Structural Characterization of Novel Cerium Phosphate Glass Ionomer Cements (GICs) Doped with GaCl (Phthalocyanine)

Cerium Pyrophosphate glass is prepared and investigated by different structural techniques. Resin modified glass io n omer cements (RGICs) of pyro cerium phosphate (40CeO₂-60P₂O _s ) composition doped with different concentration s from GaCl Phthalocyanine (C₃₂H₁₆ClGaN₈) have been also prepared and studied for the first time. Different techniques have been applied to shed light on the structural changes induced upon addition of GaCl-Phthalocyanine. The corresponding changes in material structure are widely approved by results of ³¹P magic angle spinning nuclear magnetic resonance (MAS-NMR), X-Ray diffraction and FTIR spectroscopy. The network structure of both base glass and GIC free from C₃₂H₁₆ClGaN₈ is confirmed to be amorphous. Doping even with little concentration from GaCl-Phthalocyanine leads to changing the network structure from amorphous to a highly crystalline one. Formulation of GaCl-Phthalocyanine with water soluble acid leads to monocrystalline structure due to monoclinic lattice structure of Phthalocyanine. Carbonated hydroxyl cerium and gallium phosphate structural phases are evidenced to be formed upon GaCl-Phthalocyanine addition. Presence of such bioactive phases can support that the prepared GICs of considerable C₃₂H₁₆ClGaN₈ concentration (1 and 1.5 mol%) can be applied as biocompatible materials used in biodental applications. The morphologies of some selected samples were characterized by SEM. The micrographs have revealed that formulating of cerium phosphate powder of the amorphous glass with polymeric acid successfully led to the formation of CePO₄-H₂O nanofibrous bundles. But formulation with GIC containing GaCl-Phthalocyanine can simply form co-aligned and elongated nanofibers (15 - 40 nm thick and up to ca. 1.2 m long). The formed nanofibers are mainly consisted of hydrated and carbonated CePO₄ and GaPO₄ nanocrystals. The hardness of the cemented material increases with increasing GaCl-Phthalocyanine concentrations.

• Glass Ceramics-GIC-Crtstalline Structure
• Spectroscopy

1. Introduction

There is an increasing interest in metal phosphates composites due to their relevance in biology and materials science [1] [2] . It is known that addition of modifier oxide to P₂O₅ leads to disruption of P-O-P bridges [3] [4] . At first, PO₄ branching units in Q³ configuration (Q is phosphors cation, n is the number of bridging bonds) can form metaphosphate composition. The latter species are transformed to two-connected middle units of Q² configuration which represent pyrophosphate composition. In the end, isolated PO₄ units (Q¹ and Q⁰ orthophosphate) are occurred at extremely high concentration from modifier oxide (>50 mol%). At metaphosphate composition, i.e. in glasses of less than 30 mol% modifier oxide and more than 70 mole% P₂O₅, chain and/or ring structures of PO₄ middle groups are formed. With further modifier addition, the chains become shorter and at the pyrophosphate composition, i.e. in glasses of 40 mole% modifier, the PO₄ dimers (molecular complex consisting of two identical molecules linked together) are the dominate species. The corresponding changes are widely presented by results of ³¹P magic angle spinning nuclear magnetic resonance (MAS NMR) and vibrational spectroscopy. Many of such results are reviewed in references [3] [4] .

When the powder of the oxide glass is formulated with some types of weak polymeric acids, the well-formed material is called glass ionomer cement. Expression of a glass-ionomer cement (GIC) is devoted only to a material which involves a proper acid-base reaction as a part of its setting process [5] [6] . The acid is a water-soluble polymer and the base is a special powder of specific type of glass or glass ceramic of basic character. P₂O₅ based glass systems are the most recommended type because its basic reaction is higher than that of silicate and borate glasses. Therefore, the origin of glass ionomer cements should be based on reaction between acid and the powder of phosphate glass.

