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The Effects of Silica and A Nature Polymer on The Size and Properties of Nano-Hydroxyapatite

Volume 32, Number 3

Fariba Najafizadeh1, Mir Abdullah Seyed Sadjadi1*, Seyed Jemiladine Fateami2, Mahmood Karimi Mobarakeh3 and Reza Malekpour Afshar4

1Department of Inorganic Chemistry, Science and Research Branch, Islamic Azad University, Tehran, Iran.

2Department of Chemistry, Basic Sciences Faculty, Islamic Azad and Shahid Bahonar University, Kerman, Iran.

3Department of Trauma and Orthopedic Surgery, Kerman University of Medical Sciences, Kerman, Iran.

4Department of Pathology, Medical school, P.O Box 444 Kerman University of Medical Sciences, Kerman, Iran.

*Corresponding Author E-mail : amir9002001@yahoo.com

DOI : http://dx.doi.org/10.13005/ojc/320341

Article Publishing History
Article Received on : May 17, 2016
Article Accepted on : June 25, 2016
Article Published : 08 Jun 2016
Article Metrics
ABSTRACT:

In this study, we compared the effects of silica and gelatin in nano hydroxyapatite (nHA) composite with pure hydroxyapatite. We have synthesized hydrothermal nHA gelatin template and silica. They (The obtained samples) were investigated by x-ray diffraction (XRD) and Fourier transform infrared spectroscopy (FT-IR). Scanning and transmission electron microscopy (SEM) was used for characterization of particle size and morphology of the samples. The percentage of elements in the prepared composite was determined using energy-dispersive x-ray spectroscopy (EDS). We have identified that the use of gelatin and silica as a coating agent for nHA contributes to the increase in the size of the particles.

KEYWORDS:

hydroxyapatite; gelatin; silica; nano composite

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Najafizadeh F, Sadjadi M. A. S, Fateami S. J, Mobarakeh M. K, Afshar R. M. The Effects of Silica and A Nature Polymer on The Size and Properties of Nano-Hydroxyapatite. Orient J Chem 2016;32(3).

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Najafizadeh F, Sadjadi M. A. S, Fateami S. J, Mobarakeh M. K, Afshar R. M. The Effects of Silica and A Nature Polymer on The Size and Properties of Nano-Hydroxyapatite. Orient J Chem 2016;32(3). Available from: http://www.orientjchem.org/?p=17149

Introduction

Synthetically produced calcium phosphate ceramics and implants have an important position among other biomaterials, because they are considered almost fully biocompatible with living bodies when replacing the hard bone tissues. Calcium hydroxyapatite (Ca10(PO4)6(OH)2 (HA)) and tri-calcium phosphate (Ca3(PO4)2 (TCP)) are currently recognized as ceramic materials that significantly simulate the mineralogical structure of bone [1, 2]. Hydroxyapatite due to its excellent biocompatibility, bioactivity and osteoconductivity is widely used in orthopedic, dental, and maxillofacial applications for bone reconstruction. Nanoparticles of hydroxyapatite, which are prepared synthetically, have chemical and structural similarity with nature hydroxyapatite of bones and teeth [2]. Bone or osseous material is a hard connective tissue that forms part of the skeletal system and is comprised of a matrix hardened by deposited calcium phosphate and other minerals. A bone disorder such as osteoporosis is a growing concern in many aging populations and is associated with bone loss and development of bone brittleness and fractures. In the treatment of bone diseases, such as bone tumors and all similar defects, bone substitutes are needed in the repair/replacement of the infected bone tissue and for the treatment of fractures [3]. Hydroxyapatite Ca10(PO4)6(OH)2 is one of the major constituents of inorganic components of human hard tissues, bone, teeth and tendon, which is responsible for the stability, harness and function of these organs [4]. Because of the chemical similarity with the biological calcified tissues, all calcium phosphates are remarkably biocompatible and bioactive [5-7]. This property is widely used in medicine for biomaterials that are either entirely made of or coated with calcium phosphate. Clinically, there is a high demand for synthetic bone substitution materials that mimic the chemical composition of natural hard tissue, as autologous bone is available only in limited amounts [8]. By altering the morphology of HA crystals through controlling the orientation of crystal planes, novel properties may be produced [9]. Especially, hexagonal morphology of the HA may find promising application in dental implants, because the human tooth enamel has flattened hexagonal prisms of hydroxyapatite crystals arranged parallel with the organic molecules [10-12]. In spite of the large amount of preparation procedures, only a few have been devoted to synthesis of these apatite compounds with controlled morphology [13]. More recently, the Biomaterials group at Cambridge University (Prof Bill Bonfield) has developed a pure HA and silicon substituted (0.8 wt. %) co-precipitated HA in granular form. These preparations were implanted in the femoral condyle of rabbits for 23 days with good bio-acceptance and new bone formation both on the surfaces and between the granules of both HAp and Si-HA [14-17]. However, Patel et al. [13] showed that there are much more bone and have reported the formation of bone-like HA on organic polymers using a process of nucleation in sodium silicate solution [18, 19] with a greater deposition of HA in relatively high concentrations of silica (above 2.0 M) suggesting that silicate oligomers such as dimers, trimmers and cyclic tetramers contribute significantly to HA nucleation [20-22]. Therefore, the aim of this study was evaluation effects of silica and a nature polymer on the size and properties of nano-hydroxyapatite.

