# Evaluation of Synthesized Nanohydroxyapatite-Nanocellulose Composites as Biocompatible Scaffolds for Applications in Bone Tissue Engineering

Authors: Claudia S. Herdocia-Lluberes; Simara Laboy-López; Stefannie Morales; Tania J. Gonzalez-Robles; José A. González-Feliciano; Eduardo  Nicolau
Journal: Journal of Nanomaterials
 (2015)

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## Abstract

Basic calcium phosphate (BCP) crystals have been associated with many diseases due to their activation of signaling pathways that lead to their mineralization and deposition in intra-articular and periarticular locations in the bones. In this study, hydroxyapatite (HAp) has been placed in a polysaccharide network as a strategy to minimize this deposition. This research consisted of the evaluation of varying proportions of the polysaccharide network, cellulose nanocrystals (CNCs), and HAp synthesized via a simple sol-gel method. The resulting biocompatible composites were extensively characterized by means of thermogravimetric analysis (TGA), powder X-ray diffraction (XRD), Fourier transform infrared spectroscopy (FT-IR), dynamic light scattering (DLS), zeta potential, and scanning electron microscopy (SEM). It was found that an nHAp = CNC ratio presented greater homogeneity in the size and distribution of the nanoparticles without compromising the crystalline structure. Also, incorporation of bone morphogenetic protein 2 (BMP-2) was performed to evaluate the effects that this interaction would have in the constructs. Finally, the osteoblast cell (hFOB 1.19) viability assay was executed and it showed that all of the materials promoted greater cell proliferation while the nHAp > CNC proportion with the inclusion of the BMP-2 protein was the best composite for the purpose of this study.


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## Body

## 1. Introduction

Advances in Bone Tissue Engineering (BTE) hold promise for the development of new functional coatings for bone regeneration. The integration of novel bionanomaterials that induce bone regeneration can contribute to the field of BTE and help settle the incidence of bone disorders and conditions [1, 2]. BTE has been a field of study of increasing interest over the past few decades and it focuses on alternative treatment options that will ideally eliminate issues of current clinically used treatments with bone implants, such as donor site morbidity, immune rejection, and pathogen transfer. The main goal of this field is to create bone grafts that enhance bone repair and regeneration of damaged tissue, combining body cells with highly porous scaffold bionanomaterials [2]. Scaffolds are structures that bring support to the bone by promoting biocompatibility that enriches with nutrients the existing natural bone; therefore, it must imitate its composition in the best way possible. Scaffolds must be stress-shielding, biocompatible, and porous structures that resemble the bone [3, 4]. The most studied material to replace and regenerate human hard tissue is hydroxyapatite (HAp), an interesting biomaterial with potential to improve the field of medicine and dentistry. Hydroxyapatite (Ca10(PO4)6(OH)2, HAp) is chemically and structurally similar to the inorganic components of bone, enamel, and dentin; it is also bioactive and supports bone ingrowth and osseointegration. Due to these unique features HAp has gained recognition and importance in the field of BTE. It has also been successfully used as bone filler, aesthetic restorative, coating of orthopedic implants, filler of inorganic/polymer composites, and cell-culture carrier, among others [5].Overall, the use of basic calcium phosphate (BCP) crystals, such as HAp, has been associated with many diseases due to their deposition in intra-articular and periarticular locations site [6]. New pathogenic mechanisms for the deposition mechanisms of BCPs suggest that the extracellular inorganic phosphate, inorganic pyrophosphate, and Ca2+ concentrations are critical determinants of mineralization [7, 8]. It has been found that BCP crystals activate three major signaling pathways: crystal endocytosis and intracellular crystal dissolution with subsequent intracellular calcium increase [9]. Therefore, placing the HAp in a polysaccharide network might prevent this cell activation. Additionally, the use of HAp as a coating agent for metallic implants has been discouraged by many scientists because it is limited to non-load-bearing applications due to the disproportion between the different Young modulus of each. This is an undesired effect because it leads to bone density loss and even fracture or disconnection of bone from the implant. It is of our interest that the polysaccharide network could serve as a hardening intermediate between the bone and the implant [10].There are many polysaccharides that have been used for tissue engineering applications such as chitosan and gelatin [11, 12]. A similar material, cellulose nanocrystals (CNCs), has been the subject of study in several applications because it is one of the most abundant biopolymers on earth; it is nontoxic and has a Young modulus of 167.5 GPa comparable to the stiffness of titanium, copper, and bronze materials used in bone implants [13]. CNCs are the ordered crystalline regions of cellulose microfibers (cellulose molecule chains connected through hydrogen bonding with approximately 5–50 nm in diameter) which can be obtained from hydrolysis [14, 15].Due to all of the above, herein we propose to synthesize nanohydroxyapatite (nHAp) − nanocellulose (CNC) composites via the sol-gel route in order to develop uniform molecular-level mixing of the calcium and phosphorus precursors. This strategy might provide several advantages such as improving chemical homogeneity of the resulting HAp, low synthesis temperature, and promotion of controlled growth of spherical nanoparticles [16, 17]. The sol-gel product is recognized by the nanometric dimension of the primary particles that is known to improve the contact reaction and the stability at the artificial/natural bone interface [16, 18]. In the present paper we report the synthesis and characterization of nHAp with the incorporation of CNCs via the sol-gel method and its characterization using different proportions of the bionanomaterials for the creation of scaffolds that will contribute to the field of BTE. Through the evaluation of different proportions of the HAp and CNC it was possible to determine which proportion promoted a better synthesis of nHAp nanoparticles in terms of homogeneity and dispersion. We present the addition of bone morphogenetic protein (BMP-2) to the synthesized composites as it is an important protein involved in the development and regeneration of tissue and cartilage which makes it promising for our purpose [19]. Finally, we present the inclusion of osteoblast cells into the nanoconstructs with BMP-2 in order to determine the biocompatibility of these materials. Nanomaterials have proven to be noncytotoxic in previous studies [20–22].


