equipped with an X-ray Energy Dispersive Spectrometer (SEM-EDS, Phenom ProX, Phenom World, Eindhoven, The Netherlands).
The phase composition of the samples (nanostructured surface and coatings) was studied by X-ray diffraction (Rigaku SmartLab, Tokyo, Japan) using an X-ray source of CuKα (λ = 1.5406 Å) in the range θ/2θ of 20-80 • at an incident angle of 3 • , with a medium resolution parallel beam optical system.
The Debye-Scherrer mathematical relation (Equation (1)) was used to estimate the crystallite size for the (002) diffraction plane, being the most intense diffraction peak in HAp coatings obtained by electrochemical deposition [37].
where K = 0.9 is a constant shape factor for HAp with hexagonal structure, β is the full width at half maximum (FWHM) measured in radian of (002) diffraction plane, and θ in degrees indicates the Braggs diffraction angle, λ = 1.5406 Å is the wavelength of CuKα radiation. The crystallinity (χ c ) was estimated using the following equation (Equation (2)) [43][44][45]: where K A is a constant found equal to 0.24 for HAp bioceramic, and β is the FWHM of refection (002) in degrees. The lattice parameters of hydroxyapatite-based coatings were computed using (Equation (3)), the relation between the interplanar spacing distance (d hkl ) and lattice constants (a and c) for a hexagonal crystallographic system [46,47], as follows: The chemical bonds and identification of the functional groups was achieved by Fourier Transform Infra-Red (FTIR) spectroscopy in attenuated total reflectance (ATR) mode. The FTIR-ATR spectra were collected in the 4000-600 cm −1 wave numbers range using FT-IR, Jasco 6300 (Jasco, Tokyo, Japan) with the universal ATR sampling accessory Pike MIRacle (Pike Technologies, Madison, WI, USA).
Surface roughness was measured over a length of 3000 µm, using a DEKTAK 150 (Veeco Instruments, Plainview, NY, USA) profilometer. The thickness of the coatings were also determined by a DEKTAK 150 profilometer (stylus radius of 12.5 µm), measuring the forming ledge between the deposited film and the uncoated substrate.

Morphology
The HR-SEM images of the anodized samples before and after annealing are presented in Figure 1. It can be observed that the TiO 2 nanotubes are highly oriented and uniformly distributed on the surface. The inner diameter before and after annealing was measured and highlighted that the diameter of the NT presents a small decrement from 75 (±5 nm), obtained for the as-anodized one, compared to 70 (±7 nm) for the annealed ones. The chemical bonds and identification of the functional groups was achieved by Fourier Transform Infra-Red (FTIR) spectroscopy in attenuated total reflectance (ATR) mode. The FTIR-ATR spectra were collected in the 4000-600 cm −1 wave numbers range using FT-IR, Jasco 6300 (Jasco, Tokyo, Japan) with the universal ATR sampling accessory Pike MIRacle (Pike Technologies, Madison, WI, USA).
Surface roughness was measured over a length of 3000 μm, using a DEKTAK 150 (Veeco Instruments, Plainview, NY, USA) profilometer. The thickness of the coatings were also determined by a DEKTAK 150 profilometer (stylus radius of 12.5 μm), measuring the forming ledge between the deposited film and the uncoated substrate.

