- Research article
- Open Access
Chemical characterization of some substituted hydroxyapatites
© Ibrahim et al 2010
- Received: 21 October 2011
- Accepted: 28 November 2011
- Published: 28 November 2011
Synthetic multi-substituted hydroxyapatite nano powders containing silicon and or carbonate prepared by a wet chemical method. The process parameters are set up to allow the simultaneous substitution of carbonate and silicon ions in the place of phosphorus. The chemical and structural characterizations of the prepared powders are determined with the aid of; XRF, ICP, XRD and FTIR. The results show that, the ion substitution in the crystal lattice of HA caused a change in the unit cell dimensions and affected the degree of crystallization of the produced powders. The apatite formation abilityy of the prepared discs from the synthesized powders is determined by immersing in SBF solution for different periods. The degree of ion release was determined in the obtained solutions. The examined surface of the immersed discs under SEM and analyzed by CDS showed a more dense HA layer than those of un-substituted ones. The HA with the substituted silicon and carbonate ions, showed the highest solubility with greater rate of ion release, compared with carbonate-free powder. All prepared powders took sodium ion from the SBF solution during immersion, which was not recorded before.
- Simulated Body Fluid
- Simulated Body Fluid Solution
- Prepared Powder
The calcium apatite phase forming the main mineral part of bones and teeth , contains several ions in different amounts substituting calcium and phosphorus in the HA lattice [2, 3]. Whereas, the synthesized hydroxyapatite (Ca10(PO4)6(OH)2, HA) is a pure phase that is well established bone replacement material in orthopaedics and dentistry. These substitutions provoke changes in the HA surface structure and charge, raising its solubility and increasing the ability of synthetic HA to be involved in a natural bone remodeling process. The type and the amount of ionic substitution in the apatite phase of bone varies from ~2-8 wt% in CO3 to minor concentrations in Mg, Na, to the ppm level for trace elements Si, Sr, Zn, Pb. Although these levels of substitutions are small, it is established that these elements are associated with the properties of biological apatites and play a major role in the biochemistry of bone, enamel and dentin [4–6].
Hydroxyapatite contains carbonate ions substituting both the phosphate (B-type CHA) and hydroxyl (A-type-CHA) sites of the HA structure. The B-type is the preferential carbonate substitution found in the bone of a variety of species, with the A/B type ratio in the range 0.7-0.9 . A higher value of the A/B ratio is observed in old tissue, compared to young tissue. The presence of B-carbonate in the apatite lattice is responsible for the decrease in its degree of crystallinity increasing thereby its solubility .
The importance of silicon on bone formation and calcification is tackled by different workers in vitro and in vivo studies: Carlisle et al. demonstrated the important role played by Si in connective tissue metabolism, especially in bone and cartilage . Where, it is essential to the growth and development of biological tissue such as bone, teeth and some invertebrate skeletons. They also reported that, a reduction in Si in bone results in a decrease in the number of osteoblasts , osseomatriceal collagen, and glycosaminoglycans .
The addition of Si during the HA synthesis leads to an improvement of the bioactive behavior: in vitro studies by Gibson et al. demonstrated that the substitution of silicate ions for phosphate ions into hydroxyapatite enhances osteoblast cell activity, compared to phase pure HA. Silicate ion substitution is also reported to enhance the formation of a poorly crystalline surface apatite layer on HA, incubated in simulated body fluid (SBF) . Furthermore, an in vivo study by Patel et al., comparing the rates of bone apposition to HA and silicon-substituted HA (Si-HA) ceramic implants demonstrated bone apposition to be significantly greater at the surface of Si-HA implants . Porter et al. indicated more rapid remodeling of bone surrounding the Si-HA when compared to HA . It is suggested that these findings are related to increased dissolution rates of the Si-HA implants compared to HA .
The present work aims to prepare different substituted hydroxyapatites, Si-HA and Si-CHA, as well as stoichiometric pure HA powders by wet chemical method. The ability of the prepared powders to form new apatite is tested through reaction with SBF solution.
Mole proportion of the different constituents in the prepared phases
Mole concentration of constituents
mole% Si to P- ion substituted HA
mole% Si to P- HAs
The chemical constitution of the prepared powders is determined by XRF and ICP utilizing the following equipments; (AXIOS,WD-XF Sequential Spectrometer) and (ICP-OES), respectively. The molar ratio of Calcium to phosphorus as well as the concentration of the added elements, were calculated from the results obtained. The phase composition is determined by XRD utilizing an equipment by Philips operated at 40 KV and 40 mA using Cu Kα radiation. Scanning is carried out over the range from 2Ө = 4° to 80°. The Scherrer formula is used to calculate the average crystallite size. The different elemental constitutional groups are determined by FTIR utilizing a (FT/IR-6100typeA, JASCO) equipment in the range between 400 to 4000 cm-1.
Apatite formation ability
The prepared green powders are processed in the form of discs under a pressure of 10 KN with the following dimensions; diameter 12 mm, height 2 mm. Part of the prepared powders are fired at 900°C for 1 h. Both green and fired discs are immersed in SBF solution for different periods; 24 h and, 2, 3, 5, 9, 14, 21 and 29 days, at 37°C.
