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Journal of Nanomaterials
Volume 2012 (2012), Article ID 213549, 11 pages
Preparation and Properties of Biphasic Calcium Phosphate Scaffolds Multiply Coated with HA/PLLA Nanocomposites for Bone Tissue Engineering Applications
State Key Laboratory of Material Processing and Die and Mould Technology, College of Materials Science and Engineering, Huazhong University of Science & Technology, No. 1037 Luoyu Road, Wuhan 430074, China
Received 9 January 2012; Accepted 30 March 2012
Academic Editor: Tianxi Liu
Copyright © 2012 Lei Nie 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.
A well-developed BCP scaffolds coated with multilayer of HA/PLLA nanocomposites with interconnectivity, high porosity, and moderate compressive strength as well as good biocompatibility were fabricated for bone tissue engineering. After being multiply coated with HA/PLLA nanocomposites, the scaffolds maintained the BCP framework structure, and the porous network structure of scaffolds remained unchanged; however, the compressive strength was increased with the increase of coating layer number of HA/PLLA nanocomposites. The prepared scaffolds showed lower variation of pH values in SBF solution, and an increase of coating layer number led to the decrease of the biodegradation rate at different days. Moreover, the multilayer coating scaffolds had good cytocompatibility, showing no negative effects on cells growth and proliferation. Furthermore, the bone-like apatite layer was built obviously in the interface of scaffold after 21 days after implantation in SD rat muscle. In conclusion, the BCP scaffold coated with multilayer of HA/PLLA nanocomposites could be a candidate as an excellent substitute for damaged or defect bone in bone tissue engineering.
Bone is a living tissue, which continuously rebuilds its structure. Thanks to its capacity of spontaneous regeneration, most lesions, such as fractures, heal well with conventional therapy. However, in case of large defects and osseous congenital deformities, a bone graft or a bone substitute is needed to assist healing . Due to source limitation of the autogenetic bone graft and immunologic rejection problem of the allergenic bone graft , bone tissue engineering technique has become a crucial strategy to permanently repair bone defects. Over the past decade, considerable effort has been focused on fabricating the three-dimensionally interconnected macroporous scaffold to guide bone reconstruction through rapid vascularization, bone growth, and remodeling. In order to allow for optimal osteogenesis and the formation of new bone throughout the scaffolds and the surrounding tissue , 3D scaffolds need to have the appropriate physical, biological, and mechanical properties. These include pore size, pore structure, surface topography, chemical composition, degradation, and mechanical strength. However, from the material point of view, no existing scaffold possesses excellent synergistic properties of high mechanical strength, suitable degradation rate, high porosity, and excellent bioactivity [4–6], which constitutes the main challenge to the use of traditional biomaterials in bone tissue engineering. Thus, the new scaffolding material systems as well as new fabricating techniques are the most important demands in the bone tissue engineering field.
Bioceramics have been widely studied and recognized as the most promising materials for the development of scaffolds for bone regeneration . Biphasic calcium phosphate (BCP) ceramics composed of hydroxyapatite (HA) and β-tricalcium phosphate (β-TCP) have been extensively studied in the past two decades [8, 9]. HA has excellent biocompatibility and bioactivity and can be directly bonded to the host bone , β-TCP has suitable degradation rate that matches the growth rate of newly formed bone , and by combination of the advantages of HA and β-TCP, BCP ceramics have been recently developed as an excellent starting material to prepare the bone tissue engineering scaffold. Moreover, BCP ceramics showed excellent osteoinductivity, osteoconductivity, bioactivity, and biodegradability  according to in vitro physiochemical property examinations and in vivo biological evaluations. However, the inherent brittleness of BCP ceramics makes them unsuitable in load-bearing bone applications . Different methods have been applied to overcome these drawbacks. One of the effective methods for enhancing the mechanical properties and bioactivity of ceramic scaffolds is coating the struts of scaffolds with biocompatible materials, while maintaining the macropores intact and open. The coatings used so far are ceramics, polymers, and micron-composite materials [14–22]. Composites have shown to be more effective for enhancement of both mechanical properties and bioactivity, compared to ceramic and polymers. To the best of the authors’ knowledge, nanocomposite coating layers on the surface of highly porous ceramic scaffolds are