Photoluminescent Properties of Hydroxyapatite and Hydroxyapatite/Multi-Walled Carbon Nanotube Composites

: Hydroxyapatite (HAp) and hydroxyapatite/multi-walled carbon nanotube (MWCNT) composites were obtained by the co-precipitation method, followed by ultrasound-assisted and microwave radiation and thermal treatment at 250 ◦ C. X-ray diffraction (XRD) conﬁrmed the presence of a hexagonal phase in all the samples, while Fourier-transform infrared (FTIR) spectroscopy eluci-dated the interaction between HAp and MWCNTs. The photoluminescent technique revealed that HAp and the composite with non-functionalized MWCNTs present a blue luminescence, while the composite with functionalized MWCNTs, under UV-vis radiation shows an intense white emission. These ﬁndings allowed presentation of a proposal for the use of HAp and HAp with functionalized MWCNTs as potential materials for optoelectronic and medical applications.


Introduction
Hydroxyapatite [Ca 10 (PO 4 ) 6 (OH) 2 ] is a bioceramic material used in medical applications [1] and widely studied due to its compatibility with the hydroxyapatite (HAp) present in human bones and other tissues of the body [2]. Furthermore, hydroxyapatite is naturally found in vertebrate hard tissues [3] and invertebrate shells [4]. Currently, hydroxyapatite is used for other purposes, e.g., as a heterogeneous catalyst [5], an adsorbent [6], a source of biofuel cells [7], a bioimaging agent [8], in glassy carbon electrodes [9], and in drug-delivery carriers [10].
Recently, bioimaging agents from HAp have been reported to monitor certain changes in the human body owing to its characteristic excitation and emission profiles. To improve its photoluminescent properties, hydroxyapatite has been synthesized with a number of ions partially replacing Ca 2+ , in this case of transition metals such as Fe 3+ [11] and Mn 2+ [12], or rare earth elements such as Tb 3+ , La 3+ , Er 3+ , Dy 3+ , Eu 3+ , and Gd 3+ [13,14]. Several research studies have reported that the intensity of photoluminescence emissions from rare earth elements is strongly related to the surrounding ions and their concentration because they deliver the chemical environmental information and vibrating coupling among f-d or f-f electronic transitions [15]. However, these goals are not always achieved, and, as an example, there is the work of Chen et al., who observed quenching effects when doping HAp with the Fe 3+ ion [11]. Moreover, transition metals are toxic and have an aggregation-caused quenching (ACQ) effect on conventional fluorophores, thus excluding their practical application [16,17]. Therefore, the use of non-toxic materials and the elimination of the ACQ effect are required characteristics to favor the emission of light.
Several reports have focused on preparing composites from CNTs and other materials as metal oxides (ZnO, Fe 2 O 3 , TiO 2 ,), graphene, and bioceramic materials, such as HAp, to generate a synergistic effect [25,26]. The incorporation of MWCNTs into HAp, influences structural, optical, and mechanical properties that enhance biocompatibility, adhesiveness, and corrosion resistance [27]. Ma et al. reported the fluorescence of HAp with carbon quantum dots for biological applications [28]. In a different study, the cell imagining capacity was commonly evaluated at 405 and 488 nm by focal laser scanning microscopy. Emissions in the UV-visible range can transfer luminescence resonance energy to drugs that absorb in the visible range for real-time drug release monitoring [8]. Currently, research on imaging agents using carbon and HAp has been reported, but research in this area using CNTs has been extremely limited until now.
Different methods have been used to prepare composites from HAp and MWC-NTs, such as chemical precipitation, chemical vapor deposition, ball milling, ultrasonication, spark plasma sintering, electrodeposition, sol-gel, and co-precipitation methods [19,20,[29][30][31]. In this paper, HAp and HAp/MWCNT composites were synthesized by the co-precipitation method, followed by ultrasound-assisted and microwave radiation, using functionalized and non-functionalized MWCNTs with potential optoelectronic and medical applications. 1 v/v water-ethanol mixture) was added with constant stirring. The pH solution was adjusted with ammonium hydroxide (NH 4 OH) at values from 9 to 11. After 24 h, the mixture was ultrasonicated in a Cole-Parmer model 08895-04 ultrasonic bath for 2 h. Additionally, 1200 W microwave radiation was applied to the mixture for 10 min (Sharp model Carousel), which was then maintained with stirring for 24 h. The material was thoroughly washed with a distilled water/ethanol (1:1) mixture to eliminate the residual salts left from synthesis and dried at 100 • C for 2 h and 30 min in a Sev model MF3 muffle. Finally, the sample was ground in an agate mortar and then subjected to a heat treatment at 250 • C for 6 h (Sev model MF3) to obtain the HAp powder.