The concentration of the different constituting elements of the SBF solution (mM) is as follows: Na+ 142.0; K+ 5.0; Ca2+ 2.5; Mg2+ 1.5; Cl- 147.8; HCO3- 4.2; HPO42- 1.0; SO42- 0.5 . The samples are removed out after the immersion period studied and the solutions are analyzed using spectrophotometer (UV-2401 PC, UV-VIS Recording spectrophotometer, Shimadzu, Japan) as well as with biochemical kits (Techo Diagnostic, USA) to detect the total calcium ions (Ca2+) at λ = 570 nm and phosphorus ions (P5+) at λ = 675 nm. The solutions are tested for other ions such as sodium (Na+) and silicon (Si4+), using flame atomic absorption spectrometer (Varian SpectrAA). Moreover, the pH of the SBF is measured using a pH meter (Fisher Scientific, Pittsburgh PA). SEM, Model Philips XL 30 attached with energy dispersive X-ray spectroscope (EDS) unit, utilizing an accelerating voltage of 30 KV to scan the surface of the discs after immersion and to determine the proportion of the surface elements.
Chemical constitution of Prepared Powders as determined by XRF and ICP
Chemical constitution of green powders, showing the calculated and measured molar ratios
Ca/(P + Si)
Ca/(P + Si)
Chemical constitution of green powders, showing the calculated and measured Si concentration in wt%
Difference in composition of Si-HA as measured by ICP
Main crystalline phases determined by XRD
Lattice parameters and the average crystallite size of samples calcined at 900°C as calculated from XRD
Average crystallite size (nm)
d is the lattice distance obtained from XRD results are shown in Table 5.
All samples with silicon or/and carbonate substitution showed a decrease in the a-axis and an increase in the c-axis of the unit cell of hydroxyapatite.
Main constituting groups of prepared powders determined by FTIR
Moreover, two additional IR bands are detected in the IR spectra of Si-HA (with higher Si percent) at ~822 cm−1, and ~800 cm−1, respectively. The latter band appearing at 800 cm−1 is assigned to Si-O-Si vibration modes of (SiO4)4- groups which have been polymerized as previously reported .
Activity of prepared powders in SBF
All green discs of the different hydroxyapatites showed slightly alkaline effect on pH between 7.1 to 7.4 but less than the SBF over the periods of immersion. The heat-treated samples on the other hand, showed relatively alkaline effect on pH of SBF. A variation in pH is recorded demonstrated by alternatively decreasing and increasing throughout the different durations, but always above the control SBF pH for Si-CHA sample.
The uptake of P by the different green HA disc samples is relatively high, samples consumed most of the P supplied by the SBF solution depending on the immersion period. It reaches its optimum after 9 days by all samples when the P of the SBF is consumed, as demonstrated in Figure 10. The fired discs, showed less amount of uptake and gradually increases with the period of immersion as evident from the percentage recorded in the solutions (Figure 11).
Results of green and fired discs of the different hydroxyapatite samples show an uptake of sodium from the solution (Figures 12 and 13). The major uptake is displayed by the HAs sample. It even consumed most of the sodium ion in the solution after the two last periods 9 and 14 days. All samples nearly consumed the sodium ions from the SBF solution after 5 days.
The silicon substituted hydroxyapatite green and fired disc samples showed a release of silicon ion into the solution of SBF, as shown in Figures 14 and 15. Maximum release is displayed by the Si-CHA sample after the period of 14 days.
EDS analysis is performed on the sample top surface for all the substituted hydroxyapatites, as fired samples. It shows that these precipitates are crystalline materials like the biological apatites, rich in Ca, 35.08 wt% and P 21.67 wt% and contain amounts of C, 35.82 wt%, Na, 0.13 wt% and Si, 7.30 wt%, in the case of Si-HA sample, and Ca, 48.34 wt%, P 24.06 wt%, C 26.78 wt%, Na 0.30 wt% and Si, 0.52 wt%, in the case of Si-CHA sample. Therefore, the Ca/P molar ratios of these newly formed apatites are different from that of the stoichiometric value of HA of 1.67, by decreasing or increasing due to the substitution of the incorporating ions from SBF such as Na or Si/CO3 ions for calcium or phosphate in HA lattice.
In the present work, the calculated molar ratio; Ca/(P+Si) was < 1.67 of Si-HA powders prepared with excess Si. The content of P as determined by XRF, represents 91.8% of HA and Si accounts for the 28.45% rest, (in terms of XSi; XSi which is about 60.25% of the initial value). The recorded reduction in P and Si concentrations, was compensated by the introduction of the carbonate that was detected by FTIR, as it occupies the (PO43−) sites in the HA lattice. The amount of Si measured by XRF and ICP was 4.0 and 1.2 wt%, respectively. This indicates that not all the added silica 4.0 wt% entered in the HA lattice. Only the percent determined by ICP as a result of the dissolution of the prepared powder with the Si encountered in the lattice. The rest silica was transformed into polymerized silica that was amorphous not identified by XRD and not easily dissolute. Therefore, the main Si-O-Si bands corresponding to silica are identified by FTIR.