## 2. Materials and Methods

### 2.1. Materials

Cellulose nanocrystals (CNCs) 11.8% aqueous solution was purchased from the University of Maine Process and Development Center (Orono, USA). Hydroxyapatite (HAp), ethanol, acetic acid, phosphate buffered solution 1x, pH = 7.2 (PBS), and bone morphogenetic protein 2 (BMP-2) were purchased from Sigma-Aldrich. All chemicals and solvents were used as received without further purification. Deionized water (18.3 MW, MilliQ Direct 16) was used at all times.


### 2.2. Synthesis of Hydroxyapatite Nanoparticles with Cellulose Nanocrystals (nHAp-CNC) Composites

In order to compare the effects of polysaccharide to BCD crystals, three composites were prepared with different proportions of HAp and CNC. The three compounds were prepared, following the proportions of Hap > CNC, Hap = CNC, and Hap < CNC. The same ratio of ethanol and acetic acid was used to produce nanohydroxyapatite (nHAp), following a similar procedure to that of Monreal Romero et al. [23]. In brief, 1 mL of 99% chemically pure grade biopolymer β-1,4-D-linked glucose (CNC) at 3.2% wt was placed at 30°C for 30 minutes and added to the solutions of HAp with 5 mL ethanol and 1.25 mL acetic acid for gel formation. The first solution (nHAp > CNC) was prepared using 0.5 g HAp and 9.17 μL CNCs (3.2%), the second solution (nHAp = CNC) consisted of 0.5 g HAp and 458 μL CNCs (3.2%), and the third solution (nHAp < CNC) consisted of 0.01 g HAp and 458 μL CNCs (3.2%); subsequently the solutions were sonicated at 30°C for 15 minutes. After sonication each gel was placed in a 50 mL tube and centrifuged 3 times at 12,500 rpm for 5 minutes at 30°C; in-between the procedure, the concentrated gel was poured off and the precipitate was resuspended twice with deionized water to eliminate any amount of gel residue. The resulting pellet was freeze-dried for 24 hours and stored for further characterization.


### 2.3. Inclusion of BMP-2 to nHAp

For the inclusion of BMP-2 to the composites, 10μg of BMP-2 was diluted in 1000 μL of PBS first. Afterwards, two solutions of 0.01 g of nHAp > CNC and nHAp = CNC were prepared in 900 μL of PBS and 100 μL of the solution containing the BMP-2 was added to each.


### 2.4. Cell Proliferation and Viability Assay

Human osteoblast cell line (hFOB 1.19) was purchased from the American Type Culture Collection (Manassas, VA, USA). Osteoblast cells were cultured in 1 : 1 mixture of Ham’s F12 Medium/Dulbecco’s Modified Eagle’s Medium (Gibco by Life Technologies) supplemented with 2.5 mM L-glutamine, 10% fetal bovine serum (Gibco by Life Technologies), and 0.3 mg/mL G148 (Gibco by Life Technologies) at 34°C with 5% CO2. To assess the cell viability effect of HAp, CNC, Hap > CNC, Hap = CNC, Hap > CNC + BMP-2, and Hap = CNC + BMP-2 nanoparticles, the MTS CellTiter 96 AQueous Solution Cell proliferation Assay (Promega) was used. In brief, cells were plated at 7.5 × 104 cells/mL in 96-well plates (Falcon) in contact with 5 mg/mL of the different nanoconstructs and incubated for 24 hrs. Then, 20 μL of MTS reagent was added and cells were incubated for 1 hr. Thereafter, the 96-well plates were centrifuged at 1000 rpm for 10 min to avoid any further light scattering from the nanomaterials. Then, 100 μL of the supernatant was transferred to a new 96-well plate and absorbance was measured at 490 nm using a Synergy H1 Hybrid Microplate Reader from BioTek. The results were expressed as percentage (%) of cell viability and the statistical analysis was performed with GraphPad Prism 6.


### 2.5. Physical Characterization of nHAp-CNC Composites

In order to fully characterize the composite material, several physical characterization techniques were employed in this study.


#### 2.5.1. Thermogravimetric Analysis (TGA)

A Perkin-Elmer STA 6000 simultaneous thermal analyzer was used to measure the changes in weight and heat flow as a function of temperature. Approximately 10 mg of each sample was added to ceramic crucible and heating of 30–750°C at a ramp of 20°C/min in air atmosphere at a flow rate of 20 mL/min.


#### 2.5.2. X-Ray Diffraction (XRD) Analysis

Powder X-ray diffraction measurements were conducted over 10 to 90° 2θ range using a Rigaku SmartLab diffractometer at 40 kV and 44 mA equipped with monochromatic CuKα (1.54 Å) X-ray radiation. X-ray diffraction patterns of composites were recorded in intervals of 20°C.


#### 2.5.3. Dynamic Light Scattering (DLS) and Z-Potential Analysis

Malvern ZetaSizer Nano Series with 4 mW 632.8 nm laser was used to determine the average diameter of composite suspensions. First, suspensions were sufficiently diluted with deionized water to avoid agglomeration; then approximately 1 mL of suspension was added to a disposable plastic cuvette. The backscattering mode was used in triplicate for all the samples and theZ-average (i.e., hydrodynamic radius) and polydispersity index (PDI) were recorded.


#### 2.5.4. Scanning Electron Microscopy (SEM)

Scanning electron microscopy (SEM) images were recorded using a JEOL 5800LV Scanning Microscope with electron beam energy of 20 kV. The samples were freeze-dried before measurement and, to avoid charge accumulation, a thin film of gold (15 nm) was added to the surface.


#### 2.5.5. Infrared Spectroscopy (FTIR)

Infrared spectra of freeze-dried samples were recorded on a Bruker tensor 27 Fourier transform infrared using Attenuated Total Reflectance (ATR). Sample was placed in a glass slide and then pressed using a diamond probe. The spectral width ranged from 400 to 4000 cm−1, with 4 cm−1 resolution and accumulation of 64 scans.