Most of simple and conversional GICs were brittle materials. Therefore several trials have been devoted to enhance the physical properties by the addition of some types of supported materials such as TiO₂-Cr₂O₃-Al₂O₃, Ag₂O, ZrO, SrO, CrF₂ [3] [7] [8] [9] . In addition, they play the role of compatibility enhancement of the material to be most proper in the field of bio-applications [10] [11] . The additive materials can also stimulate the nucleation and crystallization processes of hydroxyphosphate phases which are the essential mineral phase of bone and teeth. Some specific types of materials can be added as dopant to play an effective role in improving the physical properties and widening the range of applications [3] [4] .

GICs are considered the most appropriate materials in the field of bio-dental applications [4] [5] [6] [7] [8] . Several types of (MGICs) are applied as alternatives for both amalgam and resin composites which possess several shortcomings such as: 1) Resin composite lacks the characteristic of good adhesion to the bone of tooth; 2) It undergoes polymerization shrinkage which leads to crack propagation on setting; 3) Amalgam is corrosive material and its vapor is toxic. From these reasons, (GICs) were considered to possess several advantages that resins and dental amalgam do not make.

Several types of GICs modified by specific types of supporting materials have been previously studied [3] [4] [5] [6] . But modification of GIC with GaCl-Phthalocyanine species (C₃₂H₁₆ClGaN₈) as an organic agent for nucleation, antimicrobial and crystallztion processes has not yet reported. Therefore this study is aimed to determine (for the first trial) the structure role of the dopant C₃₂H₁₆ClGaN₈ molecules in the modified pyro cerium phosphate based GIC.

2. Experimental

2.1. Material Preparation

Binary Cerium phosphate glass with composition 40CeO₂∙60P₂O₅ has been synthesized using analytical grade chemicals using ordinary melt quenching technique. Calculated batches of the starting raw materials were mixed including the appropriate amounts of CeO₂ and NH₄H₂PO₄ as a source of P₂O₅. The mixture was heated in a porcelain crucible at 300˚C for 30 min. in order to evaporate ammonia, water, and nitrogen. Then, the product was melted between 1100 to 1350˚C for an hour. To assure the homogeneity, the previous oxides were added to the melt in the crucibles in small parts and the melts were stirred before each addition. After refining, the melts were quenched on a stainless steel plate. The obtained glasses were homogenous, transparent and there was no sign of devitrification. Because of the phosphate glasses have higher tendency to absorb moisture, the glass samples were sealed with silica gel pellets in sacks of plastic and kept in desiccators until required. GICs were prepared by formulating the glass powder with a polymeric acid of type (Ketac Molar Easymix, Germany). They are mixed und swirled until a homogenous past is obtained.

2.2. Measurements

Infrared absorption spectra of the glasses were recorded in the range of 400 cm⁻¹ to 4000 cm⁻¹ at ambient temperature by a spectrophotometer type (Mattson 5000 FTIR spectrometer). The measurements were carried out on powdered glass samples which is mixed with KBr (1 wt%). The measurement process occurred immediately after the mixture compression with a load of 5 tons/cm².The distribution of Qⁿ of phosphate units can be obtained from ³¹P NMR spectra of some selected samples. The measurements were analyzed using a high resolution solid state MAS NMR type (JEOL RESONANCE GSX-500 spectrometer). The obtained spectra were recorded at high external magnetic field (11.747 T), at frequency of 160.47 MHz and spinning rate of 17 KHz. X-ray diffraction pattern was obtained by using X-ray diffractometer type (Philips PW 1729) with a compact analyzer system 1840 and 8203A/02 chart recorder. Surface modification and microstructure of glass samples were examined using a Scanning Electron Microscope (SEM) equipped with EDX unit. Operated and accelerating voltage of 25 KV, with a magnification up 400,000X and resolution for W. (3.5 nm) is the feature of the used SEM. The technique of gold plated samples has been applied. The average grain size of the various specimens was 60 µm.