Experimental

Materials

Distilled water, Gelatin, CaCl2 2H2O, Na3PO4 12H2O, buffer 10, Na2SiO3 and all chemicals needed for synthesis of hydroxyapatite were supplied from Merck Company and used without any further purification.

Methods

The synthesis of nano-hydroxyapatite

For preparation of hydroxyapatite, 80 mL of the calcium chloride 0.1 M solution was slowly added to 48 mL sodium phosphate 0.1 M, and stirred at the pH = 10. The solution was put in the oven with the temperature of 100°C for half an hour and then the formed precipitate was filtered and washed with double-distilled water.

The synthesis of nano-hydroxyapatite composite based on gelatin and silica.

In situ synthesis of hydroxyapatite rods was carried out in the gelatin matrix. For preparation of modified hydroxyapatite, 2.8 g gelatin was continuously mixed in 70 mL distilled water by a magnetic stirrer at its maximum speed and heated simultaneously at about 68 °C. After stirring for 2 hours, 80 mL of the calcium chloride 0.1 M solution was slowly added to the above prepared biopolymer solution. After stirring for 1 hour, 48 mL sodium phosphate 0.1 M was added drop wisely, and stirred at the pH = 10. The solution was put in the oven with the temperature of 100°C for half an hour then 30 cc double-distilled water and 7.0 g Na2SiO3 in a beaker were poured later in the solution and it was stirred for half an hour at a temperature of 36.5 °C. The samples were incubated for 72 hours at 36.5°C. Products were filtered and washed with double-distilled water, and were dried at room temperature.

Characterization/Investigation methods

The dried products were characterized using FT-IR spectroscopy. FTIR is a technique which is used to obtain an infrared spectrum of absorption or emission of a solid, liquid or gas. An FTIR spectrometer simultaneously collects high spectral resolution data over a wide spectral range.

X-ray diffraction (XRD) relies on the dual wave/particle nature of X-rays to obtain information about the structure of crystalline materials. A primary use of the technique is the identification and characterization of compounds based on their diffraction pattern. The dominant effect that occurs when an incident beam of monochromatic X-rays interacts with a target material is scattering of those X-rays from atoms within the target material. In materials with regular structure (i.e. crystalline), the scattered X-rays undergo constructive and destructive interference. This is the process of diffraction. The diffraction of X-rays by crystals is described by Bragg’s Law, n(lambda) = 2d sin(theta). The directions of possible diffractions depend on the size and shape of the unit cell of the material. The intensities of the diffracted waves depend on the kind and arrangement of atoms in the crystal structure. We have used the X-ray deffractometer model: X’Pert Pro MPD, Manufacturer: PANalytical, Year: 2009, Angle measuring range: 157 to 0.6d degrees. (XRD; Seisert Argon 3003 PTC using nickel-filtered XD-3a Cu K radiations (λ= 0.154 nm).

In scanning electron microscopy, (SEM) an electron beam is scanned across a sample’s surface. When the electrons strike the sample, a variety of signals are generated, and it is the detection of specific signals which produces an image or a sample’s elemental composition. The three signals which provide the greatest amount of information in SEM are the secondary electrons, backscattered electrons, and X-rays. Secondary electrons are emitted from the atoms occupying the top surface and produce a readily interpretable image of the surface. The contrast in the image is determined by the sample morphology. A high resolution image can be obtained because of the small diameter of the primary electron beam. Backscattered electrons are primary beam electrons which are ‘reflected’ from atoms in the solid. The contrast in the image produced is determined by the atomic number of the elements in the sample. The image will therefore show the distribution of different chemical phases in the sample. Because these electrons are emitted from a depth in the sample, the resolution in the image is not as good as for secondary electrons. Interaction of the primary beam with atoms in the sample causes shell transitions which result in the emission of an X-ray. The emitted X-ray has an energy characteristic of the parent element. Detection and measurement of the energy permits elemental analysis (Energy Dispersive X-ray Spectroscopy or EDS).