Morphology
The HR-SEM images of the anodized samples before and after annealing are presented in Figure 1. It can be observed that the TiO2 nanotubes are highly oriented and uniformly distributed on the surface. The inner diameter before and after annealing was measured and highlighted that the diameter of the NT presents a small decrement from 75 (±5 nm), obtained for the as-anodized one, compared to 70 (±7 nm) for the annealed ones. Compared to our previous study [49], it can be said that by reducing the anodization time from 1 h to 0.5 h, the diameter has decreased from an average value of 75 nm to 70 nm, and the nanotubes appear to be better organized in terms of density (with smaller spaces between them). The obtained results are in strong correlation with the available literature [50,51]. Thus, it can be said that by reducing the anodization time, nanotubes with a smaller inner diameter can be obtained.
In Figure 2 are presented the SEM images obtained on the undoped and zinc doped HAp based coatings, electrochemically deposited on the TiO2 nanostructured surface Compared to our previous study [49], it can be said that by reducing the anodization time from 1 h to 0.5 h, the diameter has decreased from an average value of 75 nm to 70 nm, and the nanotubes appear to be better organized in terms of density (with smaller spaces between them). The obtained results are in strong correlation with the available literature [50,51]. Thus, it can be said that by reducing the anodization time, nanotubes with a smaller inner diameter can be obtained.
In Figure 2 are presented the SEM images obtained on the undoped and zinc doped HAp based coatings, electrochemically deposited on the TiO 2 nanostructured surface (NT). At small magnification, it can be observed that all coatings are covering the surface with a uniform and compact layer, which does not present defects.
At higher magnification, the SEM images highlight that the coatings' morphology consists of elongated ribbon-like crystals, very thin, within the nanometric scale, forming a complex morphology that resemble a 3D architecture. All coatings have crystallized Coatings 2022, 12, 69 6 of 16 perpendicular on the substrate, which is characteristic for the electrochemical deposition process [52].
The addition of Zn within the HAp has led to some morphological modifications, which are as follows. Compared to the H coatings, whose morphology is predominant in very thin and narrow crystals, the addition of Zn has led to visible dimensional changes of the ribbon-like crystals, which have become wider, thicker, and smaller, irrespective of Zn content. Moreover, by increasing the Zn concentration, not only are the crystals dimensions reducing, but the layer also begins to appear denser, suggesting that the addition of Zn, even in very small amounts, affects the electro-crystallization of HAp. A possible explanation for this could be attributed to the differences between the ionic radius of Zn 2+ (0.074 nm) and Ca 2+ (0.099 nm), which can lead to a structural mismatch that prevents HAp crystal growth when Zn is incorporated in the HAp structure [53,54].
(NT). At small magnification, it can be observed that all coatings are covering the surface with a uniform and compact layer, which does not present defects.
At higher magnification, the SEM images highlight that the coatings' morphology consists of elongated ribbon-like crystals, very thin, within the nanometric scale, forming a complex morphology that resemble a 3D architecture. All coatings have crystallized perpendicular on the substrate, which is characteristic for the electrochemical deposition process [52].
The addition of Zn within the HAp has led to some morphological modifications, which are as follows. Compared to the H coatings, whose morphology is predominant in very thin and narrow crystals, the addition of Zn has led to visible dimensional changes of the ribbon-like crystals, which have become wider, thicker, and smaller, irrespective of Zn content. Moreover, by increasing the Zn concentration, not only are the crystals dimensions reducing, but the layer also begins to appear denser, suggesting that the addition of Zn, even in very small amounts, affects the electro-crystallization of HAp. A possible explanation for this could be attributed to the differences between the ionic radius of Zn 2+ (0.074 nm) and Ca 2+ (0.099 nm), which can lead to a structural mismatch that prevents HAp crystal growth when Zn is incorporated in the HAp structure [53,54].

Elemental Composition
The EDS spectra, elemental composition and distribution of each element are presented in Figure 3 and Table 2. Based on this investigation, it can be stated that all characteristic elements of hydroxyapatite (Ca, O, P), along with the doping elements (Zn) and Ti, as part of the substrate and/or nanostructured surface, are present in all coatings.

Elemental Composition
The EDS spectra, elemental composition and distribution of each element are presented in Figure 3 and Table 2. Based on this investigation, it can be stated that all characteristic elements of hydroxyapatite (Ca, O, P), along with the doping elements (Zn) and Ti, as part of the substrate and/or nanostructured surface, are present in all coatings.
Considering that Zn 2+ substitutes the Ca 2+ found in the HAp structure, the Ca/P ratio was calculated accordingly, and thus the ratio was obtained by summing the Zn to the Ca content, and divided to that of P, as following (Ca + Zn)/P.
All developed coatings presented smaller values in terms of their Ca/P ratio, compared to the natural HAp one, which had a ratio of 1.67. The highest Ca/P ratio was obtained for the H coatings, with a value of 1.59, which further decreased to 1.56 for H-Zn1 and 1.55 for H-Zn2, highlighting that the addition and increment of the Zn content alters the Ca/P ratio. A similar tendency was also reported in Ref [55].
Considering that Zn 2+ substitutes the Ca 2+ found in the HAp structure, the Ca/P ratio was calculated accordingly, and thus the ratio was obtained by summing the Zn to the Ca content, and divided to that of P, as following (Ca + Zn)/P.
All developed coatings presented smaller values in terms of their Ca/P ratio, compared to the natural HAp one, which had a ratio of 1.67. The highest Ca/P ratio was obtained for the H coatings, with a value of 1.59, which further decreased to 1.56 for H-Zn1 and 1.55 for H-Zn2, highlighting that the addition and increment of the Zn content alters the Ca/P ratio. A similar tendency was also reported in Ref [55].  A smaller Ca/P ratio, between 1.33 and 1.67, indicates the presence of a Ca-deficient apatite, which has a composition and structure that resembles the natural bone mineral [56] and is considered to be a suitable candidate for bone regeneration [57]. Moreover, a lower Ca/P ratio can also suggest an enhanced solubility and thus a more bioactive character [58].  A smaller Ca/P ratio, between 1.33 and 1.67, indicates the presence of a Ca-deficient apatite, which has a composition and structure that resembles the natural bone mineral [56] and is considered to be a suitable candidate for bone regeneration [57]. Moreover, a lower Ca/P ratio can also suggest an enhanced solubility and thus a more bioactive character [58].
Regarding the Zn content, it can be noted that the H-Zn1 coatings present a quantity of 0.78 at.%, which increases by 60% for the H-Zn2, reaching a value of 1.3 at.%.
According to the study performed by Miyaji et al. [59], it has been shown that there is a substituting limit of Zn which was estimated to be at about 15 mol.%, and that a too-high content of zinc favors the formation of amorphous phase, which can lead to rapid degradation. Ito et al. [26] suggested that a low concentration of Zn 2+ , found to be between 0.6 and 1.2 wt.%, is favorable to avoid cytotoxicity, and enhances cell proliferation. Thus, it can be stated that the H-Zn1 coatings fit within the maximum amount which does not affect the cell behavior.