yet to be produced. In the present study, nanocomposite coatings consisting of poly-L-Lactide (PLLA) as a polymer matrix and nanohydroxyapatite (HA) as ceramic filler were used to coat the BCP scaffolds [23–29]. Polylactic acid is an FDA-approved biodegradable polymer with remarkable toughness and good biocompatibility. HA is the major mineral component (69% wt.) of human hard tissues. HA promotes faster bone regeneration and direct bonding to regenerated bones without intermediate connective tissues. The incorporation of HA in a polymeric matrix has to overcome processing and dispersion challenges since it is of a great interest to the biomedical community. Sui et al.  fabricated PLLA/HA composite scaffolds via electrospinning and concluded that the cell adhesion and growth on the PLLA/HA composite scaffolds were far better than those on the pure PLLA scaffolds. Jeong et al.  prepared the PLA/HA composite nanofibrous scaffolds and showed that MC3T3-E1 cells maintained viability and proliferated continuously for up to 21 days, suggesting that the PLA/HA composites are effective scaffolds for the growth of osteoblasts. Roohani-Esfahani et al. [32, 33] prepared the biphasic calcium phosphate scaffold coated with HA-PCL composites and found that gaps between inorganic particles and polymer matrix could provide a channel for the penetration of water into polymer led to the pH change in SBF solution and weight loss of scaffolds; however, the mechanical strength of scaffolds was unsatisfactory for load-bearing bone. In this study, we fabricated highly porous BCP scaffolds using a polymeric reticulate method and multiply coated them with HA/PLLA nanocomposites to improve the mechanical strength. The developed scaffolds were characterized for their mechanical properties and biological degradation and for the efficacy of multilayer coatings in enhancing the bioactivity of the scaffolds.
PVA was obtained from the Shanxi Sanwei Group Co. Ltd. (polymerization ~1799 and degree of hydrolysis ~99%). Diammonium hydrogen phosphate ((NH4)2HPO4) and calcium nitrate tetrahydrate (Ca(NO3)2·4H2O) were obtained from the Sinopharm Chemical Reagent Co. Ltd. Ammonia was obtained from the Wuhan Chemical Reagent Co. Ltd. All the chemical reagents used in this work were in analytical reagent level.
2.2. Fabrication of BCP Nanoparticles and BCP Porous Scaffold
Calcium phosphate-deficient apatite powder was prepared by aqueous precipitation reaction. Briefly, Ca(NO3)2·4H2O (0.4 M) and (NH4)2HPO4 (0.2 M) solutions were added in a three-necked flask by simultaneous drops at room temperature while the pH was adjusted at 11 using buffers; the resultant white color product was washed several times with distilled water to completely remove the buffer. The powder obtained was thermally treated at 1100°C for 1 h, to produce a biphasic calcium phosphate that consisted of about 40% HA and 60% β-TCP. The BCP powder was crushed in a mortar and pestle and classified using stainless steel sieves to provide particles of size <75 μm.
Fully reticulated polyurethane foam was used as a sacrificial template for the replication method. For preparing the slurry, PVA was dissolved in water, the concentration being 0.1 mol/L. Then BCP powder was added to PVA-water solution up to concentration of 30 wt%. PU foam templates were cut to appropriate dimensions, and the surface layer of the sponge was treated in NaOH solution for 30 min to improve the surface layer’s hydrophilicity. After cleaning and drying, the PU sponges were immersed in the BCP slurry and compressed slightly to facilitate its absorption. Excessive slurry was removed by squeezing, and the remaining slurry was subsequently blown with compressed air to obtain a uniform dispersion on the sponge. After drying at 37°C for 48 h, BCP-coated sponges were fired in air in an electric furnace using a 4-stage schedule, which include heating from 25°C to 600°C with a heating rate of 1°C/min, further heating from 600°C to 1200 at 2°C/min, dwelling at 1200°C for 2 h, and finally cooling down to 25°C at the cooling rate of 5°C/min.
2.3. Multilayers of HA/PLLA Nanocomposites Coating on BCP Porous Scaffold
As poly-L-lactide powder (PLLA; Mw = 200,000, Sigma-Aldrich) is insoluble in water, the polymer was first dissolved in 1,4-dioxane at 80°C for 1 h, until complete dissolution. Afterwards, HA nanopowder and purified water were added (dioxane/water = 87/13, HA/PLLA = 3/10) and stirred for 24 h until a homogeneous clear solution was obtained and then sonicated for 1 min just before coating the scaffolds. The prepared BCP scaffolds were cleaned with ethanol dipped into the composite solutions for 1 min, and then excess solution was removed to form a uniform coating. The coated scaffolds were dried for 3 days in an oven at 37°C followed by 1 day in a fume hood. In this way, the BCP scaffolds coated with monolayer were prepared, and the BCP scaffolds coated with multilayers were prepared by repeating the above procedure.