Composite Preparation
Two different types of MWCNTs were used in the composite samples. MWCNTs with oxygen-containing functional groups (OMWCNTs, carboxyl groups), were synthesized by using the Castle methodology [32], and MWCNTs were purchased from Timesnano. In each sample, 25 mg of nanotubes were dispersed in 2.5% of Triton X100 solution to prevent agglomeration. Dispersed nanotubes were added to the HAp precursor as shown in Figure 1, practically following the HAp preparation route to obtain the HAp/OMWCNT and HAp/MWCNT composites.

Composite Preparation
Two different types of MWCNTs were used in the composite samples. MWCNTs with oxygen-containing functional groups (OMWCNTs, carboxyl groups), were synthesized by using the Castle methodology [32], and MWCNTs were purchased from Timesnano. In each sample, 25 mg of nanotubes were dispersed in 2.5% of Triton X100 solution to prevent agglomeration. Dispersed nanotubes were added to the HAp precursor as shown in Figure 1, practically following the HAp preparation route to obtain the HAp/OMWCNT and HAp/MWCNT composites.

Characterization
X-ray powder diffraction (XRD) patterns were collected at the Elettra Synchrotron Trieste (Trieste, Italy), on XRD1 beamline, with these settings: in the 2θ range from 0 to 50° at λ = 1 Å. The samples were placed in a borosilicate glass capillary at a 360° rotation and exposed for 30 s. The standard reference used was NIST lanthanum hexaboride (LaB6). Diffraction images were obtained and integrated using the Fit2d program to extract the patterns as a function of 2θ. The PDF-4+2019 database from ICDD was used to identify the phases in each sample [33]. Refinement analyses were performed using the BGMN/Autoquan software version 4.2.22 [34] with the graphical user interface Profex version 4.3.2 [35]. The background profile was fitted combining a Lagrange polynomial and an empty capillary scan measured under the same sample conditions. Crystallographic information of the hexagonal HAp phase was taken from ICSD-PDF-2: 01-074-0565, and it was fixed in all refinements. Anisotropic crystallite size and isotropic microstrains were considered for line broadening. Additionally, texture in all samples was considered by scale factor. FTIR spectroscopy measurements were performed on a Ni-coletTM iSTM 10 FTIR spectrophotometer (Thermo Fisher Scientific, Waltham, MA, USA) from 4000 to 650 cm −1 . The morphology was determined using the FEI-ESEM-Quanta 200 scanning electron microscope (SEM) (FEI, Hillsboro, OR, USA). Photoluminescent (PL) experiments were conducted on a NanoLog spectrofluorometer (Horiba NanoLog model FL-1057, Tokyo, Japan), and the materials were excited with a He-Cd laser at 325 nm and analyzed from 350 to 850 nm. Compositional analysis was obtained by the energy dispersive spectroscopy (EDS) technique, using a Jeol JSM-6610LV scanning electron microscope (SEM) with a Cu Kα (20 kV) excitation source (JEOL, Ltd, Tokyo, Japan), and by X-ray fluorescence spectroscopy (XRF), using beamline IDEAS from Canadian Light Source Inc. (Saskatoon, Canada) in the reading range from ~2 KeV to 13.5KeV.

X-ray Diffraction
The XRD powder patterns of the HAp, HAp/OMWCNT, and HAp/MWCNT samples are shown in Figures 2b-d. The most intense Bragg peaks were identified by the 01-074-

