Electrodeposition of Hydroxyapatite-Multiwalled Carbon Nanotube Nanocomposite on Ti6Al4V

Nguyen, Thom T.; Pham, Nam T.; Dinh, Thanh T. M.; Vu, Thu T.; Nguyen, Hai S.; Tran, Lam D.

doi:https://doi.org/10.1155/2020/8639687

Advances in Polymer Technology

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Abstract Introduction Materials and Methods Results and Discussion Conclusions Data Availability Conflicts of Interest Acknowledgments References Copyright Related Articles

Research Article | Open Access

Volume 2020 | Article ID 8639687 | https://doi.org/10.1155/2020/8639687

Electrodeposition of Hydroxyapatite-Multiwalled Carbon Nanotube Nanocomposite on Ti6Al4V

Thom T. Nguyen,^1,2Nam T. Pham,¹Thanh T. M. Dinh,^2,3Thu T. Vu,³Hai S. Nguyen,⁴and Lam D. Tran¹

Academic Editor: Sagar Roy

Received03 Jul 2019

Revised14 Feb 2020

Accepted27 Feb 2020

Published15 Apr 2020

Abstract

This work aims to study the optimal conditions to synthesize hydroxyapatite-multiwalled carbon nanotube (HAp-MWCNT) coatings on Ti6Al4V by electrodeposition technique. The structural behaviors, morphology, and mechanical properties of the coatings were characterized by various advanced methods. The analyzed results showed that the obtained coatings were composed of hydroxyapatite (HAp) and multiwalled carbon nanotube (MWCNT) phases. The presence of MWCNTs in the HAp-MWCNT composite, which improved adhesion between the coatings and the substrate about 2.3 times, increased 20% of hardness and decreased about 40% the solubility of HAp-MWCNTs/Ti6Al4V in comparison with pure HAp coating on Ti6Al4V.

1. Introduction

Multiwalled carbon nanotubes have recently attracted many attention in biomedical applications due to their extraordinary behaviors, including large surface area, high tensile strength, good corrosion resistance, and good biocompatibility [1–4]. Many research groups have reported the use of this fantastic material in manufacturing highly conductive electrodes for sensor and neural stimulation [2, 3]. For bone implant, the presence of such a durable material in the mineral composite can significantly increase the strength of the tissue/bone joint and somehow stimulate new bone formation [5–8].

The HAp-MWCNT nanocomposite coatings can be fabricated by many techniques, including coprecipitation, pulsed electrodeposition, shear mixing, sprayed plasma, electrophoretic deposition and electrodeposition [6, 8–14]. By coprecipitation, a large amount of HAp-MWCNTs can be obtained. However, the obtained materials are not pure with the presence of different compounds of calcium phosphate. Studies show that using sprayed plasma to form HAp-MWCNTs has good adhesion with the substrate, but the high temperature causes the formation of tricalcium phosphate ((Ca₃(PO₄)₂), TCP) [8]. Electrodeposition seems to be the most attractive and promising technique to fabricate HAp-MWCNT coatings on the surface of metals or alloys. This method has many advantages such as low process temperature, ability to coat geometrically complex surfaces, convenience to control the coating properties, and low cost [15].

Nowadays, 316L SS and Ti6Al4V are commonly used as biomedical bone screws [16]. In our previous studies, HAp-MWCNT coating was successfully deposited on the surface of 316L SS [17–19]. Over time, studies to find more advanced materials are necessary. So, the aim of this work is to develop a new nanocomposite coating based on hydroxyapatite and carbon nanotubes on the surface of the Ti6Al4V biometallic alloy. The effects of synthesis condition such as scanning potential range, scanning rate, number of scans, synthesis temperature, and MWCNT content on the characterization of the obtained coatings were investigated. The results allow us to select the most suitable conditions to synthesize HAp-MWCNT/Ti6Al4V material.

2. Materials and Methods

2.1. Materials

Calcium nitrate hydrate (Ca(NO₃)₂.4H₂O, 99% pure), ammonium dihydrogen phosphate (NH₄H₂PO₄, 99% pure), sodium nitrate (NaNO₃, 99% pure), nitric acid (HNO₃, 67 wt.%), and sulfuric acid (H₂SO₄, 98 wt.%) were purchased from Sigma-Aldrich. Multiwalled carbon nanotubes (MWCNTs) (diameter of 15–90 nm and length of 1–10 μm, 93%) were given by the Institute of Materials Science, Vietnam Academy of Science and Technology (Hanoi, Vietnam) [20]. The substrates Ti6Al4V (composed of 89.63% Ti, 6.04% Al, 4.11% V, 0.05% C, and 0.17% Fe) were purchased from Gloria Material Technology Corp (Taipei, Taiwan).