3. Results and Discussion

Very low levels of GaCl-Phthalocyanine (0 - 1.5 mol%) within the glass ionomer cement of the cerium phosphate glass can drastically influence its propensity to crystallize as well as change structure and morphology of the final formed phases. Figure 1 reflects the effect of a small addition of the dopant material on the visual or appearance properties. Change the color from transparent yellow to green to dark blue may lead to precipitation of some crystalline phases containing gallium cations.

3.1. XRD Analysis

To understand how these small compositional changes affect the material structure via the doping process, different techniques and spectroscopic tools have been applied. Correlation between data obtained from these techniques can provide a unique insight into the structure of these GICs and how they change during phase separation and crystallization processes. Because of the large differences in molecular weight between the glass constituents, and particularly the significant effects of C₃₂H₁₆ClGaN₈, X-Ray diffraction is a highly informative technique for this type of research. In addition, local structural information on the main glass-forming elements of phosphate nuclei was obtained from solid-state NMR spectroscopy.

The addition of GaCl-Phthalocyanine has been shown to be very effective in enhancing the crystallization of GICs, as is shown in Figure 2. This is of particular interest as it enables control over the crystallization behavior of the studied GICs. Then very low levels of GaCl-Phthalocyanine have been shown to change the structure of the present investigated GIC systems and therefore this is also of interest. Mixing effect of CeO₂ and chlorogallium species in the matrix of GIC should play a good role in improvement of structure and properties of the material network and consequently induces high resistance to corrosion processes through formation of some types of fined grained crystals in the main matrix. In such situation, fine grained chloro-gallium phosphate crystals and/or hydroxyl cerium phosphate, gallium cerium chlorophosphate, and phthalocyanine dimmers are the most suggested formed phases. To confirm this aspect, changes of the PO₄ units in the corresponding glasses were also analyzed by XRD and FTIR spectroscopy.

Comparisons between XRD patterns of the studied materials with the Ga(PO₃)³ crystal [12] [13] were made. It was noteworthy realized that both XRD and FTIR spectra of GIC containing (C₃₂H₁₆ClGaN₈) involve very intensive sharp peaks even at a little addition of the dopant. This means that gallium chloride molecules are considered as good scatters for X-rays. This may because Ga-O bonds are longer than both P-O and Ce-O bonds. Thus FTIR and XRD spectra are well resolved. So X-ray diffraction experiments are excellent in a search for changes in Ga-O environments even if small concentration from the dopant material is added. Therefore, cerium phosphate based GIC were prepared only in a small range with molar fractions of C₃₂H₁₆ClGaN₈ (0 to 1.5 mol%).

The XRD patterns of investigated samples are shown in Figure 2. It illustrates the marked difference in structural changes between the reference glass sample

(cerium phosphate glass, spectra a), the reference C₃₂H₁₆ClGaN₈) GIC (spectra, b) and compares the percentage of the dopant in GICs systems (c, d and e). The spectra of the base glass of composition 40CeO₂-60P₂O₅ are presented by Figure 2(a). The corresponding spectrum exhibits a broad spectral band at low diffraction angles (25˚ - 40˚) confirming a structural disorder characteristic of amorphous network of the base glassy material. On the other hand, spectra (b) represent XRD patterns of the formulated C₃₂H₁₆ClGaN₈ with polymeric acid. It can observe that there are two characteristic sharp diffraction peaks (at about 23˚ and 34˚) representing the carboxyle groups balanced by gallium cations (COO)Ga. Crystal structure analysis of the two line spectra confirm the presence of hydroxyl gallium phthalocyanine type and chloro gallium phthalocyanine crystalline type of monoclinic structure [13] [14] [15] . The spectra (c), (d) and (e) represent XRD spectra of cerium phosphate based GIC containing different C₃₂H₁₆ClGaN₈ concentrations (0.5 and from 1 and 1.5 mol%) respectively. It can be shown that some sharp diffraction peaks are superimposed on the broad diffraction patterns (b) in GIC of 0.5 mol% C₃₂H₁₆ClGaN₈. These spectra may be considered to be formed from two components. One is due to the amorphous matrix of the glass (of spectra a) and the crystalline matrix of the resined C₃₂H₁₆ClGaN₈ (of spectra b). Therefore the obtain spectra of glass of 0.5 mol% GaCl is built from a broad hump with some sharp diffraction lines. More sharper diffraction peaks are appeared with increasing gallium chloride to reach 1.5 mol%. In such a case the broad diffraction hump is totally disappeared, (spectra d and e) which confirms the presence of the highest crystalline structure at these compositions. These changes are summarized in Figure 3, which represents change of crystallinity with glass composition. It can be shown from this figure that the crystallinty increases with increasing C₃₂H₁₆ClGaN₈ concentration to reach its saturated values at about 1 mol%.