Phase Composition
In Figure 4 and Table 3 are presented the obtained XRD diffractograms and the structural characteristic parameters obtained from XRD analysis.
The XRD diffractogram (Figure 4) of the NT substrate revealed the presence of specific diffraction peaks for titanium (ICDD #44-1298), anatase (ICDD Nr. 00-021-1272)-this being also the majority phase-and rutile (Nr. 00-021-1276). Bai et al. [60] consider that an optimal structure would consist of a mixture of phases, namely anatase and rutile, as the mechanical interaction at the bone-implant interface may be favored. Moreover, the rutile phase is expected to improve the chemical resistance of the material during its interaction with the biological environment, thus preventing the release of titanium ions, while the anatase phase, improves the proliferation and osteoblast adhesion [61] and favors the formation of calcium phosphates [62].
The X-ray diffraction of the undoped and doped HAp-based coatings confirmed the presence of HAp according to ICDD #09-0432 as the main crystal phase in all three coatings in accordance with the International Center for Diffraction Data (ICDD).
The most intense diffraction peak, which is characteristic for electrochemical deposited coatings, is located at~26 • and is associated with the (002) plane, indicating that the HAp crystals are oriented perpendicular to the NT surface [42]. According to the literature, the HAp with a c-axis orientation increases cell proliferation, chemical stability, and mechanical properties [63,64]. Moreover, as can be observed in Figure 4 and Table 3, the addition of Zn into the HAp structure has led to shifts towards higher angles, indicating the substitution of higher ionic radius Ca 2+ (0.099 nm) ions for those of Zn 2+ (0.074 nm), which have a smaller ionic radius, inducing the contraction of the HAp lattice [65]. According to ICDD #1-071-1759, one diffraction peak located at ~31° was assigned to monetite, a precursor of HAp. Its presence can be beneficial in these coatings, as it is known for its potential for bone regeneration and its osteoconductive and osseoinductive According to ICDD #1-071-1759, one diffraction peak located at~31 • was assigned to monetite, a precursor of HAp. Its presence can be beneficial in these coatings, as it is known for its potential for bone regeneration and its osteoconductive and osseoinductive character [66,67]. According to the XRD analysis, no peaks could be attributed to pure Zn in its metallic form in the Zn-doped HAp coatings, irrespective of the Zn concentration.
The addition of Zn in the HAp structure leads to a decrease in the lattice parameters a and c (Table 3), which is in accordance with the literature [68,69]. The differences in terms of lattice parameters between the H-Zn1 and H-Zn2 are very small, suggesting that a higher concentration may not induce significant changes. Both crystallite size and crystallinity contrast with lattice parameters and, based on the obtained results, it was noted that, compared to H, both increase with the addition of Zn. Thus, by comparison with H, the crystallinity of the H-Zn coatings increased by~50%, while the crystallite dimension increased by~25%, indicating the beneficial effect of the Zn in the HAp structure. By comparing the Zn doped coatings, it can be observed that by using a higher quantity of Zn, both the crystallinity and crystallite dimensions start to decrease, suggesting that a too-high Zn content inhibits the crystallinity of the HAp coatings. Similar findings have also been reported elsewhere [23,31].