2.2. Preparation of Carboxylated Multiwalled Carbonanotubes (MWCNTs-COOH)

Multiwalled carbon nanotubes were functionalized with carboxylic functional groups by treatment in a mixture of acids (HNO₃ : H₂SO₄ = 1 : 3) at 110°C for 1 h under continuous magnetic stirring [13]. The carboxylated product was filtered and washed with distilled water several times until no residual acid was found. The final product was dried and stored in ambient conditions until use. MWCNTs before and after modification process were characterized in our previous publications [18]. It confirms the formation of -COOH groups after modification process.

2.3. Electrodeposition of HAp-MWCNTs on Ti6Al4V [18, 19]

The electrolyte solution (pH = 4.4) containing 30 mM Ca(NO₃)₂, 18 mM NH₄H₂PO₄, and 150 mM NaNO₃ was first prepared in distilled water. After that MWCNTs-COOH material was dispersed in the electrolyte solution using an intense ultrasonication treatment for ten minutes at different concentrations (0-1 g·L⁻¹). These solutions are denoted as HAp, HAp-MWCNTs_0.25, HAp-MWCNTs_0.5, HAp-MWCNTs_0.75, and HAp-MWCNTs_1.0 corresponding to the MWCNTs-COOH concentration of 0, 0.25, 0.5, 0.75, and 1.0 g·L⁻¹, respectively.

Electrodeposition of HAp with and without MWCNTs-COOH was carried out on the biologic electrochemical workstation (VSP-300, France) using a cell of three-electrode setup. A platinum grid was used as the counter electrode, while a Hg/Hg₂Cl₂/KCl (SCE) electrode was used as the reference electrode. A Ti6Al4V sheet (1.5 × 1 × 0.2 cm³) was used as the working electrode. The working area was limited to be 1 cm² using epoxy glue. The working electrode was polished, then washed with distilled water, and finally dried under nitrogen gun right before use. The electrodeposition process of HAp, HAp-MWCNTs_0.25, HAp-MWCNTs_0.5, HAp-MWCNTs_0.75, and HAp-MWCNTs_1.0 onto the Ti6Al4V electrode was performed using cyclic voltammetry technique. Different synthesis conditions (scanning potential ranges, number of scans, and temperature) were investigated. All the obtained samples were rinsed thoroughly with distilled water before being dried at 80°C in vacuum for 24 h.

2.4. Morphology and Structural Behaviors of HAp and HAp-MWCNT Coatings

The morphology of the coatings was examined by using JEOL-JSM-6510LV field emission scanning electron microscopy (SEM) operated at 20 kV. More details on morphological behaviors of the coatings at a smaller scale were also tested with using atomic force microscopy (AFM) (XE-100 Park Systems).

Fourier transform infrared (FTIR), Raman spectroscopy (excitation wavelength of 633 nm) (IS10, NEXUS), and X-ray diffraction (Cu-K_α radiation, 40 kV) (SIEMENS D5005 Bruker-Germany) techniques were used to test structural behaviors of the materials.

The mass of the electrodeposited coatings was determined from the subtraction between the mass of the Ti6Al4V electrode before and after modification (balanced by the Precisa analytical balance, XR 205 SM—PR, Swiss). The thickness of HAp-MWCNT coating is measured by the Alpha-Step IQ system (KLA-Tencor, USA), which is a surface morphology device that operates on the needle contact principle, according to the ISO 4288-1998 standard at the Institute of Materials Science, Vietnam. The obtained result is the average value of 5 measurements.

2.5. Mechanic Properties of HAp and HAp-MWCNT Coatings

The adhesion of HAp and HAp-MWCNT coatings onto Ti6Al4V substrates was evaluated by tensile testing following the ASTM F1044 standard [21]. The hardness and elastic modulus of the coatings were determined using Mikrohärte-Prüfeinrichtung mhp 100 following TCVN—258-1 : 2007 Vietnam standard and MTS 793 (g), USA. The dissolution of HAp or HAp-MWCNT coatings in 20 mL of 0.9% NaCl solution at different soaked times was determined through Ca²⁺ concentration using atomic absorption apectrometry (iCE-3500, Thermo, Germany).