## 2.1. Materials

Cellulose nanocrystals (CNCs) 11.8% aqueous solution was purchased from the University of Maine Process and Development Center (Orono, USA). Hydroxyapatite (HAp), ethanol, acetic acid, phosphate buffered solution 1x, pH = 7.2 (PBS), and bone morphogenetic protein 2 (BMP-2) were purchased from Sigma-Aldrich. All chemicals and solvents were used as received without further purification. Deionized water (18.3 MW, MilliQ Direct 16) was used at all times.


## 2.2. Synthesis of Hydroxyapatite Nanoparticles with Cellulose Nanocrystals (nHAp-CNC) Composites

In order to compare the effects of polysaccharide to BCD crystals, three composites were prepared with different proportions of HAp and CNC. The three compounds were prepared, following the proportions of Hap > CNC, Hap = CNC, and Hap < CNC. The same ratio of ethanol and acetic acid was used to produce nanohydroxyapatite (nHAp), following a similar procedure to that of Monreal Romero et al. [23]. In brief, 1 mL of 99% chemically pure grade biopolymer β-1,4-D-linked glucose (CNC) at 3.2% wt was placed at 30°C for 30 minutes and added to the solutions of HAp with 5 mL ethanol and 1.25 mL acetic acid for gel formation. The first solution (nHAp > CNC) was prepared using 0.5 g HAp and 9.17 μL CNCs (3.2%), the second solution (nHAp = CNC) consisted of 0.5 g HAp and 458 μL CNCs (3.2%), and the third solution (nHAp < CNC) consisted of 0.01 g HAp and 458 μL CNCs (3.2%); subsequently the solutions were sonicated at 30°C for 15 minutes. After sonication each gel was placed in a 50 mL tube and centrifuged 3 times at 12,500 rpm for 5 minutes at 30°C; in-between the procedure, the concentrated gel was poured off and the precipitate was resuspended twice with deionized water to eliminate any amount of gel residue. The resulting pellet was freeze-dried for 24 hours and stored for further characterization.


## 2.3. Inclusion of BMP-2 to nHAp

For the inclusion of BMP-2 to the composites, 10μg of BMP-2 was diluted in 1000 μL of PBS first. Afterwards, two solutions of 0.01 g of nHAp > CNC and nHAp = CNC were prepared in 900 μL of PBS and 100 μL of the solution containing the BMP-2 was added to each.


## 2.4. Cell Proliferation and Viability Assay

Human osteoblast cell line (hFOB 1.19) was purchased from the American Type Culture Collection (Manassas, VA, USA). Osteoblast cells were cultured in 1 : 1 mixture of Ham’s F12 Medium/Dulbecco’s Modified Eagle’s Medium (Gibco by Life Technologies) supplemented with 2.5 mM L-glutamine, 10% fetal bovine serum (Gibco by Life Technologies), and 0.3 mg/mL G148 (Gibco by Life Technologies) at 34°C with 5% CO2. To assess the cell viability effect of HAp, CNC, Hap > CNC, Hap = CNC, Hap > CNC + BMP-2, and Hap = CNC + BMP-2 nanoparticles, the MTS CellTiter 96 AQueous Solution Cell proliferation Assay (Promega) was used. In brief, cells were plated at 7.5 × 104 cells/mL in 96-well plates (Falcon) in contact with 5 mg/mL of the different nanoconstructs and incubated for 24 hrs. Then, 20 μL of MTS reagent was added and cells were incubated for 1 hr. Thereafter, the 96-well plates were centrifuged at 1000 rpm for 10 min to avoid any further light scattering from the nanomaterials. Then, 100 μL of the supernatant was transferred to a new 96-well plate and absorbance was measured at 490 nm using a Synergy H1 Hybrid Microplate Reader from BioTek. The results were expressed as percentage (%) of cell viability and the statistical analysis was performed with GraphPad Prism 6.


## 2.5. Physical Characterization of nHAp-CNC Composites

In order to fully characterize the composite material, several physical characterization techniques were employed in this study.


### 2.5.1. Thermogravimetric Analysis (TGA)

A Perkin-Elmer STA 6000 simultaneous thermal analyzer was used to measure the changes in weight and heat flow as a function of temperature. Approximately 10 mg of each sample was added to ceramic crucible and heating of 30–750°C at a ramp of 20°C/min in air atmosphere at a flow rate of 20 mL/min.


### 2.5.2. X-Ray Diffraction (XRD) Analysis

Powder X-ray diffraction measurements were conducted over 10 to 90° 2θ range using a Rigaku SmartLab diffractometer at 40 kV and 44 mA equipped with monochromatic CuKα (1.54 Å) X-ray radiation. X-ray diffraction patterns of composites were recorded in intervals of 20°C.


### 2.5.3. Dynamic Light Scattering (DLS) and Z-Potential Analysis

Malvern ZetaSizer Nano Series with 4 mW 632.8 nm laser was used to determine the average diameter of composite suspensions. First, suspensions were sufficiently diluted with deionized water to avoid agglomeration; then approximately 1 mL of suspension was added to a disposable plastic cuvette. The backscattering mode was used in triplicate for all the samples and theZ-average (i.e., hydrodynamic radius) and polydispersity index (PDI) were recorded.


### 2.5.4. Scanning Electron Microscopy (SEM)

Scanning electron microscopy (SEM) images were recorded using a JEOL 5800LV Scanning Microscope with electron beam energy of 20 kV. The samples were freeze-dried before measurement and, to avoid charge accumulation, a thin film of gold (15 nm) was added to the surface.


### 2.5.5. Infrared Spectroscopy (FTIR)

Infrared spectra of freeze-dried samples were recorded on a Bruker tensor 27 Fourier transform infrared using Attenuated Total Reflectance (ATR). Sample was placed in a glass slide and then pressed using a diamond probe. The spectral width ranged from 400 to 4000 cm−1, with 4 cm−1 resolution and accumulation of 64 scans.