2.4. Physicochemical Characterization of the Prepared Scaffolds
Firstly, the BCP nanoparticles were characterized by FE-scanning electron microscopy (FSEM) (Sirion 200, Holland FE). The cross-section of the porous scaffolds were coated with gold to prevent imaging artifacts from electrical charging. And their morphologies were examined by FEI-scanning electron microscopy (SEM) (Quanta 200, Holland FEI). The pore size was calculated from SEM pictures by selecting five arbitrary areas for measurement. Furthermore, FTIR (VERTEX, Bruker) was used to characterize the presence of specific chemical groups in BCP scaffolds coated with HA/PLLA nanocomposites. FTIR spectra were obtained within the range between 4000 and 500 cm−1 on VERTEX 70 FTIR spectrometer with a resolution of 1 cm−1, using attenuated total reflectance (ATR) technique. In addition, the prepared samples were analyzed by X-ray diffraction (X-Pert PRO, PANalytical B.V.). This instrument works with voltage and current settings of 40 kV and 40 mA, respectively, and uses Cu-Kα radiation (1.540600 Å). For qualitative analysis, XRD diagrams were recorded in the interval at scan speed of 2°/min. The open porosity can be calculated by the liquid displacement method. The scaffold was submerged in a known volume () of ethanol that was not a solvent for the scaffold, and a series of brief evacuation repressurization cycles was conducted to force the liquid into the pores of the scaffold. After these cycles, the volume of the liquid and liquid-impregnated scaffold was . When the liquid-impregnated scaffold was removed, the remaining liquid volume was , and open porosity (p) was calculated as . Besides, the compressive strength was determined by crushing a mm3 scaffold between two flat platens using electromechanical universal testing machine (SANSCMT4503, China) with a ramp rate of 0.5 mm min−1. Five identical specimens for each sample group were used for porosity and the compressive testing.
2.5. Biodegradation in Simulated Body Fluid
The biodegradation of the prepared scaffolds in vitro was investigated by soaking them in SBF solution at 37°C. The SBF solution was prepared according to the procedure described in Table 1 . Cylinder-shaped scaffolds were immersed in SBF solution at 37°C for 1, 5, 10, 15, 20, and 25 days at a solid/liquid ratio of 50 mg/mL. All samples were held in plastic flasks which were sealed to minimize the change in pH and microorganism contamination. The SBF solution was not refreshed during the experiment. After soaking, the samples were filtrated, rinsed with distilled water, and dried at 40°C for 4 days and the final weight of samples carefully measured. The weight loss was calculated according to percentage of initial weight. Five scaffolds were used to measure the weight loss and pH change, and results were expressed as mean ± SD.
2.6. In Vitro Cytotoxicity Testing: MTT Assay
The immortalized rat osteoblastic ROS 17/2.8 cell line (obtained from the Orthopedics Department, Union Hospital, Tongji Medical College of Huazhong University of Science and Technology) was utilized in this study. These cells were incubated in a humidified atmosphere of 5% CO2 at 37°C. Cells were cultured in Dulbecco’s modified Eagle’s medium (DMEM, Invitrogen, Paisley, UK) and supplemented with 10% fetal bovine serum (FBS, Invitrogen, Paisley, UK), 100 mg/mL streptomycin, and 100 U/mL penicillin. The culture medium was changed every alternate day. The cytotoxicity of the prepared was investigated by the MTT (3-[4,5-dimethylthiazol-2-yl]-2,5-diphenyltetrazolium bromide) assay which was used to assess cell proliferation by measuring mitochondrial succinate dehydrogenase activity. The samples were fixed in each bottom of a 24-well cell culture plate and were sterilized with ethylene oxide (ETO) steam for 24 h at room temperature; then 1 mL cell suspension was seeded evenly onto each sample. The culture medium was changed by fresh medium every 2 days. After seeding for 1, 3, and 5 days, 100 μL of MTT (5 mg/mL) solution was added to each well and incubated at 37°C for 4 h to allow the formation of formazan crystals; respectively, after removing supernatants, 650 μL of dimethyl sulfoxide (DMSO) was added to each well for dissolving the blue formazan crystal; then the solution was transferred to 96-well plates. The absorbance of each well was measured at 570 nm using an ELISA microplate reader (Bio-Rad). The cells without scaffold were served as the negative control in this study. A mean value was obtained from the measurement of four test runs. The results were statistically analyzed to express the mean 5 the standard deviation (SD) of the mean.