3. Results and Discussion

3.1. Effect of Process Parameters on the Properties of the Obtained Coatings

3.1.1. Electrodeposition of HAp-MWCNT Coatings

The growth mechanism of HAp-based materials on the electrode surface can be expressed in equations (1)–(7). At first, hydroxyl ions (OH⁻) and phosphate anions (PO₄³⁻) are generated from water reduction (equation (1)) and hydrogen phosphate anions (H₂PO₄⁻ and HPO₄²⁻) (equations (2) and (3), respectively). Later, these ions react with calcium cations (Ca²⁺) to provide a white precipitate (HAp) which is deposited directly onto the electrode surface (equation (5)). In the same time, MWCNTs-COOH material which might be bonded to HAp through hydrogen bonds between carboxylic and hydroxyl groups [22] will also be trapped into HAp coatings. The presence of carbonaceous material in HAp coatings might be observed visibly by a slight color change from white to grey white. It is worthy to note that the occurrence of hydrogen bubbles during electrodeposition process is unavoidable. This continuous formation of hydrogen gas at the electrode-electrolyte interface will surely increase the roughness and somehow reduce the adhesion of HAp-based coatings. In addition, some undesired add products such as octacalcium phosphate (OCP) and dicalcium phosphate dehydrate (DCPD) might be also be present in HAp-based coatings. Probably, it is essential to control precisely the major factors that affect directly the growth process such as sweeping potential range, content of carbonaceous nanomaterial, and temperature.

Reactions occurred during electrodeposition of HAp onto the electrode surface. Note the potentials at which these reactions occur in this scheme:

3.1.2. Effect of Potential Range

Figure 1 presents the electrodeposition of HAp-MWCNTs_0.5 coatings onto Ti6Al4V using cyclic voltammetry technique by sweeping from 0 V to −2.1 V (vs. SCE) at a scan rate of 5 mV·s⁻¹, number of scans of 5, and temperature of 45°C. It can be seen from Figure 1 that the current density is kept nearly constant at less negative potentials (0V to −1.2 V) and then starts to change at around −1.2 V and finally increases rapidly [23, 24]. This is an important evidence on the formation of localized OH⁻ ions that will facilitate the growth of HAp-based materials on the electrode surfaces.

In fact, the current density is one of the most important factors that determine the thickness of the electrodeposited layer [25]. Herein, we have investigated the growth kinetics of HAp-MWCNTs_0.5 coatings by sweeping in 5 scans and stopping at different potentials ranging from −1.4 V to −2.1 V with an interval of 0.1 V. All preliminary observations on thickness, mass, and adhesion of the HAp-MWCNTs_0.5 coatings with different potential ranges are provided in Table 1. At very low current densities of only −2.4 mA ·cm⁻² (stopped potential of −1.4 V) and −4.5 mA·cm⁻² (stopped potential of −1.5 V), the growth of HAp-MWCNTs_0.5 was strictly limited. Obviously, thicker coatings were obtained with increasing current density. A very thick coating with thickness of 7 μm and mass density of 2.33 mg·cm⁻² was obtained at the highest current density of −35 mA ·cm⁻² (stopped potential of −2.1 V). In general, these HAp-MWCNTs_0.5 coatings might be qualified for further biomedical applications in terms of the thickness (several micrometers). Unfortunately, the adhesion of HAp-MWCNTs_0.5 coatings onto the substrate was found to be declined with their thickness. This value was slightly decreased from 12.2 MPa to 10.4 MPa as increasing the coating thickness from 4.0 to 6.3 μm and then suddenly dropped to 7.6 MPa at the thickness of 7 μm. The evolution of hydrogen bubbles during water electrolysis at negative potentials is responsible for the low adhesion of the coatings [26, 27]. The HAp-MWCNTs_0.5 coating obtained at a sweeping range from 0 V to −2.0 V with considerable thickness (6.3 μm) and acceptable adhesion (10.4 MPa) seems to be the most suitable for further applications. Therefore, the stopped potential for cyclic electrodeposition will be chosen to be −2.0 V for all further experiments.