Characterization
X-ray powder diffraction (XRD) patterns were collected at the Elettra Synchrotron Trieste (Trieste, Italy), on XRD1 beamline, with these settings: in the 2θ range from 0 to 50 • at λ = 1 Å. The samples were placed in a borosilicate glass capillary at a 360 • rotation and exposed for 30 s. The standard reference used was NIST lanthanum hexaboride (LaB 6 ). Diffraction images were obtained and integrated using the Fit2d program to extract the patterns as a function of 2θ. The PDF-4+2019 database from ICDD was used to identify the phases in each sample [33]. Refinement analyses were performed using the BGMN/Autoquan software version 4.2.22 [34] with the graphical user interface Profex version 4.3.2 [35]. The background profile was fitted combining a Lagrange polynomial and an empty capillary scan measured under the same sample conditions. Crystallographic information of the hexagonal HAp phase was taken from ICSD-PDF-2: 01-074-0565, and it was fixed in all refinements. Anisotropic crystallite size and isotropic microstrains were considered for line broadening. Additionally, texture in all samples was considered by scale factor. FTIR spectroscopy measurements were performed on a NicoletTM iSTM 10 FTIR spectrophotometer (Thermo Fisher Scientific, Waltham, MA, USA) from 4000 to 650 cm −1 . The morphology was determined using the FEI-ESEM-Quanta 200 scanning electron microscope (SEM) (FEI, Hillsboro, OR, USA). Photoluminescent (PL) experiments were conducted on a NanoLog spectrofluorometer (Horiba NanoLog model FL-1057, Tokyo, Japan), and the materials were excited with a He-Cd laser at 325 nm and analyzed from 350 to 850 nm. Compositional analysis was obtained by the energy dispersive spectroscopy (EDS) technique, using a Jeol JSM-6610LV scanning electron microscope (SEM) with a Cu Kα (20 kV) excitation source (JEOL, Ltd., Tokyo, Japan), and by X-ray fluorescence spectroscopy (XRF), using beamline IDEAS from Canadian Light Source Inc. (Saskatoon, SK, Canada) in the reading range from~2 KeV to 13.5 KeV.

