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Page 1 of 9
RSC Advances
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Cite this: DOI: 10.1039/c0xx00000x
ARTICLE TYPE
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Chitosan (PEO)/bioactive glass hybrid nanofibers for bone tissue
engineering
Sepehr Talebiana,*, Mehdi Mehralia, Saktiswaren Mohanb, Hanumantha rao Balaji raghavendranb ,
Mohammad Mehrali a, Hossein Mohammad Khanloua, Tunku Kamarulb, Amalina Muhammad Afifia,*
A novel hybrid nanofibrous scaffold prepared with chitosan [containing 1.2 wt% polyethylene oxide
(PEO)] and bioactive glass (BG) was fabricated by an electrospinning technique. The morphological and
physicochemical properties of scaffolds were studied by scanning electron microscopy (SEM) and
spectroscopy. The measurements of tensile strength and water-contact angles suggested that the
incorporation of BG into the nanofibers improves the mechanical properties and hydrophilicity of the
scaffolds. Biomineralization of the nanofibers was evaluated by soaking them in simulated body fluid
(SBF), and the formation of hydroxycarbonate apatite (HCA) layer was determined by EDX and FESEM. The results showed that BG-containing nanofibers could induce the formation of HCA on the
surface of composite after 14 days of immersion in SBF. In vitro-cell viability of human mesenchymal
stromal cells (hMSCs) on nanofibers was assessed by using the MTT assay. The cell-adhesion results
showed that hMSCs were viable at variable time points on the chitosan/PEO/ BG nanofiber scaffolds. In
addition, the presence of BG enhanced the alkaline phosphatase (ALP) activity of hMSCs cultured on
composite scaffolds at day 14 as compared to that on pure chitosan/PEO scaffolds. Our results suggest
that chitosan/PEO/BG nanofibrous composite could be a potential candidate for application in tissue
engineering.
Introduction
The major bone extracellular matrix (ECM) building blocks are
composed of collagen I fibrils (50–500-nm diameter) mineralized
with a thin, highly crystalline carbonated apatite layer. Therefore,
a biodegradable, highly porous, strong nanofibrous scaffold that
mimics the collagen fibrils is highly recommended for use in the
field of bone tissue engineering for promoting osteoblasts
infiltration and proliferation 1, 2. Electrospun nanofibers are a
promising materials for bone tissue engineering owing to their
morphological similarity with that of bone ECM, large ―surface
area/volume‖ ratio that offers a larger space for cell adhesion and
proliferation, and a tunable porous structure that provides a
favorable site for drug release and ion exchange in vitro and in
vivo 3, 4. It has been reported that the biological features of
electrospun nanofibrous scaffolds including biocompatibility,
bioactivity, hydrophilicity, and mechanical properties are mainly
dependent on the selected polymer material 5.
Meanwhile, chitosan, a polysaccharide obtained by partial
deacetylation of chitin, has a linear structure and is composed of
randomly distributed β-(1-4)-linked D-glucosamine (deacetylated
section) and N-acetyl-D-glucosamine (acetylated section). It
plays important roles in the attachment, differentiation, and
morphogenesis of osteoblast cells owing to its structural
similarity to that of glycosaminoglycans (GAG), which is a major
bone and cartilage component 6-8. Nevertheless, lack of
This journal is © The Royal Society of Chemistry [year]
bioactivity and low mechanical strength limits the application of
biopolymers in bone regenerative scaffolds 9. To overcome these
drawbacks of biopolymers, a variety of bioactive inorganic
materials have been incorporated into the polymer matrix (by a
composite approach) to improve the biological properties (such as
bioactivity, protein adsorption, cell proliferation, and osteogenic
differentiation) and the mechanical strength of the resulting
biocomposite 10-16.