Then from Figure 2 and Figure 3, one may expect that the crystallization

process is offered mainly by effect of galliumcholoride since the material containing even limited doping level (0.5 mol%) is crystallized prior to undergoing the second step of crystallization (at 1 and 1.5 mol%). The number of diffraction lines in all doped GIC is the same but change in intensities is the most observed changeable parameter. This means that the type of the formed crystalline phases is similar but the content of the separated phases increases with increasing C₃₂H₁₆ClGaN₈ concentrations. There are additional phases are formed by comparing spectra a and b. Besides the hydroxyl-gallium phthalocyanine and chloro-gallium phthalocyanine crystalline phases, GaPO₄ or GaCePO₄ hydrated and carbonated species are also formed in GICs matrix [15] [16] [17] [18] [19] . This interpretation may account on the presence of several diffraction lines in spectra of cerium phosphate based GIC modified by C₃₂H₁₆ClGaN₈ (spectra c, d, e). Presence of such crystalline hydroxyapatite phases are considered to be useful for the material to be used in the field of bio dental and bioactive application.

On mixing powder of binary CeO₂-P₂O₅ glass with acid (water-soluble polymer), the acid attacks the matrix of glass and C₃₂H₁₆ClGaN₈ resulting in surface degradation. As a result of degradation, release of metal ions such as cerium and gallium cations should occur. The released ions can react with the hydrated or the carbonated phosphate units and the carbonated hydroxyapaptite phases are constructed [10] [11] . Presence of different line spectra leads to formation of different phosphate groups containing cerium or gallium or both cations. Increasing of C₃₂H₁₆ClGaN₈ as a dopant material was found to enhance the cement structure via forming GaPO₄ crystalline species. The crystal structure of Ce₂Ga(HPO₃)₃(PO₃) exhibits a complicated 3D framework based on CeO₆ and GaO₆ octahedral connected by HPO₃ and H₂PO₃ anions via corner- or edge-sharing [10] [11] . Finally interactions between (COO)Ce and GaPO₄ species leads to formation of more crystallized phosphate phases containing Ga and Ce cations. These crystallite phases are relevant to support the fabrication of bone tissue engineering scaffolds from cerium phosphate bioglass which should exhibit tailored porosity, controlled crystallinity and enhanced bioactivity [14] [15] [16] .

3.2. FTIR and NMR Spectroscopy

Formation of the above mentioned crystalline phases is highly evidenced also from FTIR spectra of GIC containing different concentrations from GaCl-Phthalocyanine. The appearance of new sharp FTIR absorbance peaks (Figure 4) are assigned to Ga or Ce vibration in the crystalline carbonated cerium phosphate phase (poly acid salt). Figure 4 presents FTIR spectra of both glasses after and before the reaction with organic polymeric acid. The cement phase is only present in glass after the reaction process. The cement species are presented by presence of new splitting absorbance peaks around 1950 cm⁻¹ (Figure 4, curve b) which are totally absent in the glass before the reaction process (curve a). Due to the acid-base reaction, the surface of the glass becomes

a phousphours hydrogel (P-OH) which forces both gallium and cerium cations to link with hydrated phouphor units. Then on mixing powder of glass and liquid, the self cure polymerization reaction begin and setting can be occurred [6] [8] .