X-ray Diffraction
The XRD powder patterns of the HAp, HAp/OMWCNT, and HAp/MWCNT samples are shown in Figure 2b-d. The most intense Bragg peaks were identified by the 01-074-0565 card from the PDF-2 database [36], unambiguously confirming, as expected, a hexagonal HAp phase and excluding the less common monoclinic HAp [37]. Figure 2a,e also present the reflections associated with MWCNTs and OMWCNTs (002), (100), and (004). The results indicated that the intensity of OMWCNTs decreased because their surface area was modified by functionalization, as reported in [27]. However, MWCNT reflections were not observed in the composite samples because they overlapped with HAp reflections. Nevertheless, differences in crystallinity between HAp and composites were observed in the peak intensity and definition in both powder patterns. During synthesis, the carbon nanotubes acted as nucleation centers for HAp, which allowed crystallites to grow on the MWCNT surface, depending on the type of carbon nanotubes contained in the samples [38]. The crystallite size of the samples was estimated by Rietveld analysis (see Table 1). Anisotropic crystallite size was obtained as expected due to the hexagonal lattice. Hydroxyapatite crystallite sizes along the 100 crystallographic direction of HAp and HAp/MWCNT were almost equal to 10 nm. Crystallite sizes along the 001 crystallographic direction of HAp were slightly greater that those of the HAp/MWCNT composite, which indicated that the crystallite sizes in both samples were almost the same. The pattern intensity in the HAp/MWCNT sample was~50% greater than that of the HAp. The HAp/OMWCNT crystallite sizes were 15.74 nm along 100 and 30.9 nm along 001 crystallographic directions, respectively, which were greater than those obtained in the HAp and HAp/MWCNT samples. Peak intensity in the HAp/OMWCNT sample was 70% greater than that in the HAp, which is shown in Figure 2d. Adding the MWCNT sample did not change the crystallite size of the HAp; however, adding the OMWCNT sample did increase it. This suggests that the OMWCNTs interact differently from the non-functionalized MWCNTs with the precursors of HAp under experimental conditions. Adding non-functionalized SWCNTs resulted in an increased crystallite size in the same way as the HAp [20], whereas in the work by Arul et al., the incorporation of functionalized MWCNTs caused a smaller crystallite size than that of the HAp [27]. The differences may be attributed to the working temperature during synthesis, because the experiments were carried out at room temperature in this work, whereas temperatures of 50 and 90 • C, respectively, were used in the reports cited above.
The Rietveld refinement did not indicate significant variations in the cell parameters a and c or in the cell volume. However, the HAp sample showed the greatest cell volume, and the HAp/OMWCNT composite has the greatest HAp crystallite size, while the microstrain had the smallest size, as expected according to this sample's crystallinity. Table 1 shows the fitting parameters determined through a comparison between the experimental and calculated diffraction patterns. Figure 3 shows the Rietveld difference plot, where the fluctuation indicates a reasonable fitting between the observed and calculated diffraction patterns. The lower band shows the fitting deviation of original diffractograms.    Figure 3 shows the Rietveld difference plot, where the fluctuation indicates a reasonable fitting between the observed and calculated diffraction patterns. The lower band shows the fitting deviation of original diffractograms.  Figure 4 illustrates the characteristic vibrational modes of HAp identified and shown in the IR spectrum of each sample. Table 2 enlists the specific vibrational modes detected  Figure 4 illustrates the characteristic vibrational modes of HAp identified and shown in the IR spectrum of each sample. Table 2 enlists the specific vibrational modes detected in each sample. The weak band at 3572 cm −1 was assigned to the OH − group. The vibrational modes related to PO 4 3− ions were found at approximately 1000 cm −1 , and their resonances were identified at the 1950-2200 cm −1 interval [39]. As shown in the inset in Figure 4, the band at 1630 cm −1 refers to adsorbed water [39,40], which appeared in both HAp and the HAp/OMWCNT samples. The band at 1325 cm −1 that appeared in the HAp/OMWCNT sample is associated with the interaction between the Ca 2+ ion and the COO − group on the OMWCNT sample. According to [38], this band confirms the interaction between HAp and MWCNTs, which was corroborated by the XRD results. In addition, the band deconvolution approximately at 875 cm −1 showed a substitution of the OH − (870 cm −1 substitution type A) and PO 4 3− (877 cm −1 substitution type B) ions for the CO 3 2− ion. The contribution of these substitutions was observed at the 1410-1540 cm −1 interval [39,41]. Bands attributed to the substitution in HAp had 17.74 and 17.04 a.u. for substitution types A and B, respectively. Band areas decreased significantly in the composites. The HAp/MWCNT sample had 9.35 and 12.30 a.u., respectively, while the HAp/OMWCNT sample had 7.37 and 12.45 a.u., respectively. Figure 5 displays the probable interaction between HAp and OMWCNT. The FTIR results suggested that the Ca 2+ ion from HAp is linked to the carboxylic groups from OMWCNT. Therefore, the nucleation centers promote the HAp growth on the surface of OWCNT. The HAp was modeled using VESTA software considering 100 atoms, while the OMWCNT was modeled with a Nanotube Modeler JCrystalSoft 1.8.0, and Spartan 1.1.4 using 676 atoms. The interaction of HAp and MWCNT could be explained by Van der Waals forces; however, theoretical studies are required to determine the bond energies.   Figure 5 displays the probable interaction between HAp and OMWCNT. T results suggested that the Ca 2+ ion from HAp is linked to the carboxylic groups fro WCNT. Therefore, the nucleation centers promote the HAp growth on the su OWCNT. The HAp was modeled using VESTA software considering 100 atoms, w OMWCNT was modeled with a Nanotube Modeler JCrystalSoft 1.8.0, and Spart using 676 atoms. The interaction of HAp and MWCNT could be explained by Waals forces; however, theoretical studies are required to determine the bond ene    Figure 5 displays the probable interaction between HAp and OMWCNT. T results suggested that the Ca 2+ ion from HAp is linked to the carboxylic groups fr WCNT. Therefore, the nucleation centers promote the HAp growth on the su OWCNT. The HAp was modeled using VESTA software considering 100 atoms, w OMWCNT was modeled with a Nanotube Modeler JCrystalSoft 1.8.0, and Spar using 676 atoms. The interaction of HAp and MWCNT could be explained by Waals forces; however, theoretical studies are required to determine the bond en

Morphological Analysis
The surface morphologies of MWCNT, OMWCNT, HAp, and HAp/OMWC shown in Figure 6. Figure 6a presents the aligned, straight, and smooth surfac MWCNT in comparison to the aligned, straight, and wavy surface of the OM These results suggest that the functionalization of nanotubes with carboxyl gro modify the morphology. Figure 6c shows the semi-spherical shape of HAp due to

Morphological Analysis
The surface morphologies of MWCNT, OMWCNT, HAp, and HAp/OMWCNT are shown in Figure 6. Figure 6a presents the aligned, straight, and smooth surface of the MWCNT in comparison to the aligned, straight, and wavy surface of the OMWCNT. These results suggest that the functionalization of nanotubes with carboxyl groups can modify the morphology. Figure 6c shows the semi-spherical shape of HAp due to the fast nucleation during synthesis. Figure 6d displays the HAp agglomerates formed by aggregation. The OMWCNTs are not visible because the HAp covers them. nucleation during synthesis. Figure 6d displays the HAp agglomerates formed by aggregation. The OMWCNTs are not visible because the HAp covers them.