## 2.5.1. Thermogravimetric Analysis (TGA)

A Perkin-Elmer STA 6000 simultaneous thermal analyzer was used to measure the changes in weight and heat flow as a function of temperature. Approximately 10 mg of each sample was added to ceramic crucible and heating of 30–750°C at a ramp of 20°C/min in air atmosphere at a flow rate of 20 mL/min.


## 2.5.2. X-Ray Diffraction (XRD) Analysis

Powder X-ray diffraction measurements were conducted over 10 to 90° 2θ range using a Rigaku SmartLab diffractometer at 40 kV and 44 mA equipped with monochromatic CuKα (1.54 Å) X-ray radiation. X-ray diffraction patterns of composites were recorded in intervals of 20°C.


## 2.5.3. Dynamic Light Scattering (DLS) and Z-Potential Analysis

Malvern ZetaSizer Nano Series with 4 mW 632.8 nm laser was used to determine the average diameter of composite suspensions. First, suspensions were sufficiently diluted with deionized water to avoid agglomeration; then approximately 1 mL of suspension was added to a disposable plastic cuvette. The backscattering mode was used in triplicate for all the samples and theZ-average (i.e., hydrodynamic radius) and polydispersity index (PDI) were recorded.


## 2.5.4. Scanning Electron Microscopy (SEM)

Scanning electron microscopy (SEM) images were recorded using a JEOL 5800LV Scanning Microscope with electron beam energy of 20 kV. The samples were freeze-dried before measurement and, to avoid charge accumulation, a thin film of gold (15 nm) was added to the surface.


## 2.5.5. Infrared Spectroscopy (FTIR)

Infrared spectra of freeze-dried samples were recorded on a Bruker tensor 27 Fourier transform infrared using Attenuated Total Reflectance (ATR). Sample was placed in a glass slide and then pressed using a diamond probe. The spectral width ranged from 400 to 4000 cm−1, with 4 cm−1 resolution and accumulation of 64 scans.