Among the inorganic phases, bioactive glasses (BGs) are quite
fascinating because immersing BG in a body fluid initiates
formation of amorphous calcium phosphate on their surface,
which later crystallizes into a hydroxyl carbonate apatite (HCA)
layer. This HCA layer mimics the chemical composition and
structure of bone mineral and plays a key role in forming a bond
with the surrounding bone tissues 5, 6, 9, 17-21. The combination of
chitosan/BG as a composite scaffold is a new and promising
approach for bone cell regeneration, with only few supporting
literature 10, 22, 23. However, to the best of our knowledge, bone
cell regeneration using electrospun chitosan (polyethylene oxide;
PEO)/BG nanofibrous composite is the first of its kind approach
that can pave the way toward the development of a novel bone
tissue regenerative scaffold for repairing bone defects. For this
purpose, an electrospinning technique was employed to fabricate
a novel nanofibrous nanocomposite membrane from
chitosan/PEO solution incorporating BG particles. Various
properties of the nanocomposite membrane including mechanical
[journal], [year], [vol], 00–00 | 1
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properties, wettability, and biomineralization were investigated.
In addition, detailed in vitro biological assessments were
performed, such as cell adhesion, cell viability [3-(4,5dimethylthiazol-2-yl)-2,5-diphenyltetrazolium bromide; MTT
assay], and bone cell differentiation [alkaline phosphatase (ALP)]
to evaluate the efficiency of nanofibrous scaffold for bone repair.
Results and Discussion
Morphology of electrospun nanofibers
Figure 1 shows the FE-SEM images of electrospun chitosan/PEO
and chitosan/PEO/BG nanofibers. The original chitosan/PEO
nanofibers were smooth fine fibers with random orientation on
the collector. However, after addition of BG powders, in some
areas the fibers started to fuse together (adjacent fiber adhered
together from their interface) due to the formation of secondary
bonding (hydrogen bonds and ionic bonds) 24. Moreover, in some
regions, small particles of BG were located on the surface of
fibers, which imparted roughness to the fibers2.
Figure 2. Characterizations of BG and electrospun nanofibers. (a) FTIR
spectrums. (b) XRD spectrums.
Figure 1. FESEM images of chitosan/PEO (a, b) and chitosan/PEO/BG (c,
d) scaffolds.
Evaluation of BG particles in chitosan/PEO/BG nanofibers
Three independent characterization methods—XRD, FTIR, and
EDX—were used to characterize the nanofibrous membranes,
particularly the BG particle deposits on the surface of
chitosan/PEO/BG nanofibers. Figure 2 shows the XRD and FTIR
spectra of BG powders and the electrosopun nanofibers.
The X-ray diffractograms revealed that the BG powders formed
sodium calcium silicate (Na2CaSi3O8) and Na2Ca2Si3O9, which
coincides with sodium calcium silicate in the JCPDS card 0120671 and 022-1455, respectively19, 25-29
2 | Journal Name, [year], [vol], 00–00
The XRD pattern of chitosan/PEO shows the crystalline nature
of these nanofibers, consisting of three peaks. The sharp peak at
2θ of 19° and the broad peak at 2θ of 23° are attributed to the
crystalline phase of PEO, and the one broad peak at 2θ of 15° is
assigned to the crystalline phase of chitosan 30. The addition of
BG to the nanofibers introduces four extra peaks to the pattern
that are related to the crystalline phase of BG (Na2Ca2Si3O9);
peak at 2θ of 26° is attributed to 211 crystal plane, peaks at 2θ of
33° and 34° are attributed to 204 and 220 crystal planes,
respectively, and the peak at 2θ of 48° is attributed to 404 crystal
plane 27-29. The FTIR spectra of pure BG powder showed the
absorption bands of 527 cm−1 and 624 cm−1 assigned to the
bending vibrations of the O-P-O groups. The three peaks at 451,
913, and 1014 cm−1 were allocated to the stretching vibration of
Si-O bonds in each SiO4 tetrahedron 6, 10, 26, 31-34. In chitosan/PEO
FTIR spectra, the triple bands at 1061, 1099, and 1146 cm−1 were
assigned to the stretching vibration (νs) of the C-O-C groups and,
together with the band at 2883 cm−1 (CH2 stretching), they were
considered as the characteristics peaks of PEO. In the same
spectra, the broad band at 3362 cm−1 was allocated to N-H and
O-H stretching of polysaccharide molecules. Furthermore, the
absorption band at 1645 cm−1 was attributed to the stretching
vibration of amide I groups (canbonyl, C=O-NHR) in the
chitosan. Finally, the FTIR spectra of chitosan/PEO/BG
nanofibers revealed the bands at 463 and 659 cm−1 that did not
appear in the chitosan/PEO spectra, which have been assigned to
the Si-O stretching band and the O-P-O bending band,
respectively. In addition, broadening of the band at approximately
961 and 1060 cm−1, in conjunction with a slight shift of amid I
band to 1563 cm−1, were attributed to the interaction of chitosan
with BG 6, 10, 35-37.