Compositional Analysis
The compositional analysis by EDS showed that, as expected, all the samples contained Ca, P, and O, and only the composites contained C. This analysis also revealed that the HAp/OMWCNT sample had some impurities of Al and Si from cross-contamination, Fe traces from the MWCNT sample, and Br traces from the surfactant used in the synthesis; all are shown in Table 3. Then, a synchrotron XRF analysis detected several impurities of Ar, Ni, Zn, and Mo from cross-contamination in all the samples, because none of the reagents was composed of these elements. On the other hand, all the samples had Br residues from the surfactant, confirming that the HAp/OMWCNT sample also contained Fe, as shown in Figure 7a-c. Finally, the Al and Si content was discarded from the HAp/OM-WCNT sample (detected by EDS), because these elements were not detected by the synchrotron XRF analysis, which is a very sensitive and reliable technique. Besides that, the amounts of these elements were outside the scope of consideration.  [42], but when HAp is synthesized by the precipitation method, that expected ratio is lower [43], as shown in Table 3. The composites' Ca/P ratio was higher than HAp, which is attributed to the substitution of the PO4 3− ion for the CO3 2 ion or tetrahedral hydroxyl [42]. The HAp/OMWCNT sample with substitution type B (observed by FTIR) had a slightly higher amount of CO3 2− ions than the PO4 3− ions, thus resulting in an increased Ca/P ratio in the composites.

Compositional Analysis
The compositional analysis by EDS showed that, as expected, all the samples contained Ca, P, and O, and only the composites contained C. This analysis also revealed that the HAp/OMWCNT sample had some impurities of Al and Si from cross-contamination, Fe traces from the MWCNT sample, and Br traces from the surfactant used in the synthesis; all are shown in Table 3. Then, a synchrotron XRF analysis detected several impurities of Ar, Ni, Zn, and Mo from cross-contamination in all the samples, because none of the reagents was composed of these elements. On the other hand, all the samples had Br residues from the surfactant, confirming that the HAp/OMWCNT sample also contained Fe, as shown in Figure 7a-c. Finally, the Al and Si content was discarded from the HAp/OMWCNT sample (detected by EDS), because these elements were not detected by the synchrotron XRF analysis, which is a very sensitive and reliable technique. Besides that, the amounts of these elements were outside the scope of consideration.
The typical Ca/P ratio in HAp is 1.67 [42], but when HAp is synthesized by the precipitation method, that expected ratio is lower [43], as shown in Table 3. The composites' Ca/P ratio was higher than HAp, which is attributed to the substitution of the PO 4 3− ion for the CO 3 2 ion or tetrahedral hydroxyl [42]. The HAp/OMWCNT sample with substitution type B (observed by FTIR) had a slightly higher amount of CO 3 2− ions than the PO 4 3− ions, thus resulting in an increased Ca/P ratio in the composites.

Photoluminescence Spectroscopy
Figure 8a-c presents the photoluminescence spectra of the three samples and their corresponding deconvolution that shows each contribution in the luminescent process. Arabic numerals were used to label the HAp contribution bands, whereas those bands that belong to the MWCNT contribution were labeled with uppercase Roman numerals. The curves were deconvoluted using the Gaussian function in OriginPro 2019b software. The HAp and HAp/OMWCNT samples were adjusted to eight bands, while the HAp/MWCNT sample was adjusted to nine bands. Table 4 presents the exact position of each curve and the assignment to each contribution to explain their behavior. Figure 8a displays the HAp spectra with a strong emission at 410 nm (blue), which is attributed to a significant amount of vacancy defects in the lattice due to the synthesis process, as reported by Zhang et al., where HAp did not reveal luminescence by itself [44]. These defects may be related to oxygen vacancies from the PO4 3− and OH − ions [45][46][47][48]. The FTIR spectra confirmed oxygen vacancies and loss of a complete OH − ion because the bands were weak. No contribution of HAp impurities to photoluminescent properties was observed, according to the works mentioned above.
In contrast, the HAp/OMWCNT composite spectrum indicated the effect of excitons from the OMWCNT sample, which was evidence of the peak shift to higher wavelengths, further distorting the peak symmetry [49]. Figure 8 shows that the HAp and HAp/MWCNT samples had a maximum photoluminescence emission at the 411 nm wavelength, while the HAp/OMWCNT sample had it at the 496 nm wavelength. These wavelength shifts in the spectrum occurred due to the presence of the functionalized MWCNTs, as reported by Sun et al., who found a maximum photoluminescence emission at 610 nm; thus, it is evident that the OMWCNT sample contributed to those higher wavelength shifts [50]. When the HAp and OMWCNT samples combined their properties during synthesis at 250 °C, there was no need to used high temperatures to obtain a composite material that reached the redshift in the photoluminescence emission [41].