More evidences for acid-base reaction can be considered from NMR result of phosphors nuclei. It can be shown from Figures 5 (a)-(b) that the intensity and the fullwidth at half maximum (FWHM) of the NMR resonance peak are highly affected by the acid-base reaction. The intensity of the resonance NMR peak is decreased and FWHM is increased. These changes are considered as good evidences for the degradations processes which are simply produced due to the reaction between the glass and the acid [20] .

By considering FTIR absorbance spectra of doped samples (Figure 6), they exhibited many absorption bands at 3500, 3000, 1910, 1000, 1465, 1151 and 750 cm⁻¹. The presence of a large band at 3500 cm⁻¹ is corresponding to the O-H stretching frequency [6] [7] [8] . The peak at 1151 cm⁻¹ is assigned to the stretching vibration of the C-N bond of gallium phosohate structural units [6] [7] [8] , while the peak at 1465 cm⁻¹ is due to the deformation mode of phosphate species. The intensity of the peaks at 740 cm⁻¹ is decreased while peak at 1900 is increased with increasing GaCl Phthalocyanine concentrations. This behavior may lead to suggest that NBO component was frequently removed by effect of increasing dopant concentration. This may mean that the degradation induced by acid-base reaction could be amended by the dopant cations. This result is further supported, since presence of Ce-O-C or Ga-O-PO₄ bond formed by the interaction between cerium oxide and the carboxylate group of GIC or Ga are evidenced to be present (1680 cm⁻¹). The intensity of band at 1680 is grown and became resolved (Figures 6(b)-(d)). However, spectra shows the presence of a band at 3430 cm⁻¹ corresponding to the O-H stretching frequency and a band at 1676 cm⁻¹ to the bending vibration of associated water. The formation of Ce-O-C bond indicates that there is a degree of interaction between the organic and inorganic components via condensation reaction in the initial GIC precursor,

while this type of GIC strengthening can assist the formation of mesopores. The most to be noticed from Figure 6 that the absorbance peaks represented carboxyle groups (1680 cm⁻¹) is splited into differed components suggesting that the interaction is carried out due to GaCl Phthalocyanine modifications. In addition, in doped GIC, all FTIR spectra (Figure 6) clearly show sharpening of the peaks in the spectral region 600 - 1900 cm⁻¹ which is associated with crystalline phosphate units containing Ga(PO₄) or CePO₄ or both. Formation of such phases additionally accounts for the sharpening of the shoulder at about 600 cm⁻¹ with increasing C₃₂H₁₆ClGaN₈ concentration. However, it is seen that the sharpening occurs more rapidly from the first C₃₂H₁₆ClGaN₈ addition. In comparison with C₃₂H₁₆ClGaN₈ free glass, very clear changes can be seen in the region 500 - 1900 cm⁻¹. The peak developed at 590 may be explained by the presence of metallic ions such as Ga or Ce [13] [14] [15] . The typical crystalline phosphate or apatite split bands at 560 cm⁻¹ and 613 cm⁻¹ are clearly present for all Ga containing glasses. The spectra indicating the presence of crystalline phases which have another band at about 960 cm⁻¹ corresponding to the P-O stretch in the phosphate tetrahedron. As is clear from Figure 5, it can be observed that strong changes can be seen in the spectra with increasing C₃₂H₁₆ClGaN₈ concentrations.

Results based on both FTIR and XRD spectra have shown sharp peaks in glasses containing GaCl Phthalocyanine. The added agents should act as both stimulator for nucleation and crystallization of cerium phosphate phases which are the essential mineral phase of bone and teeth. Mixing effect of CeO₂ and GaCl plays a good role in improvement of hardness and compactness of the material network and consequently high corrosion resistance. Figure 7 represents changes of the hardness number with concentration. H_v increases frequenty with GaCl Phthalocyanine addition.