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RSC Advances
Finally, the elemental analysis (EDX) (Figure 3a) of the
chitosan/PEO/BG nanofibers showed large peaks of carbon and
oxygen indication of the two main components of chitosan and
PEO, in addition small amounts of silicon, calcium and sodium
were indication of BG particles in the scaffolds. Moreover, EDX
mapping results revealed the distribution of carbon (Figure 3b)
and oxygen (Figure 3c) as the major organic components of
scaffolds whereas the inorganic sodium (Figure 3d), silicon
(Figure 3e) and calcium (Figure 3f) were observed in the form of
BG particles on fibres. It is worth noting that silicon as the major
component of BG particles showed several large bright spots on
the EDX map (Figure 3e) (that is also observable in Figure 3a as
white particles), which implies to heterogeneous distribution of
BG particles in some areas of the nanofiber membrane.
Page 4 of 9
chitosan/PEO matrix 38.
Figure 4. Stress-strain curves of chitosan/PEO and chitosan/PEO/BG
nanofibers.
Wettability of electrospun nanofibers
Cell–scaffold interactions are strongly influenced by the
wettability of the scaffold’s surface, because this property
determines some of the most significant biological events such as
protein adsorption, cell attachment, and cell proliferation 10. The
water-contact angle of chitosan/PEO and chitosan/PEO/BG
nanofibers was measured to evaluate the wettability of the
scaffolds (Figure 5). The chitosan/PEO membranes had a contact
angle of 57.5 ± 4°, while the BG-containing membranes
possessed a contact angle of 38.1 ± 2°. This difference implies
that the BG-containing nanofibers possessed a higher
hydrophilicity. The exposure of BG particles on the surface of
fibers creates a relatively rough and more hydrophil surface,
which imparts better wettability of these composite fibers 38.
Figure 3. EDX spectra of chitosan/PEO/BG composite nanofibers (a).
Elemental mapping representing the elemental distribution of carbon
(b), oxygen (c), sodium (d), silicon (e) and calcium (f) of the composite
nanofibers.
Mechanical properties of electrospun nanofibers
The stress–strain curves of chitosan/PEO and 1% (w/v)
chitosan/PEO/BG nanofibers are given in Figure 4. The average
tensile strength of chitosan/PEO nanofibers was 1.58 ± 0.2 MPa
with strain at break of 2.5%, whereas chitosan/PEO/BG
nanofibers had a tensile strength of 3.01 ± 0.15 MPa with strain
at break of 4%. Accordingly, the 1%-loaded nanofibers showed a
higher tensile strength than pristine chitosan/PEO nanofibers, due
to the formation of secondary bonds between BG particles and
the matrix 6. Moreover, the composite nanofibers exhibited better
ductility as a result of yielding phenomenon, which is the
consequence of debonding between BG particles and
This journal is © The Royal Society of Chemistry [year]
Figure 5. Water contact angle of chitosan/PEO (a) and chitosan/PEO/BG
(b) nanofibers.