2.7. In Vivo Experiment: Muscle Implantation
Ten healthy Sprague-Dawley (SD) rats of 200 g were randomly divided into five groups. The rats were anaesthetized using an intraperitoneal injection of 0.3 wt% pentobarbital sodium. A muscle pouch about 8 mm in length was created along the fiber direction in the thigh muscle of the rat under surgical asepsis condition. After the implantation of one-column sample in the muscle pouch of each animal, the wound was closed with suture and disinfection. Penicillin was injected in the following 1 day, and the stitches were taken out in 7 days after implantation. The animals were observed to affirm whether there existed any wound injection and abnormal reaction. Two rats were executed by breaking the neck at consecutive time period of 1, 7, 14, 21, and 28 days, respectively, and the related tissues were separated and retrieved. Then samples were fixed with 10% neutral formalin, undecalcified sectioned, HE (hematoxylin and eosin) stained and analyzed histologically under optic microscope.
2.8. Statistical Analysis
All the statistical data are expressed as the mean ± SD and were obtained from at least five independent experiments. For statistical analysis, first Levene’s test was performed to determine the homogeneity of variance for all the data, and then, the Tamhane post hoc test was performed for the comparison between different groups. PASW statistics program was employed for all statistical analysis, and differences were the data was accepted at a value of <0.05 for 95% confidence.
3. Results and Discussion
3.1. Physical Properties of BCP Nanopowders
The BCP nanopowders properties were investigated by XRD and FSEM analysis in our study. Figure 1(a) shows the distinct high-resolution FSEM morphologies of the BCP nanoparticles prepared in this study. The BCP nanoparticles were agglomerated as spherical form, and the diameter of spherical grain was in the range of 0.5 ~ 1 μm. It was necessary that the stirring hours were long enough in the preparation process of BCP slurry to disperse BCP particles in PVA-water solution uniformly. Existence of nanoparticulate phase in solid ceramic matrix is known as a method of achieving enhanced mechanical strength and toughness of the matrix . It was found that the BCP scaffold was crisp while the prepared BCP particle size was greater than 75 μm. The nanoparticles serve to steer cracks to propagate along the paths of higher toughness. The toughness at grain boundaries is lower than that within grains. The internal stress produced by the nanoparticles at grain boundaries tends to alter the crack propagation path from intergranular to transgranular and thus increases the overall toughness of the material. Furthermore, nanoparticles will also improve sinterability and reduce flaw size . Figure 1(b) shows the XRD pattern of BCP powders treated at 1100°C. The HA and β-TCP peaks were present in prepared BCP samples, the peaks at 2θ = 25.9° (002), 28.2° (102), 29.7° (210), 31.8° (211), 32.3° (112), and 34.6° (202) matching closely with the diffraction peaks of stoichiometric HA (JCPDS no. 9-0432). The peaks of β-TCP appear at 2θ = 22.9° (3 3 −2), 24.2° (3 6 −1), 30.8° (4 3 −4), 34.2° (3 3 −5), and 34.6° (4 2 −1) (JCPDS no. 9-0169). XRD pattern showed that no other impurity was found in the BCP nanopowders. By quantitative analysis for the XRD patterns, it was confirmed that biphasic calcium phosphate that consisted of about 40% HA and 60% β-TCP was acquirable. BCP is more effective in bone repair or regeneration than pure HA or pure β-TCP and has a controllable degradation rate.
3.2. Physicochemical Characterization of the Prepared Scaffolds
The XRD patterns of pure HA and HA/PLLA composite compared to BCP are shown in Figure 2. As presented in Figure 2, the synthetic HA has a poorly crystalline nature with peaks at 2θ = 26° (002), 28.7° (210), 31.8° (211), 32.3° (112), and 34.6° (202) matching closely with the diffraction peaks of stoichiometric HA, which also present in the sintered BCP sample. XRD data show the crystalline structures of PLLA, and the diffraction peaks for PLLA were at 2θ = 17.49° and 19.31° .