## 3. Results and Discussion

### 3.1. Physical Characterization

The main objective of this work was to prepare and characterize biocompatible constructs for Bone Tissue Engineering and repair. Nevertheless, it was of interest to extensively characterize the prepared materials to account for any structural or chemical changes in the products. In this sense, thermal stability of the material provides an indication of the interactions between particles and also about the critical transition temperatures in the material. In order to determine this, a dual thermal gravimetric analyzer with differential scanning calorimetry functions was utilized and results are shown in Figure1. This figure shows the weight loss (straight lines) and heat flow (dotted lines) of the different nHAp-CNC constructs. From these results, a temperature drop atca. 300°C was consistently observed and is ascribed to the thermal decomposition of the CNC while the nHAp decomposition transition was not observed as it belongs to a region of approximately 1080°C, although some mass loss is present. The decomposition of nHAp occurs in three steps: (1) the appearance of Ca10(PO4)6OxOH2-2x as a transition product for the (2) dehydroxylation producing oxyapatite Ca10(PO4)6O ending with (3) decomposition of this oxyapatite and resulting calcium phosphates [24]. The mass losses belonging to the first two steps can be observed at around 400°C and 600°C, respectively, for each sample. The nHAp > CNC sample (red) is the most stable of all, maybe due to the higher proportion of Hap, followed by the nHAp = CNC (black) with a well-defined transition belonging to the CNC and nHAP. Lastly, the nHAp < CNC sample (blue) shows less thermal stability due to a lower amount of CNC in the sample in comparison to the nHAp with a higher change in mass loss at 300°C belonging to the CNC. Also, in this sample a transition atca. 450°C ascribed to the mass loss from the first step of the decomposition of nHAp appears to be more significant. This behavior may be due to the expected stronger interaction between nHAp and CNC that will ultimately cause heat dissipation in order to reach the transition product. The heat flow results also evidence the evaporation of remaining water in the samples. The transitions ascribed to the water removal are not very noticeable in the gravimetric results atca. 130°C. These results suggest a correlation between the ratio of nHAp and the thermal stability. It is noticeable that the samples with higher hydroxyapatite content provide better thermal stability as it was expected due to the degradation temperature of nHAp being much higher than that of CNC.Figure 1
TGA and DSC analysis of nHAp > CNC (red), nHAp = CNC (black), and nHAp < CNC (blue), in air atmosphere at 20 mL/min and a ramp of 20°C/min.After observing the variations in thermal stability of the constructs, it was important to determine if any crystallinity loss is observed for the prepared materials. In order to assess this, XRD was carried out and the resulting patterns are shown in Figure2. The CNC peaks can be observed between 10° and 25° with characteristic phases of (110) at 17° and (200) at 26°; a zoomed version of this area can be observed in Figure 3 [25, 26]. The nHAp characteristic phases are observed at 32°, 39°, and 49° with peaks corresponding to the phases of (311), (410), and (313), respectively (COD ID 2300273) [26]. As a qualitative observation, the intensity of the CNC peaks is much lower than those of the nHAp due to the high crystallinity of nHAp in comparison to CNC, but this does not mean that the CNC loses crystallinity. As can be observed, all diffraction patterns showed the same behavior leading to the conclusion that the crystallinity of the sample was not compromised after sol-gel reaction with polysaccharide network. It is important to note that as the crystallinity of the cellulose decreases, the level of water absorption and biodegradability increases because with decreasing crystallinity cellulose fibers get more disorganized and hence more susceptible to degradation processes [27]. Because of this, the CNC in the synthesized composite will not degrade which sustains the initial purpose of using CNC that can serve as a hardening agent due to its high Young’s modulus and reinforcing the strength of the bone. It is also possible that this polymer network formed by cellulose may prevent the mineralization of HAp and deposition in the intra-articular and periarticular locations.Figure 2
Powder XRD analysis of nHAp > CNC (red), nHAp = CNC (black), and nHAp < CNC (blue).Figure 3
Powder XRD analysis of CNC phase in nHAp > CNC (red), nHAp = CNC (black), and nHAp < CNC (blue).Moreover, even when the crystallinity of the samples was conserved, it was of our interest to determine any chemical changes in the surface of the composites after the synthesis. FTIR was carried out from 400 to 4000 cm−1 (Figure 4) and the presence of CNC is confirmed by the band at around 3400 cm−1 due to OH-stretching, the band at 1640 cm−1 likely due to the OH-bending vibration of adsorbed water, and the band at 2889 cm−1 assigned to C-H aliphatic stretching. Other noticeable bands from C-O-C (ether) at 1200 cm−1 and CH2 (alkaline) at 692 cm−1 are also worth noting. It is important to observe that even though nHAp is an ionic compound, its anions (PO42-) are present at 1020 cm−1 and 559 cm−1. The peaks around 2000 cm−1 are attributed to the presence of CO2 in the samples, so these were discarded for the analysis of the spectrum. The effect of proportion is clearly visible, especially in nHAp < CNC, in the intensity of the graphs.Figure 4
FTIR analysis of nHAp > CNC (red), nHAp = CNC (black), and nHAp < CNC (blue).It has been noted that the composite size and homogeneity of the particles can influence the adherence of tissue to the host implant. As a strategy to account for the composite size, DLS analyses were conducted and are shown in Table1. First, the size for natural HAp and CNC was determined and then the analysis of the particle size and distribution for the composites was carried out. As can be observed for the Z-average (RH) results, most particles fluctuated between 289 and 311 nm. The results showed that the sizes for the nanoparticles were 311 nm for the nHAP > CNC, 289 nm for the nHAp = CNC, and 307 nm for the nHAp < CNC composites. The polydispersive index (PDI) for the nHAP > CNC and nHAp = CNC samples was the lowest with a value of 0.21 which indicates a good size uniformity of the particles, a factor that is notably missing in the nHAp < CNC. The average reduction of particle size from starting natural HAp with an average size of 2061 nm is approximately 85.7%, which proves that the polymer network was a determining factor in this size reduction; a representation of this interaction can be observed in Scheme 1. To further verify this, SEM was carried out to correlate the size and homogeneity of the composites and is presented in Figure 5. From these images it can be observed that the nHAp > CNC sample presents a high porosity while the nHAp = CNC showed a better uniformity in the spherical shape, distribution, and particle size and the nHAp < CNC showed neither of these. Also, in agreement with DLS, the sizes of the particles are between 150 and 300 nm with few particles whose size is over 300 nm. The presence of submicron particles is attributed to the aggregation factor that occurs when the solution is in suspension; nevertheless the formation of smaller nanoparticles is present. DLS was also carried out for the BMP-2 protein alone and with its incorporation to the composites, a representation of this interaction can be observed in Scheme 2. The BMP-2 size was found to be 59.97 nm and for the nHAp < CNC and nHAp = CNC composites with the protein, it was observed that the size of the nanoparticles remained around 349 nm which is still in the range of our composites without the protein with a PDI of 0.24 (Table 2). These results in fact corroborate that the sol-gel method followed by Monreal Romero et al. is, in fact, effective for these types of materials [23].Table 1
DLS analyses for HAp, CNC, and nHAp-CNC at a 1% w/v.
Sample∗
Z-average (nm)
PDI
nHAp > CNC (3.2%)
311 ± 7
0.21 ± 0.02
nHAp = CNC (3.2%)
289 ± 3
0.21 ± 0.01
nHAp < CNC (3.2%)
307 ± 5
0.43 ± 0.00
Natural HAp
1965 ± 170
0.29 ± 0.04
CNC
142.3 ± 0.72
0.30 ± .007
∗All samples at H2O (10 mg/mL) at pH = 7.07.Table 2
DLS analyses for BMP-2, nHAp > CNC, and nHAp = CNC composites with protein at 1% w/v.
Sample∗
Z-average (nm)
PDI
nHAp > CNC (3.2%) + BMP-2
333.4 ± 11
0.18 ± 0.01
nHAp = CNC (3.2%) + BMP-2
364.6 ± 2
0.30 ± 0.02
BMP-2
59.97 ± 0.9
0.46 ± 0.04
∗All samples in PBS at pH = 7.20.Scheme 1
Representation of the interaction between nanohydroxyapatite (nHAp) and cellulose nanocrystals (CNCs) polymer network.Scheme 2
Representation of the interaction between the nHAp/CNC nanocomposites with the BMP-2.Figure 5
SEM analyses of nHAp > CNC (a and b), nHAp = CNC (c and d), and nHAp < CNC (e and f).
(a)
(b)
(c)
(d)
(e)
(f)After thorough characterization of the composites,Z-potential was performed in order to determine the overall charge of the nHAp > CNC and nHAp = CNC composites with and without the BMP-2 (Table 3). The analyses were run in PBS in order to understand how the composites would behave under physiological conditions. The overall charge of the HAp alone was found to have an average charge of −19.36 mV. The isoelectric point of the BMP-2 is 8.5 and therefore below this value the BMP-2 will be positively charged [28]. When the Z-potential measurement was performed with the protein alone, the charge was −12.8 mV, which indicates that there is in fact an interaction occurring between the protein and composite. A recent study about thermodynamics studies on the BMP-2 adsorption onto different hydroxyapatite surfaces conducted by Lu and team has reported that the process of adsorption is by physisorption where the initial driving force is governed by an electrostatic interaction between HAp (negatively charged at pH = 7.2) and BMP-2 (positively charged at pH = 7.2). They report that this process has a positive ΔH corresponding to an endothermic process and negative ΔG corresponding to a spontaneous and energetically favored process [29]. The composites alone had an average charge of −11.4 and −18.1 mV for the nHAp > CNC and nHAp = CNC, respectively, and the charges with the BMP-2 were lowered to −11.0 and −17.3 mV, respectively. Several studies have already shown that the incorporation of BMP-2 results in an initial burst release followed by a stable sustained release of the protein [30]. This slight decrease in the overall charge suggests that there is in fact an interaction between the composites and the protein although this does not provide any inquiry over the stability of the construct.Table 3
Zeta potential measurements of nHAp > CNC and nHAp = CNC with BMP-2.
Sample
Zeta potential (mV)
Natural HAp
−20 ± 2
BMP-2
−11.4 ± 0.7
nHAp > CNC
−18 ± 1
nHAp = CNC
−11.0 ± 0.6
nHAp > CNC & BMP-2
−17.3 ± 0.6
nHAp = CNC & BMP-2
−20 ± 2
∗All samples at 1 mg/mL in PBS solvent at pH = 7.2.