Biomineralization of electrospun nanofibers with respect to
apatite formation
The bone-bonding capability of a scaffold is sometimes assessed
by its ability to induce apatite formation on its surface upon
immersion in SBF 39 (apart from few exceptions where the
materials directly bonded to living bone without the formation of
detectable apatite on their surface39). The response of electrospun
nanofibers in contact with SBF was evaluated by FE-SEM and
EDX. FE-SEM micrographs of electrospun chitosan/PEO and
chitosan/PEO/BG membranes soaked in SBF for 14 days are
shown in Figure 6a–d. After soaking in SBF, on both BGcontaining and non-BG-containing nanofibers, a calcium
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phosphate layer was observed. In BG-containing nanofibers a
layer of plate-like apatite with approximate thickness of 100-150
nm formed on their surface that was developed perpendicular to
the fibers surface. Furthermore, based on the EDX spectra of
chitosan/PEO/BG nanofibers after incubation with SBF (Figure
6f), the presence of calcium and phosphorous on their surface
was confirmed, and the Ca/P molar ratio of the coating was
estimated to be 1.53, which is lower than that of stoichiometric
hydroxyapatite (Ca/P = 1.67), but similar to that of
hydroxycarbonate apatite (HCA) (Ca/P = 1.5) 34, 35. Previously it
has been reported that formation of apatite on artificial scaffolds
is induced by incorporation of functional groups that could create
negative charge on the scaffold. Thus, BG particles in
chitosan/PEO/BG nanofibers act as nucleation initiation sites for
formation of apatite, leading to faster formation of more apatite
40
. On the other hand, non-BG-containing nanofibers showed a
significantly different morphology of calcium phosphate
deposition on their surface. In these nanofibers the calcium
phosphate layer didn’t appear as plate-like apatite, instead it was
emerged as a smooth layer (with approximate thickness of 50nm)
covering the fibre surface causing the average fiber diameter to
increase to 100-150nm. In addition, The EDX spectra of
chitosan/PEO nanofibers after incubation with SBF (Figure 6e)
showed negligible amount of Ca and P (comparing to
chitosan/PEO/BG nanofibers) with Ca/P molar ratio of 0.65,
which is far lower than that of stoichiometric hydroxyapatite
(Ca/P = 1.67) but closer to that of calcium pyrophosphate (Ca/P
= 1)41. It is worth noting that presence of positively charged
amino groups on the back bone of chitosan together with absence
of apatite nucleation initiators could cause a reduction in apatite
forming ability of chitosan/PEO nanofibers and lowers the Ca/P
40
ratio35,
.
These results suggest that chitosan/PEO/BG nanofibers show
improved apatite forming ability compared to chitosan/PEO
nanofibers when immersed in SBF and therefore they might be
ideal for forming a bond with bone39.
Figure 6. Characterizations of nanofibers surface after 14 days incubation
in SBF at 37○C. FESEM images of chitosan/PEO (a, b) and
chitosan/PEO/BG (c, d) nanofibers surface after immersion in SBF. EDX
spectra of calcium phosphate layer formed on the surface of
chitosan/PEO (e) and chitosan/PEO/BG (f) nanofibers after immersion in
SBF.
Cell adhesion and viability
Initial attachment and adhesion of hMSCs are extremely crucial
for their long-standing stability and differentiation 42. In our
study, we investigated the cellular behavior by fluorescence
microscopy and MTT assay to evaluate cell adhesion and
viability in order to correlate the properties of scaffolds and the
cultivated cell response. Furthermore, FE-SEM was used to
visualize the morphological changes in hMSCs during culturing.
The cell viability at different time points was confirmed by the
MTT assay; however, no statistically significant difference was
noted between chitosan/PEO and chitosan/PEO/BG scaffolds.
These results indicate that these scaffold materials did not
interfere with cell viability and hence were not cytotoxic.
Figure 7. MTT viability assay (a) and ALP activity (b) of hMSCs measured
on chitosan/PEO/bioactive glass scaffolds (BG) and chitosan/PEO
scaffolds (NBG) after 3, 7, 10 and 14 days of cultivation.
Consistent with the cell-viability assay, Hoechst staining also
confirmed that cells were viable at every tested time points in the
scaffolds. The blue-stained cells were observed on all scaffolds,
which indicated that the composition of the scaffolds provided a
physiological environment for cell attachment and, thus, the
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Page 6 of 9
scaffolds were biocompatible. The MTT results and fluorescence
microscopy images are shown in Figure 7a and Figure 8-9,
respectively.
Figure 10. FESEM images of hMSCs cultured on the chitosan/PEO
scaffolds after 1(a), 3(b), 5(c) and 7(d) days.
Figure 8. Fluorescence microscope images of adherent hMSCs on
chitosan/PEO scaffolds after 1(a), 3(b), 5(c) and 7(d) days.
Figure 11. FESEM images of hMSCs cultured on the chitosan/PEO/BG
scaffolds after 1(a), 3(b), 5(c) and 7(d) days.
Cell differentiation and mineralization
Figure 9. Fluorescence microscope images of adherent hMSCs on
chitosan/PEO/BG scaffolds after 1(a), 3(b), 5(c) and 7(d) days.