The absorption spectrum of the HA/PLLA nanocomposites was shown in Figure 3. The phosphate ions, , were the principal molecular components of BCP contributing to the IR absorbance in the 1200–550 cm−1 regions. The characteristic peaks at 1040 and 1085 cm−1 correspond to the stretching vibration of and at 599 cm−1 to the deformation vibrations of . As with other major components, the characteristics of the OH− bands in HA were identified by observing the broad band from about 3700 to 2500 cm−1. The peak of this band was centered at about 3131 cm−1, which was a typical assignment of the stretching mode of OH− ions. In addition, the two distinct bands were observed at 3571 and 1752 cm−1 which arise from the stretching mode and bending mode of H2O molecules, respectively. Furthermore, the characteristics of carbonyl group and methyl in PLLA were identified by observing the band at 1452 and 1360 cm−1, respectively.
3.3. Scaffold Morphology and Microstructure Analysis
Figure 4 shows the macroporous network morphologies and strut microstructure of the biphasic calcium phosphate scaffolds before (a) and after coating with different multilayer of HA/PLLA nanocomposites ((b) to (f)). The expected 3D interconnected porous structure with open macropores was observed in the SEM pictures, and the pore sizes of open macropores were about 300–600 μm. The average pore size of the macropores of the scaffolds was approximately 450 μm. For BCP scaffold without coating (Figure 4(a)), the pore wall was coarse and the small pores were observed. After coating BCP with HA/PLLA nanocomposites, the scaffolds maintained the BCP framework structure, and the porous network structure of scaffolds remained unchanged. However, the surface morphologies of scaffolds have changed significantly. A uniform coating was found over the surface of BCP, and the crack-like defects as well as microspores in the struts were filled by nanocomposites. After coating BCP scaffold with monolayer of HA/PLLA nanocomposites (Figure 4(b)), the strut of the scaffold showed a smooth surface. As can be seen in Figure 4(c), the cracks on the scaffold surface were observed while BCP coated with two layers of HA/PLLA nanocomposites. Furthermore, the coating layers were observed clearly while the BCP scaffold coated with three layers of nanocomposites, which was most likely attributed to low-hydrophilicity property of HA/PLLA nanocomposites (Figure 4(d)). For BCP scaffolds coated with four layers and five layers of nanocomposites, the interconnected porous structure of scaffolds was influenced by the pore blocking slightly (Figures 4(e) and 4(f)).
3.4. Scaffold Porosity and Compressive Strengths’ Analysis
Figure 5 showed the porosity of the BCP scaffolds coated with different layers of HA/PLLA nanocomposites. The porosity of the scaffold without coating was about 96.8%, and it decreased while the scaffold coated with HA/PLLA nanocomposites. As the layers of HA/PLLA nanocomposites increased from 1 to 5, the porosity of the scaffolds gradually decreased from 94.9% to 84.4%; however, the compressive strength increased from 2.09 to 10.93 MPa (Figure 6). The compressive strength of BCP scaffold without coating was about 0.31 MPa, which was lower than all BCP scaffolds coated with different layers of HA/PLLA nanocomposites. The BCP scaffold without coating presented the ceramic property, and the struts of scaffolds were reinforced by the coating of HA/PLLA nanocomposites. It could be deduced that the coating layer number has strong influence on the porosity and compressive strength of BCP scaffolds. The results illustrated that BCP scaffold coated with three-layer HA/PLLA nanocomposites was appropriate in the BCP matrix when comprehensively considering the requirement of porosity and mechanical strength for tissue engineering scaffold.
3.5. Biodegradation in Simulated Body Fluid
Figure 7 represents the weight loss of the scaffolds soaked in SBF solution after different soaking times. After 28 days of soaking, the weight loss of BCP scaffold without coating was about 26% relative to initial weight and showed a greater weight loss than those scaffolds with coating layers of HA/PLLA nanocomposites. The weight loss of BCP scaffolds coated with multilayer of HA/PLLA nanocomposites were decreased at different soaking times compared to BCP scaffold without coating. And the weight loss decreased with the increase of coating number for prepared scaffolds. The dissolution of BCP nanoparticles in SBF was prevented by the coating of HA/PLLA nanocomposites. The result indicated that the degradation of BCP scaffold could be controlled by the coating layers of HA/PLLA nanocomposites. The graphs of the pH changes in terms of soaking time also illustrate the dissolution behavior of prepared scaffolds as shown in Figure 8. The pH values of SBF without scaffolds were stable throughout the experimental period. The pH values of BCP scaffold without coating in SBF solution exhibited approximately 7.40–7.61, and the lower variation was observed. For BCP scaffolds coated with HA/PLLA nanocomposites, the pH values in SBF solution changed from 6.87 to 7.40, and the lowest pH values in SBF solution decreased with the increase of coating number of HA/PLLA nanocomposites.