EDS can provide rapid qualitative, or with adequate standards, quantitative analysis of elemental composition with a sampling depth of 1-2 microns. X-rays may also be used to form maps or line profiles, showing the elemental distribution in a sample surface.

Results and Discussion

Fourier transform infrared spectroscopy

FT-IR spectra have been shown for HA in Figure 1 and Silica coated HA+ Gelatin in Figure 2. The peaks of 603.91, 563.01, 1030.33, 1169.81 cm-1 tensile and flexural modes of phosphate groups and the peak of 1611.12 cm-1 (H-OH) stretching, 3113.76 cm-1 indicates vibration of bond O-H, confirms the presence of hydroxyapatite. FT-IR spectra for synthesized HA have been shown in Figure 1.

Figure 1. FTIR image of HA. Figure 1: FTIR image of HA.

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Figure 2. FTIR image of Silica coated (HA+ Gelatin). Figure 2: FTIR image of Silica coated (HA+ Gelatin).

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The peaks reported in range of the wavenumber region from 650 cm−1 to 1300 cm−1 for the SiO2. The Si-O bond appears at 880 cm−1 and 1250 cm−1 and Si-O bond out of plan 485 cm−1 and Si-O bonding appears at 800 cm−1, the Si-O-Si bond at 970 cm−1, 1083cm−1 and1108 cm−1, Si-O bonds at 884 cm−1, the Si-OH bond at 880 cm−1 and 939 cm−1, the silica bond of 820 cm−1 [23-27]. FT-IR spectra for synthesized HA in the presence of gelatin and silica have been shown in Figure 2.

Information FT-IR spectra HA and Silica coated HA+ Gelatin have been shown in Tables 1 and 2, respectively.

Table 1: Fourier transform infrared spectroscopy HA [23].

Wavenumber, cm-1

Tape of bond

603.91

ν 4 ,Phosphate modes

563.01

ν 4 ,Phosphate modes

1030.33

ν 3 ,Phosphate modes

1169.81

ν 3 ,Phosphate modes

1611.12

(H-OH) Stretching

3113.76

vibration of O-H

 

Table 2: Information FT-IR spectra Silica coated (HA+ Gelatin).

Wavenumber, cm-1

Tape of bond

464, 605, 566

υ4 phosphate modes

1036

Vibration is a phosphate group.

3851

O-H Stretching in hydroxyapatite

3851

N-H Stretching in gelatin

3443

The stretching vibration and bending modes of the OH- and (N-H) Stretching amid (II)

1651

Vibration of C=O

1384 ,1471

-NH bending

464

phosphate mode

3413, 1637

adsorbed H2O

650 cm−1 – 1300 cm−1

SiO2.

800 cm−1, 880 cm−1 and 1250 cm−1

Si-O

970 cm−1, 1083cm−1 and1108 cm−1

Si-O-Si

880 cm−1 and 939 cm−1

Si-OH

820 cm−1

silica bond

 

The bands at 464, 605, 566 cm-1 are derived from the υ 4 phosphate modes. The bands at 1036cm-1 stand for the Phosphate vibration .The band at 3851 cm-1; band may come from N-H Stretching secondary amid in gelatin, O-H Stretching in HA. The stretching vibration and bending modes of the OH- and (N-H) Stretching amid (II) appeared at 3443 cm-1. The typical peaks of phosphate vibration at 1036 cm-1 and, C=O stretching at 1651 can be seen in spectra. Out-of-plane wagging at 605 cm–1. In FT-IR spectra of HA in the absence of biopolymer, The 464 cm-1 band belongs to the υ phosphate mode. The bands at 3413 and 1637cm–1 correspond to the adsorbed H2O. Si-O bonds (1100 cm-1) the proof of the silica is coat. The -NH bending between 1384cm–1 and 1471cm–1 can be seen in spectra.

 

X-ray diffraction investigation

The prepared nHAs presented diffractions peaks at 2Ɵ values of 23, 27, 31, 32, 33, 34, 40, 44, 47, 50, 52, 54, 57 corresponding to (111),(002), (211), (112),(202), (310),(400), (222), (213),(321) , (004) and (322) planes, respectively, confirming that the obtained products are predominantly HA (JCPDS #09-0432). Figure 3 shows the XRD patterns of synthesized nHA.

Figure 3. The XRD patterns nHA. Figure 3: The XRD patterns nHA. 