Photoluminescence Spectroscopy
Figure 8a-c presents the photoluminescence spectra of the three samples and their corresponding deconvolution that shows each contribution in the luminescent process. Arabic numerals were used to label the HAp contribution bands, whereas those bands that belong to the MWCNT contribution were labeled with uppercase Roman numerals. The curves were deconvoluted using the Gaussian function in OriginPro 2019b software. The HAp and HAp/OMWCNT samples were adjusted to eight bands, while the HAp/MWCNT sample was adjusted to nine bands. Table 4 presents the exact position of each curve and the assignment to each contribution to explain their behavior. Figure 8a displays the HAp spectra with a strong emission at 410 nm (blue), which is attributed to a significant amount of vacancy defects in the lattice due to the synthesis process, as reported by Zhang et al., where HAp did not reveal luminescence by itself [44]. These defects may be related to oxygen vacancies from the PO 4 3− and OH − ions [45][46][47][48]. The FTIR spectra confirmed oxygen vacancies and loss of a complete OH − ion because the bands were weak. No contribution of HAp impurities to photoluminescent properties was observed, according to the works mentioned above.
In contrast, the HAp/OMWCNT composite spectrum indicated the effect of excitons from the OMWCNT sample, which was evidence of the peak shift to higher wavelengths, further distorting the peak symmetry [49]. Figure 8 shows that the HAp and HAp/MWCNT samples had a maximum photoluminescence emission at the 411 nm wavelength, while the HAp/OMWCNT sample had it at the 496 nm wavelength. These wavelength shifts in the spectrum occurred due to the presence of the functionalized MWCNTs, as reported by Sun et al., who found a maximum photoluminescence emission at 610 nm; thus, it is evident that the OMWCNT sample contributed to those higher wavelength shifts [50]. When the HAp and OMWCNT samples combined their properties during synthesis at 250 • C, there was no need to used high temperatures to obtain a composite material that reached the redshift in the photoluminescence emission [41].
In the figure above, the HAp/MWCNT sample has a band profile similar to that of HAp but a lower photoluminescence intensity due to the lattice arrangement, as previously observed in the XRD section. Crystals 2021, 11, x FOR PEER REVIEW 10 of 14 In the figure above, the HAp/MWCNT sample has a band profile similar to that of HAp but a lower photoluminescence intensity due to the lattice arrangement, as previously observed in the XRD section.

Conclusions
Luminescent HAp and composites were synthesized by the co-precipitation method followed by ultrasound bath and microwave radiation. The HAp sample had a strong blue emission because of oxygen defects in the lattice, whereas the HAp/MWCNT sample had a weak blue emission. The HAp/OMWCNT composite had a white emission due to the interaction between Ca 2+ from HAp and carboxylic groups from OMWCNTs. In composite materials, OMWCNT contributed to the maximum photoluminescence emissions. The hexagonal phase in HAp and composites was obtained at 250 • C by the synthesis method used, in contrast to a higher temperature in previous reports. Here, we have reported a simple method to obtain HAp and composite materials without using rare earth elements in the synthesis.
The HAp/OMWCNT composite showed photoluminescent properties that make it a promising material for cell imaging and drug-release monitoring. This composite emits photoluminescence in the UV-visible range, where most confocal laser scanning microscopes are equipped. Drug release could be monitored by recovering luminescence from materials emitting in this wavelength range. Furthermore, the photoluminescence emission intensity of the composites obtained was comparable to materials used in bioimaging and biosensing. Similarly, relevant applications of HAp and HAp/OMWCNT composite may be developed in optoelectronics (light emitting diodes) owing to the great photoluminescent properties and salient characteristics of OMWCNTs.