### 3.2. Biocompatibility of Nanocomposites with Osteoblast Cells

In recent years, a great interest has been dedicated to the development of biocompatible and nontoxic nanoparticles that can be used in bone implants and biomedical devices. For instance, studies with carbon nanotubes have been shown to support the osteoblastic cells grow. However, the hydrophobic nature of carbon nanotubes requires extensive functionalization with hydrophilic conjugates in order to afford its biocompatibility [31]. Here in this study we used biocompatible nanohydroxyapatite/nanocellulose composites. To examine the effect in cell viability of such nanoconstructs, osteoblasts cells were exposed to 5 mg/mL of nHAp, CNC, nHAp > CNC, nHAp = CNC, nHAp > CNC + BMP-2, and nHAp = CNC + BMP-2 nanoparticles for 24 hrs. Then, cell viability was measured by MTS assay. The results for these experiments are shown in Figure 6 and it demonstrates that neither of the compounds compromised the osteoblast cell viability. As can be noted, the nHAp > CNC + BMP-2 composite had the highest growth of osteoblast in comparison to the others. This result was expected given the fact that one of the reasons HAp was chosen is because of its high porosity in which the pore size of these scaffolds as long as it is equal to or bigger than 20 μm will permit the growth of cells [32].Figure 6
Cell viability in human osteoblasts exposed to the different nanoconstructs. The cells were exposed to 1 mg/mL of HAp, CNC, Hap > CNC, HAP = CNC, Hap > CNC + BMP-2, and HAP = CNC + BMP-2 nanoconstructs for 24 h and cell viability was determined with the MTS reduction assay. Values represent mean ± standard error of the mean (SEM) from three replicates. An asterisk indicates statistical significance in comparison with the untreated samples (p<0.05).Recent studies have shown that the use of hydroxyapatite- (HA-) 2,2,6,6-tetramethylpiperidine-1-oxyl- (TEMPO-) oxidized bacterial cellulose- (TOBC-) GEL composites in calvarial osteoblasts from Sprague-Dawley rats did not compromise the cell viability and promote cell proliferation [33]. Furthermore, other studies have demonstrated that poly-L-lactide acid (PLLA)/HA/cellulose composites did not affect the cell viability of rat osteosarcoma cells (URM-106) [34]. In this study we showed that the use of nHAp > CNC with BMP-2, which is an important protein that regulates osteoblast differentiation, promotes the growth of human fetal osteoblast cells (Figure 6). Taken together, these results might suggest that cellulose nanocomposites with the addition of proteins that are important for osteoblast growth and differentiation such as BMP-2 are suitable for biomedical applications in the field of Bone Tissue Engineering.