The SEM images of MSCs after 1, 3, 5, and 7 days of culturing
on the scaffolds are demonstrated in Figure 10-11. The SEM
results complimented the fluorescence microscopy results,
indicating that MSCs adhere and spread on the nanofiber
scaffolds. From day 1, the cells started to spread on the nanofiber
scaffolds and tended to show filopodia extending toward the
adjacent cells. This filopodia extension continues until the 7th
day, by when the adjacent cells adhere to each other to form tight
clusters. Moreover, with time, the number of cells adhered to the
scaffold surface increases, indicating that these scaffolds are good
supporters of the cells.
This journal is © The Royal Society of Chemistry [year]
An efficient bone scaffold should be able to support bone
formation, including the organic and inorganic constituents on the
natural tissue. ALP is considered to be one of the major
components of the bone tissue vesicles owing to its role in the
formation of calcium phosphate-containing apatite. In addition,
ALP is a well-know early stage marker of osteogenic
differentiation. The ALP activity results are shown in Figure 7b.
Consequently, the ALP activity gradually increased 2-fold in
cells cultured in the chitosan/PEO/BG scaffold by day 14 as
compared to that at the early time points (P < 0.05). Although a
gradual increase in ALP was noted in the cells cultured in
chitosan/PEO, the increase was almost similar to that on days 3,
7, and 10. A significant increase was noted on day 14; however,
the increase was approximately 0.5-fold.
In addition, the cell mineralization pattern on chitosan/PEO and
chitosan/PEO/BG nanofibers after 14 days of culturing was
qualitatively assessed by FE-SEM/EDX (Figure 10 and 11,
respectively). The FE-SEM images revealed the surface
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mineralization of cells in the form of distinct nodules for both
type of scaffolds. In case of chitosan/PEO/BG nanofibers these
nodules were larger in size comparing to the ones in
chitosan/PEO nanofibers. Overall, the cell on chitosan/PEO
scaffold showed a smoother surface comparing to the cell grown
on chitosan/PEO/BG scaffold. Moreover, the EDX results
showed the presence of calcium phosphate on surface of merging
cell on both scaffolds. Notably, the Ca/P molar ratio on surface of
merging cell layer on non-BG-containing scaffold was equal to
1.1 whilst this ratio was measured to be 1.4 (close to 1.5 of HCA)
for the cell grown on BG-containing scaffold. These results
suggests that cell mineralization occurred in both type of
scaffolds, however, the BG-containing scaffold showed a higher
level of mineralization due to the presence of BG in the scaffolds
34
. Consistent with the cell mineralization results, the apatite
formation and ALP production indicates that BG scaffold had
higher potential to induce hMSCs differentiation into osteogeniclike cells; however, further studies on extended time points are
needed to clarify its potential.
Figure 11. FESEM image of hMSCs grown on the surface of
chitosan/PEO/BG scaffold after 14 days (a). EDX spectra of hMSCs in the
boxed region which is representing a significant presence of Ca and P on
the surface of composite nanofibers after 14 days of seeding (b).
Experimental
Materials
Low-molecular weight chitosan powders (DD ≥75%) were
purchased from Sigma-Aldrich; high-molecular weight PEO
(PEO-900,000 Mw) was supplied by Acros-Organics; and glacial
acetic acid was obtained from R&M Chemicals. Tetraethyl
orthosilicate (TEOS, 98%) and triethyl phosphate (TEP, 99%)
were purchased from Acros Organics, while sodium nitrate
(NaNO3), calcium nitrate tetrahydrate (CaNO3.4H2O), and nitric
acid (HNO3, 65%) were supplied by R&M Chemicals.
Synthesis of BG particles
Figure 10. FESEM image of hMSCs grown on the surface of chitosan/PEO
scaffold after 14 days (a). EDX spectra of hMSCs in the boxed region
which is representing a significant presence of Ca and P on the surface of
composite nanofibers after 14 days of seeding (b).
BG was fabricated by a sol-gel method proposed by Siqueira 19;
accordingly, fabrication of BG involved hydrolysis and
polycondensation of stoichiometric amounts of TEOS, TEP,
NaNO3, and CaNO3.4H2O to obtain the final composition of SiO2
as 49.15 mol%, CaO 25.80 mol%, Na2O 23.33 mol%, and P2O5
1.73 mol%. The hydrolysis of TEOS and TEP was performed in
0.1 mol L−1 HNO3 solution using a 8 molar ratio of
HNO3+H2O/TEOS+TEP. First, TEOS was added to the HNO3
solution under constant stirring by using an overhead mixer, then
other reagents were added to the mixture at 60-min intervals with
continuous stirring until the solution reached the gelation point.