The structural behaviors of HAp-MWCNTs_0.5 coatings deposited at different potential ranges were examined by FTIR and XRD techniques. Figure 2(a) presents the FT-IRR spectrum of MWCNTs-COOH with the characteristic peak of the -COOH group observed at 1735 cm⁻¹ and 1380 cm⁻¹ which was characterized for C = O and C-OH bindings. Bands in the range 1630 cm⁻¹ are characteristic for carbonaceous materials and are most often associated with the occurrence of the C-C stretching bonds characteristic to the expected nanotube phonon modes. FTIR spectrum of HAp-MWCNTs shows characteristic vibration modes of HAp (1030, 610, and 560 cm⁻¹, −PO₄) and MWCNTs-COOH (3430–3440 cm⁻¹, stretching, -OH; and 1630 cm⁻¹, C-C stretching) (Figure 2(c)). The spectral shoulder of C = O at the wavenumber of 1735 cm⁻¹ was not observed due to its small intensity. In addition, the position of the stretching vibration mode -OH in the carboxylic group of MWCNTs (1380 cm⁻¹) was found to be red-shifted by 20 cm⁻¹ (at 1360 cm⁻¹), indicating the formation of hydrogen bonds between calcium ions in the HAp and carboxylic groups of MWCNTs [13, 28, 29]. It means that HAp and MWCNTs have surely been codeposited onto the substrate. XRD patterns (Figure 3) have also confirmed the presence of HAp (JCPDS 09-432) and MWCNT (JCPDS 01-075-1621) materials in all samples. It must be noted that the diffraction peak at 2θ = 25.8° of HAp and diffraction peak at 2θ = 26° of MWCNTs are superpositioned. Remarkably, some diffraction peaks (2θ∼29°, 43°, and 51°) relevant to dicalcium phosphate dihydrate (DCDP, CaHPO₄.2H₂O) were also found at low current densities (stopped potentials −1.6 V and −1.7 V). This might be resulted from low concentration of hydroxyl groups at the electrode surface which is not enough to convert completely HPO₄²⁻ ions to PO₄³⁻ during HAp deposition. Again, these results have firmly confirmed that the stopped potential of −2.0 V is the best choice for the electrodeposition of HAp-MWCNT coatings.

FE-SEM images of HAp-MWCNTs_0.5 coatings obtained at different potential ranges are given in Figure 4. As seen from Figure 4, the Ti6Al4V substrate was fully covered by microporous HAp-MWCNTs_0.5 material. The porosity of the coatings was found to be increased with increasing applied current density. Probably, the occurrence of hydrogen gas at the electrolyte-electrode interface is responsible for such a high porosity accompanying with low adhesion of the coatings.

(a)

(b)

(c)

3.1.3. Effect of the MWCNTs-COOH Content

Figure 5 shows the polarization curves of the Ti6Al4V electrode sweeping in the electrolyte containing different amount of MWCNTs-COOH (0-1 g·L⁻¹) between 0 and − 2V (vs. SCE) at 45°C and scan rate of 5 mV·s⁻¹. Clearly, the cathodic current density was increased with increasing MWCNT amount due to the high conductivity of this carbonaceous material. FTIR spectra (Figure 6) and XRD patterns (Figure 7) of HAp-MWCNT coatings with different amounts of MWCNTs (0-1 g·L⁻¹) have shown structural characteristics of pure HAp and MWCNTs. No add products (neither OCP nor DCPD) were observed.

The mass, thickness, and adhesion of these HAp-MWCNT coatings are given in Table 2. As seen from Table 2, the thickness and mass of HAp-based coatings are decreased while adding MWCNTs-COOH into the deposition solution. MWCNT material with long tubes and voluminous molecular structure might have prevented the formation of HAp-MWCNT coatings on the surface of Ti6Al4V. Remarkably, the growth of HAp-MWCNTs is seriously limited at carbonaceous content of more than 0.5 g·L⁻¹. Nevertheless, the adhesion of HAp-based coatings is found to be improved significantly in presence of MWCNTs and is the strongest (10.4 MPa) at MWCNT concentration of 0.5 g·L⁻¹. The obtained coatings were tighter in the cases of the presence of MWCNTs because of the formation of hydrogen bonds between -COOH groups of MWCNTs and -OH groups of HAp. But, the high amount of MWCNTs in the electrolyte (0.75 g/L or 1.0 g/L) was the cause of agglomeration of MWCNTs-COOH in the coatings, leading to a strong decrease in adhesion strength. Therefore, 0.5 g·L⁻¹ MWCNTs-COOH was selected for further studies.

3.1.4. Effect of Synthesis Temperature

To investigate the effect of temperature on behaviors of the obtained coatings, the electrodeposited temperature was controlled at 30°C, 45°C, and 60°C. The cathodic polarization curves recorded during electrodeposition of HAp-MWCNTs_0.5 coatings at different temperatures are depicted in Figure 8. When the synthesis temperature increased from 30°C to 60°C, the cathodic current density increased. Probably, the reactions occurring during the growth of HAp-MWCNT coatings have been accelerated by the heat. Obviously, the mass and the thickness of HAp-MWCNTs_0.5 coatings were found to be increasing rapidly with increasing synthesis temperature (Table 3). However, the adhesion of these coatings was decreased strongly and reached 6 MPa at 60°C. The results showed clearly that at high temperature, the reaction rate to form H₂ gas on the surface of the Ti6Al4V electrode increased leading to obtained porous coatings. Therefore, the electrodeposited temperature of 45°C was selected to synthesize HAp-MWCNTs/Ti6Al4V. XRD patterns (Figure 9) have shown only characteristic peaks of HAp and MWCNT materials. The morphology of HAp-MWCNTs films grown in the Ti6Al4V substrate (Figure 10) exhibits coral-like shape at lower temperatures (30 and 45°C) but turn into leaf-like shape with large size at higher temperature (60°C). It is supposed that the high growth speed of the apatite crystal is the main reason for this morphology transition [30].