Roughness
The main roughness parameters and profile line specific to each surface are presented in Figure 5. By comparing the average roughness (Ra) of the Ti with that of the NT, it can be noted that roughness has increased, reaching a value of~130 nm due to the presence of the nanotubes, which is in good agreement with other studies [49].
By comparison to the NT surface, the H coatings obtained through the pulse galvanostatic technique have led to an increment of the roughness of 4 times more, with a value of the Ra of~540 nm. The addition of Zn in the HAp structure has led to a decrement of its roughness, from~540 nm (H coatings) to~320 nm (H-Zn1) and~240 nm (H-Zn2), suggesting that Zn smooths the surface. These results are in agreement with the SEM images, in which the size of the ribbon-like crystals decreases after the addition of Zn, leading to a denser coating.
The skewness parameter (R sk ) offers information on the hills (slope < 0) and valleys (slope > 0) distribution. According to the literature, the R sk parameters can provide valuable information on how the material will act in terms of electrochemical behavior and biodegradation [70][71][72][73]. Moreover, the surfaces with a positive R sk present favorable coating adhesion compared to surfaces with a negative one [66].
Thus, it can be observed that all coatings registered positive values of the R sk parameter, which are very close to each other, indicating that the surface is predominantly hills.
In terms of coating thickness, which was determined with the contact profilometer, by measuring the profile of the ledge between the coating and the substrate, it can be observed that the H and H-Zn1 coatings have registered close values of 9.75 µm for the H and of 10.61 µm for the H-Zn1. According to Ref. [74], a thickness of~10 µm is favorable for bone apposition. If the thickness of the coatings is too high, the coatings can present poor adhesion, while a too-small value, associated with poor crystallinity, can affect the coating stability [75,76]. The smallest thickness, of 5.54 µm, was noted for the H-Zn2 coatings, suggesting that the nucleation and growth of HAp is affected when even a slightly higher amount of Zn is added within the electrolyte, leading to a smaller deposition rate.
decrease, suggesting that a too-high Zn content inhibits the crystallinity of the HAp coatings. Similar findings have also been reported elsewhere [23,31].

Roughness
The main roughness parameters and profile line specific to each surface are presented in Figure 5. By comparing the average roughness (Ra) of the Ti with that of the NT, it can be noted that roughness has increased, reaching a value of ~130 nm due to the presence of the nanotubes, which is in good agreement with other studies [49]. By comparison to the NT surface, the H coatings obtained through the pulse galvanostatic technique have led to an increment of the roughness of 4 times more, with a value of the Ra of ~540 nm. The addition of Zn in the HAp structure has led to a decrement of its roughness, from ~540 nm (H coatings) to ~320 nm (H-Zn1) and ~240 nm (H-Zn2), suggesting that Zn smooths the surface. These results are in agreement with the SEM images, in which the size of the ribbon-like crystals decreases after the addition of Zn, leading to a denser coating.
The skewness parameter (Rsk) offers information on the hills (slope < 0) and valleys (slope > 0) distribution. According to the literature, the Rsk parameters can provide valuable information on how the material will act in terms of electrochemical behavior and biodegradation [70][71][72][73]. Moreover, the surfaces with a positive Rsk present favorable coating adhesion compared to surfaces with a negative one [66].
Thus, it can be observed that all coatings registered positive values of the Rsk parameter, which are very close to each other, indicating that the surface is predominantly hills.
In terms of coating thickness, which was determined with the contact profilometer, by measuring the profile of the ledge between the coating and the substrate, it can be observed that the H and H-Zn1 coatings have registered close values of 9.75 μm for the H and of 10.61 μm for the H-Zn1. According to Ref. [74], a thickness of ~10 μm is favorable for bone apposition. If the thickness of the coatings is too high, the coatings can present poor adhesion, while a too-small value, associated with poor crystallinity, can affect the  coating stability [75,76]. The smallest thickness, of 5.54 μm, was noted for the H-Zn2 coatings, suggesting that the nucleation and growth of HAp is affected when even a slightly higher amount of Zn is added within the electrolyte, leading to a smaller deposition rate.  Thus, the spectrum illustrates the main vibration modes of the phosphate group (PO ), which were identified between 1022 cm −1 and 1100 cm −1 (ν3), and at 635 cm −1 and 961 cm −1 (ν4), respectively [77,78]. The υ4 and υ3 (PO ) vibration bands are considered Thus, the spectrum illustrates the main vibration modes of the phosphate group PO 3− 4 , which were identified between 1022 cm −1 and 1100 cm −1 (ν 3 ), and at 635 cm −1 and 961 cm −1 (ν 4 ), respectively [77,78]. The υ 4 and υ 3 PO 3− 4 vibration bands are considered the IR fingerprint of a HAp structure.