Next, the gel was kept at room temperature for overnight until it
turned translucent. Subsequently, the gel was dried at 130°C for 2
days. Finally, the dried gel was calcinated at 700°C for 3 h with
heating at the rate of 1°C min−1 , after which the resulting
ceramic was ball milled for 12 h until a fine particulate BG
ceramic was obtained.
Preparation of electrospun nanofibrous membrane
A suspension of BG particles was prepared by dispersing 0.05 g
BG in 4 mL distilled water (1% w/v) and homogenized on an
ultrasonic bath for 30 min. Then, PEO was added to 4 mL BG
suspension (3 wt%) and agitated by using a magnetic stirrer until
the PEO was completely dissolved. Separately, 3 wt% chitosan
powder was dissolved in acetic acid/water mixture (80/20 volume
ratio). Then, the chitosan solution and PEO/BG solution were
mixed together in a 60/40 (chi/PEO) weight ratio and stirred for 1
h until a clear solution was obtained. Finally, electrospinning was
performed under the following conditions: 19-gauge needle, 10cm tip to the collector distance, 0.4 mL/h pump-rate, and 6-kV
voltage. The electrospun fibers were then kept in an oven at low
6 | Journal Name, [year], [vol], 00–00
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RSC Advances
temperature (60○C) for 24 h to allow complete removal of the
solvent.
Chemical and physical characterization of nanofibrous
membranes
The microstructure of chitosan/PEO/BG nanofibrous composite
was studied under a field-emission scanning electron microscope
(FE-SEM; High-resolution FEI Quanta 200F; Hitachi; Japan).
Furthermore, to study the elemental composition of the scaffolds,
energy dispersive X-ray analysis (EDX) was performed by using
the EDX-System (S-4800; Hitachi; Japan) attached to the FESEM
instrument with accelerating voltage of 5Kv. The functional
groups of the composite membranes were identified by fourier
transform infrared (FTIR) analysis (Spectrum 400; Perkin Elmer,
USA) with a frequency range of 400 to 4000 cm−1. The X-ray
diffraction (XRD) patterns of the powder and the composite were
obtained by the PAN analytical’s Empyrean XRD (USA) with
mono-chromated CuKα radiation (λ = 1.54056 A°), operated at
45 kV, 40 mA, a step size of 0.026°, and a scanning rate of 0.1°
s−1 over a 2θ range from 2° to 90°.
The mechanical properties of the chitosan/PEO/BG and
chitosan/PEO nanofibrous membranes were measured at room
temperature by using the Instron 3365 machine (USA) at a strain
rate of 1 mm/min. All fibrous membranes were processed into
rectangular shape by electrospinning of the samples on a
cardboard frame with gap dimensions of 35 mm × 19 mm 43. The
ultimate tensile strength was obtained from the stress–strain curve
and calculated as the average of 4 samples.
The static water-contact angle of nanofibrous scaffolds was
measured by using a video-based optical contact angle measuring
instrument (OCA 15EC; DataPhysics Instruments GmbH;
Germany). The nanofibers were the carefully coated onto a glass
slide. A single droplet of distilled water (2 µL) was applied to the
surface of membrane, and the contact angle was measured after
30 s. The measurements were repeated three times at different
locations for each sample, and the average value was calculated.
Biomineralization of the electrospun composites was evaluated
by examining the ability of the membranes to form a bone-like
apatite on their surface on immersion in simulated body fluid
(SBF), which was prepared according to the method described
earlier 39, 44. The scaffolds (10 mm × 10 mm) were soaked in 5
mL SBF and incubated at 37°C in a humidified atmosphere of 5%
CO2 for 14 days with daily replacement of the soaking medium.
At the end of the soaking period, the samples were removed from
the SBF, carefully rinsed with deionized water, and dried at 80°C
in vacuum. FE-SEM and EDX were performed to assess the
formation of an apatite layer on the surface of nanofibers.