## 3.1. Physical Characterization

The main objective of this work was to prepare and characterize biocompatible constructs for Bone Tissue Engineering and repair. Nevertheless, it was of interest to extensively characterize the prepared materials to account for any structural or chemical changes in the products. In this sense, thermal stability of the material provides an indication of the interactions between particles and also about the critical transition temperatures in the material. In order to determine this, a dual thermal gravimetric analyzer with differential scanning calorimetry functions was utilized and results are shown in Figure1. This figure shows the weight loss (straight lines) and heat flow (dotted lines) of the different nHAp-CNC constructs. From these results, a temperature drop atca. 300°C was consistently observed and is ascribed to the thermal decomposition of the CNC while the nHAp decomposition transition was not observed as it belongs to a region of approximately 1080°C, although some mass loss is present. The decomposition of nHAp occurs in three steps: (1) the appearance of Ca10(PO4)6OxOH2-2x as a transition product for the (2) dehydroxylation producing oxyapatite Ca10(PO4)6O ending with (3) decomposition of this oxyapatite and resulting calcium phosphates [24]. The mass losses belonging to the first two steps can be observed at around 400°C and 600°C, respectively, for each sample. The nHAp > CNC sample (red) is the most stable of all, maybe due to the higher proportion of Hap, followed by the nHAp = CNC (black) with a well-defined transition belonging to the CNC and nHAP. Lastly, the nHAp < CNC sample (blue) shows less thermal stability due to a lower amount of CNC in the sample in comparison to the nHAp with a higher change in mass loss at 300°C belonging to the CNC. Also, in this sample a transition atca. 450°C ascribed to the mass loss from the first step of the decomposition of nHAp appears to be more significant. This behavior may be due to the expected stronger interaction between nHAp and CNC that will ultimately cause heat dissipation in order to reach the transition product. The heat flow results also evidence the evaporation of remaining water in the samples. The transitions ascribed to the water removal are not very noticeable in the gravimetric results atca. 130°C. These results suggest a correlation between the ratio of nHAp and the thermal stability. It is noticeable that the samples with higher hydroxyapatite content provide better thermal stability as it was expected due to the degradation temperature of nHAp being much higher than that of CNC.Figure 1
TGA and DSC analysis of nHAp > CNC (red), nHAp = CNC (black), and nHAp < CNC (blue), in air atmosphere at 20 mL/min and a ramp of 20°C/min.After observing the variations in thermal stability of the constructs, it was important to determine if any crystallinity loss is observed for the prepared materials. In order to assess this, XRD was carried out and the resulting patterns are shown in Figure2. The CNC peaks can be observed between 10° and 25° with characteristic phases of (110) at 17° and (200) at 26°; a zoomed version of this area can be observed in Figure 3 [25, 26]. The nHAp characteristic phases are observed at 32°, 39°, and 49° with peaks corresponding to the phases of (311), (410), and (313), respectively (COD ID 2300273) [26]. As a qualitative observation, the intensity of the CNC peaks is much lower than those of the nHAp due to the high crystallinity of nHAp in comparison to CNC, but this does not mean that the CNC loses crystallinity. As can be observed, all diffraction patterns showed the same behavior leading to the conclusion that the crystallinity of the sample was not compromised after sol-gel reaction with polysaccharide network. It is important to note that as the crystallinity of the cellulose decreases, the level of water absorption and biodegradability increases because with decreasing crystallinity cellulose fibers get more disorganized and hence more susceptible to degradation processes [27]. Because of this, the CNC in the synthesized composite will not degrade which sustains the initial purpose of using CNC that can serve as a hardening agent due to its high Young’s modulus and reinforcing the strength of the bone. It is also possible that this polymer network formed by cellulose may prevent the mineralization of HAp and deposition in the intra-articular and periarticular locations.Figure 2
Powder XRD analysis of nHAp > CNC (red), nHAp = CNC (black), and nHAp < CNC (blue).Figure 3
Powder XRD analysis of CNC phase in nHAp > CNC (red), nHAp = CNC (black), and nHAp < CNC (blue).Moreover, even when the crystallinity of the samples was conserved, it was of our interest to determine any chemical changes in the surface of the composites after the synthesis. FTIR was carried out from 400 to 4000 cm−1 (Figure 4) and the presence of CNC is confirmed by the band at around 3400 cm−1 due to OH-stretching, the band at 1640 cm−1 likely due to the OH-bending vibration of adsorbed water, and the band at 2889 cm−1 assigned to C-H aliphatic stretching. Other noticeable bands from C-O-C (ether) at 1200 cm−1 and CH2 (alkaline) at 692 cm−1 are also worth noting. It is important to observe that even though nHAp is an ionic compound, its anions (PO42-) are present at 1020 cm−1 and 559 cm−1. The peaks around 2000 cm−1 are attributed to the presence of CO2 in the samples, so these were discarded for the analysis of the spectrum. The effect of proportion is clearly visible, especially in nHAp < CNC, in the intensity of the graphs.Figure 4
FTIR analysis of nHAp > CNC (red), nHAp = CNC (black), and nHAp < CNC (blue).It has been noted that the composite size and homogeneity of the particles can influence the adherence of tissue to the host implant. As a strategy to account for the composite size, DLS analyses were conducted and are shown in Table1. First, the size for natural HAp and CNC was determined and then the analysis of the particle size and distribution for the composites was carried out. As can be observed for the Z-average (RH) results, most particles fluctuated between 289 and 311 nm. The results showed that the sizes for the nanoparticles were 311 nm for the nHAP > CNC, 289 nm for the nHAp = CNC, and 307 nm for the nHAp < CNC composites. The polydispersive index (PDI) for the nHAP > CNC and nHAp = CNC samples was the lowest with a value of 0.21 which indicates a good size uniformity of the particles, a factor that is notably missing in the nHAp < CNC. The average reduction of particle size from starting natural HAp with an average size of 2061 nm is approximately 85.7%, which proves that the polymer network was a determining factor in this size reduction; a representation of this interaction can be observed in Scheme 1. To further verify this, SEM was carried out to correlate the size and homogeneity of the composites and is presented in Figure 5. From these images it can be observed that the nHAp > CNC sample presents a high porosity while the nHAp = CNC showed a better uniformity in the spherical shape, distribution, and particle size and the nHAp < CNC showed neither of these. Also, in agreement with DLS, the sizes of the particles are between 150 and 300 nm with few particles whose size is over 300 nm. The presence of submicron particles is attributed to the aggregation factor that occurs when the solution is in suspension; nevertheless the formation of smaller nanoparticles is present. DLS was also carried out for the BMP-2 protein alone and with its incorporation to the composites, a representation of this interaction can be observed in Scheme 2. The BMP-2 size was found to be 59.97 nm and for the nHAp < CNC and nHAp = CNC composites with the protein, it was observed that the size of the nanoparticles remained around 349 nm which is still in the range of our composites without the protein with a PDI of 0.24 (Table 2). These results in fact corroborate that the sol-gel method followed by Monreal Romero et al. is, in fact, effective for these types of materials [23].Table 1
DLS analyses for HAp, CNC, and nHAp-CNC at a 1% w/v.
Sample∗
Z-average (nm)
PDI
nHAp > CNC (3.2%)
311 ± 7
0.21 ± 0.02
nHAp = CNC (3.2%)
289 ± 3
0.21 ± 0.01
nHAp < CNC (3.2%)
307 ± 5
0.43 ± 0.00
Natural HAp
1965 ± 170
0.29 ± 0.04
CNC
142.3 ± 0.72
0.30 ± .007
∗All samples at H2O (10 mg/mL) at pH = 7.07.Table 2
DLS analyses for BMP-2, nHAp > CNC, and nHAp = CNC composites with protein at 1% w/v.
Sample∗
Z-average (nm)
PDI
nHAp > CNC (3.2%) + BMP-2
333.4 ± 11
0.18 ± 0.01
nHAp = CNC (3.2%) + BMP-2
364.6 ± 2
0.30 ± 0.02
BMP-2
59.97 ± 0.9
0.46 ± 0.04
∗All samples in PBS at pH = 7.20.Scheme 1
Representation of the interaction between nanohydroxyapatite (nHAp) and cellulose nanocrystals (CNCs) polymer network.Scheme 2
Representation of the interaction between the nHAp/CNC nanocomposites with the BMP-2.Figure 5
SEM analyses of nHAp > CNC (a and b), nHAp = CNC (c and d), and nHAp < CNC (e and f).
(a)
(b)
(c)
(d)
(e)
(f)After thorough characterization of the composites,Z-potential was performed in order to determine the overall charge of the nHAp > CNC and nHAp = CNC composites with and without the BMP-2 (Table 3). The analyses were run in PBS in order to understand how the composites would behave under physiological conditions. The overall charge of the HAp alone was found to have an average charge of −19.36 mV. The isoelectric point of the BMP-2 is 8.5 and therefore below this value the BMP-2 will be positively charged [28]. When the Z-potential measurement was performed with the protein alone, the charge was −12.8 mV, which indicates that there is in fact an interaction occurring between the protein and composite. A recent study about thermodynamics studies on the BMP-2 adsorption onto different hydroxyapatite surfaces conducted by Lu and team has reported that the process of adsorption is by physisorption where the initial driving force is governed by an electrostatic interaction between HAp (negatively charged at pH = 7.2) and BMP-2 (positively charged at pH = 7.2). They report that this process has a positive ΔH corresponding to an endothermic process and negative ΔG corresponding to a spontaneous and energetically favored process [29]. The composites alone had an average charge of −11.4 and −18.1 mV for the nHAp > CNC and nHAp = CNC, respectively, and the charges with the BMP-2 were lowered to −11.0 and −17.3 mV, respectively. Several studies have already shown that the incorporation of BMP-2 results in an initial burst release followed by a stable sustained release of the protein [30]. This slight decrease in the overall charge suggests that there is in fact an interaction between the composites and the protein although this does not provide any inquiry over the stability of the construct.Table 3
Zeta potential measurements of nHAp > CNC and nHAp = CNC with BMP-2.
Sample
Zeta potential (mV)
Natural HAp
−20 ± 2
BMP-2
−11.4 ± 0.7
nHAp > CNC
−18 ± 1
nHAp = CNC
−11.0 ± 0.6
nHAp > CNC & BMP-2
−17.3 ± 0.6
nHAp = CNC & BMP-2
−20 ± 2
∗All samples at 1 mg/mL in PBS solvent at pH = 7.2.