3.6. In Vitro Cytotoxicity Analysis
MTT test was usually used for evaluating the cell toxicity of biomaterials. In this study, rat osteoblast cells were cultured on six groups of porous scaffolds for 1, 3, and 5 days; respectively, after treatment of the cell-scaffold constructs with the MTT solution, dark blue crystals of formazan were seen, indicating the presence of metabolically active cells. The MTT absorption was measured at 570 nm with a background subtraction at 630 nm, a higher absorbance indicates that there are either more cells or that they are metabolizing , and the results were presented in Figure 9. The reason for which might be owing to the surface morphologies and excellent bioactivity of BCP [39–41]. The absorbance of BCP scaffolds coated with HA/PLLA nanocomposites was higher compared to the negative group at different days, and the BCP scaffold coated with three-layer coating exhibited highest absorbance. Therefore, the biphasic calcium phosphate scaffolds coated with multilayer of HA/PLLA nanocomposites prepared in this study can be a promising biomaterial for bone tissue regeneration application due to their good biocompatibility.
3.7. In Vivo Experiment Analysis
The BCP scaffolds coated with three layers of HA/PLLA nanocomposites implanted in the thigh muscle of the SD rat. After operation, the implant site did not show any inflammation such as red swelling and effusion in the skin. No adverse reaction of the animal was observed. Histological images of the tissue section of the implanted site are shown in Figure 10. After 1 day, inflammatory cells like neutrophil, eosinophil, lymphocyte, plasma cell, and macrophage were found to be close to the implant-tissue interface compared to the control group in Figures 10(a) and 10(f). After 7 days, the appearance and shape of the implanted material showed no obvious change, and the amount of inflammatory cells decreased rapidly. After 14 days, the slight connection between the material and surrounding tissue was observed, and the number of fibroblasts increased with increasing time. The disappearance of the inflammatory cells was clearly seen, and their amount was low. Mature fibroblasts were found to form a hyperplastic fibrous tissue surrounding the materials in Figure 10(c). After 21 days after implantation, the connection between material and tissue occurred, and there were slight changes in the appearance and shape of the material. A dense, thin fibrous tissue layer was built in the interface. The surface of materials became roughness, and the semitransparent connection fibrous tissue layer in the interface was observed. Furthermore, the bone-like apatite layer was built obviously in the interface of scaffold. After 28 days after implantation, the thickness of bone-like layer was enhanced, and the blood cells were found in Figure 10(e), which means the blood vessels grown into the pores of the materials. Implantation experiment in muscle experiment revealed that BCP scaffolds coated with multilayer of HA/PLLA nanocomposites were clearly nontoxic.
Well-developed BCP scaffolds coated with multilayer of HA/PLLA nanocomposites with interconnectivity, high porosity, and moderate compressive strength as well as good biocompatibility were fabricated for bone tissue engineering. After coated with HA/PLLA nanocomposites, the scaffolds maintained the BCP framework structure, and the porous network structure of scaffolds remained unchanged; however, the compressive strength was increased with the increase of coating layer number of HA/PLLA nanocomposites. The prepared scaffolds showed the lower variation of pH values in SBF solution, and an increase of coating layer number led to the decrease of the biodegradation rate at different days. Moreover, the multilayer coating scaffolds had good cytocompatibility, showing no negative effects on cells growth and proliferation. Furthermore, the bone-like apatite layer was built obviously in the interface of scaffold after 21 days after implantation in SD rat muscle. In conclusion, the BCP scaffold coated with multilayer of HA/PLLA nanocomposites could be a candidate as an excellent substitute for damaged or defect bone in bone tissue engineering. Further animal bone defect experiments will be carried out to demonstrate its capacity for bone repair and regeneration.
The authors acknowledge the Independent Innovation Foundation of Huazhong University of Science and Technology (2010JC029/2011JC042). Technical assistance from the Analytical and Testing Center of HUST is gratefully acknowledged.
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