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Investigation the XRD patterns Silica coated HA+ Gelatin

The peaks of apatite in are widened, indicating that the crystallinity is weak due to the lack of active sites for calcification. It is obvious that the relative intensity of diffraction peaks, particularly the peaks corresponding to (211), (112) and (300) planes are increased when gelatin is added into nHA, implying that the crystallinity of apatite is enhanced, the XRD peaks of as-prepared HA in gelatin solution is similar to that of pure HA, implying that gelatin could guide the HA growth with more perfect crystal structure through the interaction between COO− of gelatin and Ca2+ of apatite [28]. The diffraction peaks of the product prepared nHA at 2Ɵ values of 22, 28, 29, 36, 37, 38, 43 and 48 corresponding to peaks of silica, (002), (210), (211), (112), (130), (222) and (213) planes, respectively, confirming that the obtained products are predominantly HA (JCPDS #09-0432). Figure 4 shows the XRD patterns of synthesized Silica coated HA+ Gelatin.

 Figure 4. The XRD patterns Silica coated HA+ Gelatin. Figure 4: The XRD patterns Silica coated HA+ Gelatin.



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The results of X-ray spectrum

HA+ Gelatin + SiCrystallite size = 10.73 nm

HA  Crystallite size = 6.7 nm

Similar studies indicates that Si is coat on the HA+ Gelatin and crystallite size HA is 10.73 nm and crystallite size HA is 6.7 nm. So existence of Si is due to greater particles. When silica was as the shell surrounding the hydroxyapatite, crystallite size in XRD patterns Silica coated HA+ Gelatin increases.

Scanning electron microscopy

SEM image of nHAp

SEM spectra for synthesized HA have been shown in Figure 5. The size of particles is ranged from 12.75 nm to 15.5 nm.

Figure 5. SEM image of nHAp Figure 5: SEM image of nHAp.
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Table 3: HA particles size.

Sample

Particles Size

nHA

12.75 nm to 15.5 nm

SEM image of Silica coated HA+ Gelatin

SEM spectra for synthesized Silica coated HA+ Gelatin have been shown in Figure 6. The size of particles is ranged from 37.11 nm to 54.07 nm. Compare the size of the particles formed, proves that, a layer of silica around hydroxyapatite surrounds. Therefore, the size of synthesized nanocomposite particle was greater than pure hydroxyapatite. This observation confirms the core shell.

 Figure 6. SEM image of silica coated HA+ gelatin. Figure 6: SEM image of silica coated HA+ gelatin.

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Table 4: Silica coated HA+ Gelatin particles size.

Sample

Particles Size

Silica coated HA+ Gelatin

37.11 nm to 54.07 nm

 

Energy-dispersive X-ray spectroscopy investigation

Elemental analysis did by Energy-dispersive X-ray spectroscopy (EDS) method for confirming of nano composite preparation. Figure 7 and Table 5 shows obtain results for synthesized of HA. We obtain the Ca/P ratios by using of amount of calcium and phosphorus. The Ca/P ratios of 1.7 were calculated for HA with gelatin, this ratio is nearly to the theoretical value. Considering the repeat unit of the HA chemical structure Ca10(PO4)6(OH)2. In addition, Figure 8 and Table 6 show EDS analysis for HA/ gelatin silica coated. The presence of silica in Figure 8 and Table 6 confirms coated of silica in HA/ gelatin matrix. The Ca/P ratios of 1.6 were calculated for HA/ gelatin silica coated, this ratio is equivalent to the theoretical value. Considering the repeat unit of the HA chemical structure Ca10(PO4)6(OH)2.

Figure 7. EDS pattern of nHA. Figure 7: EDS pattern of nHA.

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Table 5: EDS quantitative result of HA.

Element

[wt.-%]

Oxygen

31.61

Phosphorus

25.71

Calcium

52.68
Figure 8. EDS pattern of HA/gelatin coated with silica. Figure 8: EDS pattern of HA/gelatin coated with silica.

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Table 6: The EDS Quantitative Result of silica coated in HA/gelatin.

Element

[wt.-%]

[A.-%]

C

12.11

18.82

O

49.38

57.62

Na

7.69

6.69

Si

8.36

5.55

P

8.67

4.90

Ca

13.79

6.42

100.0

100.0

Conclusions

The presence of PO43− group in nHA and Si-HA synthesized in gelatin matrix was confirmed from IR studies.The absorption band observed at 3425-3586 cm-1 corresponding to the characteristic stretching vibration of the OH- groups in HA structure shows the presence of HA structure in both the cases. The EDAX elemental analysis data and appearance of additional new bands in FTIR spectrum observed at 800 and 1250 cm-1 confirm presence of silica components in Si-HA samples.Appearance of the same atomic ratio of Ca/P for the samples before and after immersion in silica solution confirms that any substitution of phosphate by silicate ions has not been occurred in HA samples.

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