## 3.2. Biocompatibility of Nanocomposites with Osteoblast Cells

In recent years, a great interest has been dedicated to the development of biocompatible and nontoxic nanoparticles that can be used in bone implants and biomedical devices. For instance, studies with carbon nanotubes have been shown to support the osteoblastic cells grow. However, the hydrophobic nature of carbon nanotubes requires extensive functionalization with hydrophilic conjugates in order to afford its biocompatibility [31]. Here in this study we used biocompatible nanohydroxyapatite/nanocellulose composites. To examine the effect in cell viability of such nanoconstructs, osteoblasts cells were exposed to 5 mg/mL of nHAp, CNC, nHAp > CNC, nHAp = CNC, nHAp > CNC + BMP-2, and nHAp = CNC + BMP-2 nanoparticles for 24 hrs. Then, cell viability was measured by MTS assay. The results for these experiments are shown in Figure 6 and it demonstrates that neither of the compounds compromised the osteoblast cell viability. As can be noted, the nHAp > CNC + BMP-2 composite had the highest growth of osteoblast in comparison to the others. This result was expected given the fact that one of the reasons HAp was chosen is because of its high porosity in which the pore size of these scaffolds as long as it is equal to or bigger than 20 μm will permit the growth of cells [32].Figure 6
Cell viability in human osteoblasts exposed to the different nanoconstructs. The cells were exposed to 1 mg/mL of HAp, CNC, Hap > CNC, HAP = CNC, Hap > CNC + BMP-2, and HAP = CNC + BMP-2 nanoconstructs for 24 h and cell viability was determined with the MTS reduction assay. Values represent mean ± standard error of the mean (SEM) from three replicates. An asterisk indicates statistical significance in comparison with the untreated samples (p<0.05).Recent studies have shown that the use of hydroxyapatite- (HA-) 2,2,6,6-tetramethylpiperidine-1-oxyl- (TEMPO-) oxidized bacterial cellulose- (TOBC-) GEL composites in calvarial osteoblasts from Sprague-Dawley rats did not compromise the cell viability and promote cell proliferation [33]. Furthermore, other studies have demonstrated that poly-L-lactide acid (PLLA)/HA/cellulose composites did not affect the cell viability of rat osteosarcoma cells (URM-106) [34]. In this study we showed that the use of nHAp > CNC with BMP-2, which is an important protein that regulates osteoblast differentiation, promotes the growth of human fetal osteoblast cells (Figure 6). Taken together, these results might suggest that cellulose nanocomposites with the addition of proteins that are important for osteoblast growth and differentiation such as BMP-2 are suitable for biomedical applications in the field of Bone Tissue Engineering.


## 4. Conclusion

The proportion of the nHAp = CNC ratio appeared to be the most suitable ratio for this methodology as it provides homogeneity of the particle’s size and distribution that was shown by the DLS and SEM analyses. We conclude that the CNC did work as expected by the sol-gel method to include HAp in its network without affecting its degree of crystallinity, as shown by the XRD analyses, or the thermal stability as shown by the TGA. Neither of the properties of either CNC or HAp changed due to the chemical interaction between them. The inclusion of BMP-2 does not appear to have a negative effect on the particle size and the charge reduction indicates that there is an interaction between the protein and the composite. The cell proliferation and viability assays demonstrated that all of our composites promoted an increased cell growth, but the nHAp > CNC ratio with BMP-2 had a higher growth percentage than the other composites. Therefore it appears to be the best nanocomposite for the fabrication of scaffolds or bioactive layers that can be used in the Bone Tissue Engineering field.



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*Source: 310935-2015-12-22.xml*