Chemical Bonds
A very broad band identified between 3000 cm −1 and 3600 cm −1 in the H coatings was assigned to the adsorbed water [79]. Even though the Zn doped HAp coatings presented the same shape, some differences were noted, as follows. The peaks found between 1022 cm −1 and 1100 cm −1 associated with the υ 3 PO 3− 4 vibration and the symmetric stretching mode of PO 3− 4 (ν 1 ) identified at 961 cm −1 decrease in intensity after zinc addition, being also dependent on the Zn concentration.
All coatings present a weak sharp peak at 628 cm −1 which was assigned to the libration of (OH) − groups in HAp [80][81][82]. However, the intensity of this absorption peak, associated with the structural (OH) − group at 628 cm −1 observed in the H coatings, has significantly diminished after the addition of Zn, highlighting the loss of OH − ions from the unit cell and the apparent substitution of Zn ions into the lattice of HAp [83].

Adhesion
In Figure 7 are presented the SEM images of the coatings after performing the adhesion assays by "tape test" according to the ASTM procedure. Similar tests were also performed by Parcharoen et al. [84], who have investigated the adhesion between HAp based coatings deposited on NT of different lengths.
The results of adhesion tests based on SEM investigation revealed that the H and H-Zn1 have a strong adhesion to the substrate classified according to the standard ASTM D 3359-17 on the top category, namely 4B, highlighting only small detachments of coating along the indentation line or at cuts intersection.
By increasing the amount of Zn, it was noted that the delamination/detached area is found between 5-15%, thus affecting the H-Zn2 coating, which falls into the 3B category of the standard. Based on the results, it can be concluded that by adding a small amount of a doping element, the adhesion of coatings is not affected.
Even though in the present study the nanotubes' lengths were not evaluated, based on the other literature reports [50,51], it can be argued that the length of the nanotubes obtained in weak hydrofluoric acid electrolyte (0.5 wt.% HF) when a potential of 20 V is applied for 30 min or 60 min is~400 nm. Thus, it was assumed that the length of the nanotubes is within the range which offers suitable adhesion to the HAp based coatings.
Moreover, in a study performed by Dey et al. [85], it was highlighted that if the NT length is too high, the in vivo behavior could be compromised, due to insufficient mechanical stability, which can cause breakage of the nanotubes from the titanium. Nevertheless, according to Bauer et al. [86], the length of the nanotubes does not influence cell behavior, and thus the length of the nanotubes was not considered in the current study.
Zn1 have a strong adhesion to the substrate classified according to the standard ASTM D 3359-17 on the top category, namely 4B, highlighting only small detachments of coating along the indentation line or at cuts intersection.
By increasing the amount of Zn, it was noted that the delamination/detached area is found between 5-15%, thus affecting the H-Zn2 coating, which falls into the 3B category of the standard. Based on the results, it can be concluded that by adding a small amount of a doping element, the adhesion of coatings is not affected. Even though in the present study the nanotubes' lengths were not evaluated, based on the other literature reports [50,51], it can be argued that the length of the nanotubes obtained in weak hydrofluoric acid electrolyte (0.5 wt.% HF) when a potential of 20 V is applied for 30 min or 60 min is ~400 nm. Thus, it was assumed that the length of the nanotubes is within the range which offers suitable adhesion to the HAp based coatings.
Moreover, in a study performed by Dey et al. [85], it was highlighted that if the NT length is too high, the in vivo behavior could be compromised, due to insufficient mechanical stability, which can cause breakage of the nanotubes from the titanium. Nevertheless, according to Bauer et al. [86], the length of the nanotubes does not influence cell behavior, and thus the length of the nanotubes was not considered in the current study.

•
The electrochemical surface functionalization of Ti by the growth of nanotubes with an average diameter of~70 nm and deposition of undoped HAp doped with Zn in different concentrations was successfully achieved by electrochemical techniques. The present study highlighted that the addition of Zn in even a small amount can enhance the characteristics of HAp. All coatings presented a morphology consisting of ribbon-like crystals, which suffers some alterations by the addition and increment of Zn content. The XRD and FTIR investigations have confirmed that all coatings consist in HAp as a main phase. Irrespective of the Zn content, the crystallinity of the HAp coatings was enhanced after the addition of Zn.

•
Regarding the effect of Zn content on the properties of HAp, it can be said that even though the differences between the two selected concentrations is minor, the coating H-Zn1 (with Zn of 0.78 at.%) has met most of the requirements, being more suitable for medical applications. Thus, the coatings with a smaller Zn amount will be further evaluated in terms of electrochemical behavior in synthetic media, along with their biomineralization ability and in vitro cell behavior, to establish if the proposed coatings can impart a good biocompatibility with a suitable bioactive character and antibacterial efficiency, without inducing a cytotoxic effect.