The reason for this polymerization is the competition between (CO32−) and (SiO44−) to substitute for the (PO43−) groups in HA structure. The charge difference resulting from the substitution of (SiO44−) for (PO43−) in HA, is compensated by loss of OH−, which is limited by the number of OH ions that can be extracted from the HA structure.
The excess silicate species that failed to substitute into HA lattice, polymerized on the surface of the prepared HA grains. This amorphous phase affects the sharpness of the XRD peaks becoming wider and less intense. This polymerization is ensured by the appearance of the new band at 800 cm−1 corresponding to the Si-O-Si stretching modes. Balas et al.  and Tang et al.  detect the polymerization behavior. Balas et al.  reported that an increase of the silicon content up to 1.6 wt% leads to the polymerization of the silicate species at the surface, that is readily recorded for 1.5 wt% by Tang et al.  They explained the phenomenon as the charge difference between (SiO44−) and (PO43−) compensated by the introduction of (CO32−) beside the silicate in the lattice. Yet, the (CO32−) is preferred to the silicate in the lattice. Moreover the substitution of (SiO44−) for (PO43−) in HA charge is compensated by loss of OH− extracted from the structure. So when the TEOS content increases the silicate species that could not incorporate in the lattice polymerize on the HA surface. This cause the XRD peaks to widen becoming less intense.
No other phosphate or silicate phases are recorded in the XRD pattern of Si-HA. The incorporation of silicon into the HA was previously explained by Gibson et al.  Silicon atoms substitute for P in the center of the tetrahedron with the four O atoms at the corners. The radius of Si4+ is greater than that of P5+, and the average length of the Si-O bonds (0.162 nm) is greater than that of the P-O bonds (0.152 nm, Boyer et al. ). The radius of the (PO4) tetrahedron would be expected to be smaller than that of the (SiO4) tetrahedron, which results in a change of HA lattice constants, as was explained by Balas et al.  and Tang et al. .
The recorded change in lattice parameters determined through the (hkl) peaks positions of apatites from XRD is a decrease in the a-axis and an increase in the c-axis of the unit cell of HA.
The XRD patterns obtained in the present study shows the peaks broader and less intense compared with pure HA attributed to the ill-crystalline nature of the product, accompanying the formation of hydroxyl vacancies, caused by the isomorphous substitution of (PO43−) by (SiO44−).
The multi-substituted HA samples (Si-CHA) showed high solubility for silicon ion, over that of the sample containing silicon, in spite of the low substituting amount of silicon in them, 0.523 wt% for Si-CHA, as compared to 4.0 wt% for Si-HA.
The immersion of the apatite disks in SBF solution produces noticeable changes in the chemical composition of the solution. Balas et al.  reported a rapid decrease in calcium ion at the beginning of the reaction that reaches a quasi-stationary state after 3 weeks. The hydroxyapatite which does not contain silicon shows the lower activity in trapping calcium from the solution. The calcium consumption by the samples is proportional to the decrease of the pH. On the other hand, no significant change in the phosphorus concentration is observed in the first two weeks, but it began to increase after 3 weeks, indicating dissolution of the surface layer. Phosphorus remains essentially in equilibrium with the solid in the first two weeks with no remarkable change.
The decrease of pH produced by this reaction would enhance the solubility of the apatite, which increases with the H+ ion concentration, indicating dissolution of the surface layer. Sprio et al.  reported a release of calcium ions with a rate more than doubled when granules of HA powders containing carbonate (Si-CHA compared to the carbonate-free HA, or (Si-HA).
The case reported by Balas et al.  is similar to what happened in the present work. The application of disc specimens furnish less surface to the action of SBF solution compared with the granulated powders tested by Sprio et al.  that subjects a high surface area to solution. Meanwhile the surface of the discs forms a center for the nucleation of the calcium phosphate layer providing the needed ions from the SBF solution. As a result a drop in both Ca2+ and p5+ ion concentrations of the SBF solution, in the first two periods followed by a dissolution of the surface layer.
The EDS of the precipitated calcium phosphate layer on the surface showed the incorporation of Na and C from the solution beside the Ca and P, and that was confirmed through the analysis of SBF for Na ion, a result was not recorded before. This confirms the fact that wherever Na ion is available in the solution it is incorporated beside the other substituted ions.
The present study succeeded in the preparation of synthetic multi-substituted hydroxyapatite nano powders; namely, Si-HA and Si-CHA, by using the wet chemical method. The chemical analysis confirmed the presence of the substituting atoms in the final HA powders. No secondary phases are found to contaminate the substituted HA, except for that containing initial amount of carbonate ions, Si-CHA, where β-TCP formed.
The ion substitution in the crystal lattice of HA caused a change in the unit cell dimensions and affected the degree of crystallization of the produced powders.
The activity as measured by immersion in SBF solution was higher for the prepared powders over the un-substituted HA. The HA that with simultaneous occupation of the phosphate site by silicate and carbonate ions, exhibit the highest solubility and a faster release, compared with carbonate-free powder.
All prepared powders took sodium ion from the SBF solution during immersion which was not recorded before.
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