Human mesenchymal stromal cells (hMSCs) culturing
hMSCs were isolated by using a previously described method 45.
Then, the cells were cultured in ABC media (Invitrogen,
Carlsbad, CA, USA) supplemented with 15% fetal bovine serum
(FBS, Invitrogen), 100 U/mL penicillin (Sigma-Aldrich, USA),
and 100 mg/mL streptomycin (Sigma-Aldrich) in tissue-culture
flasks at 37°C in a humidified atmosphere of 5% CO2. When the
cells reached near confluence (80–90%), they were detached by
trypsin/ethylenediaminetetraacetic
acid
(EDTA;
Cell
This journal is © The Royal Society of Chemistry [year]
Page 8 of 9
Applications, San Diego, CA, USA) and then subcultured into the
next passage. All cells used in this study were obtained from a
control donor and continuously cultured without any recryopreservation until a predetermined number of passages were
performed. Then, each scaffold was seeded with a cell suspension
(2 × 105 cells/ml) and placed in an incubator for 1 h. Finally, 450
μL of medium was added to each well, and the cells were
cultured on tissue culture polystyrene as controls.
MTT assay
The cell viability at different time points (3, 7, 10, and 14 days)
was performed in a 96-well microplate reader (Becton Dinkinson,
Lincoln Park, USA) by the MTT colorimetric assay, and the
absorbance was measured at 570 nm on a spectrophotometer
(Bio-Tek Instruments, Winooski, USA). The well containing only
the MTT solution were considered as the blank reference.
Cell morphology
The scaffolds seeded with hMSCs were stained with Hoechst
33342 blue (Invitrogen, USA) and analyzed by fluorescence
microscopy (C-HGFi; Nikon, Japan) after 20 min of incubation at
room temperature. For confocal microscopy (TCS-SP5 II; Leica
Microsystem, Mannheim, Germany), the post-fixed (2.5%
formalin) scaffold samples were dual stained with Hoechst dye
and acridine orange. The three-dimensional (3D) image obtained
from the incorporation of multiple series of images collected by
confocal laser microscopy facilitated investigation of cell
infiltration up to 0–80 µm into the scaffolds.
In order to observe the cells adhering to the sample surface after
culturing for 1, 3, 5, and 7 days by FE-SEM, the post-fixed
scaffolds (2.5% formalin) were dehydrated by using a series of
graded ethanol/water solutions (10, 30, 50, 70, 90, and 100%) and
kept in a fume hood to dry at room temperature. After the
scaffolds were dried, they were sputter coated with platinum and
observed.
ALP assay
The differentiation of hMSCs cultured on scaffolds was evaluated
by quantifying the ALP activity. After being cultured for 3, 7, 10,
and 14 days, on each indicated day, the supernatant was collected
and the ALP activity was immediately measured by using a
commercial kit (Abcam, USA) according to the manufacturer’s
protocol. The production of p-nitrophenol and indication of ALP
activity was measured using a microplate reader at 405 nm.
Statistical Analysis
The values obtained were averaged and expressed as means ±
standard deviation (SD). Statistical differences were determined
using SPSS version 10, post-hoc analysis, followed by ANOVA
and LSD. The differences were considered statistically significant
if the value of p was < 0.05.
Conclusions
Our results suggest that incorporation of BG into chitosan (PEO)
nanofibers would lead to the development of a new nanofibrous
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composite that may be an appropriate scaffold for tissue
engineering due to its improved mechanical and biological
properties as compared with that of pure chitosan(PEO)
nanofibers.
20.
21.
Acknowledgements
22.
The authors gratefully acknowledge the financial supports from
University of Malaya under the HIR-MoE Grant (Reference
number - UM.C /625/1/HIR /MOHE /MED/32 account number –
H20001-E000071); University of Malaya Research Grant
(UMRG), Grant No. RP021/2012B, and Postgraduate research
Fund (PPP), Grant No. PG066/2013A .
23.
Notes and references
a Department of Mechanical Engineering, Engineering Faculty,
University of Malaya, 50603 Kulala Lumpur, Malaysia.
b Tissue Engineering Group (TEG), Department of Orthopaedic Surgery,
NOCERAL, Faculty of Medicine, University of Malaya, Kuala Lumpur50603, Malaysia.
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