(a)

(b)

(c)

3.1.5. Effect of Number of Scans

In this section, HAp-MWCNTs_0.5 coatings were synthesized at a potential range of 0 ÷ −2.0 V (vs. SCE), scan rate of 5 mV·s⁻¹, and temperature of 45°C with different number of scans (3, 4, 5, and 6).

XRD pattern confirmed that the phase component of obtained coatings is not affected by number of scans (Figure 11).

The variations of mass, thickness, and adhesion between HAp-MWCNTs_0.5 coatings and substrate are depicted in Table 4. With increasing number of scans, the mass and thickness increased but the adhesion decreased. After 3 scans, a nonhomogeneous HAp-MWCNT_0.5 with low density (0.92 mg/cm²) is formed on the substrate. Consequently, the adhesion strength can be determined in this case. After 4 and 5 scans, the quality of HAp-MWCNT_0.5 films was much improved with lower roughness, higher density, and a complete coverage over the surface of the Ti6Al4V substrate. A better adhesion strength of 10 MPa was also obtained at the number of scans of 5. But up to 6 scans, the adhesion was strongly decreased to 7 MPa since the film now is too thick and porous. In summary, the optimal number of scans was chosen to be 5.

Based on the above results on the effect of the scanning potential range, MWCNTs amount, synthesis temperature, and number of scans, we offer the optimal condition to synthesize the HAp-MWCNT coating on Ti6Al4V by electrodeposition as following: scanning potential range from 0 to −2.0 V/SCE, 5 scans, and scanning rate of 5 mV/s at 45°C in the electrolyte solution containing 0.5 g/L of MWCNTs. HAp-MWCNTs synthesized at this condition have a crystal structure which are composed of phases of HAp and MWCNTs with the thickness of 6.3 μm and the adhesion of 10 MPa. The optimal conditions obtained in this study are not completely similar to the optimal conditions for HAp-MWCNTs on 316L SS in our previous publication [17–19]. It is clear that the study on synthesis of HAp-MWCNT coating on the different substrates is necessary because in implant areas with large tonnage that require a large tonnage such as the leg, femur, and hip, the use of Ti6Al4V materials are necessary.

3.2. Coating Mechanical Properties

The elastic modulus (determined from tensile stress curves) was about 115, 121, and 126 GPa for the bare electrode, HAp, and HAp-MWCNTs_0.5 coating, respectively (Figure 12). Meanwhile, the hardness of HAp-MWCNTs_0.5 coating (6 GPa) is significantly higher than that of HAp coating (5.1 GPa). The improved elasticity and hardness of the HAp-MWCNTs_0.5 coating must be benefited from high mechanical flexibility and strength of carbonaceous material present in the coating.

(a)

(b)

(c)

3.3. Dissolution of the Coatings

The dissolution of HAp and HAp-MWCNTs_0.5 coatings was determined by Ca²⁺ released concentration when these materials were immersed in 0.9% of NaCl solution. The data in Table 5 shows that the dissolution of HAp coating was higher than that of HAp-MWCNTs coating at all immersion times. It means that MWCNTs plays the role in reducing the solubility of the coating because of the formation of hydrogen bonding between MWCNTs and HAp.

4. Conclusions

The HAp-MWCNT coatings were successfully electrodeposited on the surface of Ti6Al4V electrodes. The optimal synthesis conditions were obtained at the stopped potential of −2.0 V/SCE, 5 scans, and 5 m· s⁻¹ at 45°C with the presence of MWCNTs (0.5 g·L⁻¹) in the electrolyte solution. FTIR spectra and XRD patterns have firmly confirmed the presence of HAp and MWCNTs and the absence of add products on the modified electrodes. More importantly, it was found that the presence of MWCNTs has reinforced mechanical behaviors as well as improved the stability of HAp-based coatings. These findings support further applications of HAp-MWCNT nanocomposites in orthopedics in future.

Data Availability

All of the data used to support the findings of this study are included within the article.

Conflicts of Interest

The authors declare that there are no conflicts of interest regarding the publication of this paper.

Acknowledgments

This research was funded by the Institute for Tropical Technology (ITT) and Graduate University of Science and Technology (GUST), Vietnam Academy of Science and Technology.

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Copyright © 2020 Thom T. Nguyen et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

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