The fast increase of Hv (Figure 8) is considered as an additional evidence for acid-base reaction together with increasing doping concentration which was documented from both XRD and FTIR data. It can be shown from Figure 2 and Figure 6 that the intensity of XRD diffraction and FTIR absorbance peaks of GIC are highly affected by the doping concentration. The intensity of XRD, FTIR peak and the hardness number increase with increasing GaCl-Phthalocyanine concentrations. These changes give additional confirmation that C₃₂H₁₆ClGaN₈ can

simply activate the interaction of organic and the inorganic species which results in decreasing degradations processes that takes place by attacking the acid to the surface of the glass. As a consequence the hardness of the glass shows an effective increasing trend.

3.3. Morphological Studies (SEM)

Recent investigations have evidenced that the properties of CePO₄ nano species depend strongly on, morphology and crystallinity relationships [18] - [23] . The controlled synthesis of these nanomaterials often requires the employment of sensitive and specific technique. The applied method of acid-base reaction is considered between the most suitable routes. The addition of chelating or complexing additives such as GaCl-Phthalocyanine applied as surfactants is often necessary to control the synthesis conditions. The latter may be generally needed to obtain the desired morphology, including preparation variables such as the chosen Ce and phosphate the P/Ce ratio which is 1.5 in the present study. This higher ratio (than 1:1) is enough to obtain more uniform and highly-elongated (high aspect ratio) morphologies with a better crystallinity as is evidenced from Figure 2(d) and Figure 2(e).These characteristics become essential to improve the biomedical application of the used materials.

The morphology and amorphous structure of CePO₄ glass were characterized by Scanning Electron Microscopy. The micrograph of base glass is presented by Figure 9 which shows homogenous glass network. Noteworthy, formulating of cerium phosphate power of the amorphous glass with polymeric acid successfully led to the formation of CePO₄-H₂O nanofibrous bundles (Figure 10). But for mutation with GIC containing GaCl-Phthalocyanine can simply form co-aligned and elongated nanodifused species (Figure 11) which is transformed to more aligned thinner elongated nanofibers at (Figure 12). The well formed

fibers are characterized with 10 - 20 nm thick and up to ca. 1.2 m long, as shown in Figure 12. The formed nanofibers consisted of CePO₄ and CaPO₄ nanocrystals, with better-elongated shapes which are considered to be useful for using the materials in the field of tissue engineering or bio scaffolds applications.

Given the strong affinity of carboxylate or peptide moieties for cerium phosphate species [24] [25] [26] , it makes the structure to simultaneously incorporating the precursor phosphate moieties which called (grafting) throughout the self-assembled nanofibrous network can produce scaffold matix of elongated nanofiber shape (Figure 12).

As important advantage, this acid-base reaction can be performed under relatively mild conditions (pH around 4 - 4.5) avoiding the strict requirements of using a great excess amount of phosphates of very low pH values (<1.5). Such conditions, are often necessary to obtain high aspect ratio of elongated CePO₄ nanofibers functional gels [27] [28] , and they have been also successfully employed as templates in the transcription of nanofibrous inorganic materials and hybrid biomaterials [28] [29] [30] .

4. Conclusion

XRD and SEM analysis provides the crystalline nature and the morphology of the metal complexes. Most of the added GaCl molecules exhibited realble improvement in crystallinity, morphological and structural properties. The current studies are seeking to shed light on cerium phosphate based GIC containing small additives from GaCl-Phthalocyanine with unusual properties and different potential applications. For example, GIC-based nanocomposite species, containing GaCl nanocrystals as functional components, were successfully prepared and cross-linked using acid-base reaction between the organic and inorganic constituents of GIC. XRD and SEM showed that cerium phosphate glass and glass ionomer cement retained its amorphous characteristics after and before the reaction between the glass powder and the polymeric acid, while formulating cerium phosphate powder with both polymeric acid and GaCl-Phthalocyanine results in producing nanocrystals which retained crystalline morphology in the nanocomposites after cross-linking, processes. Some crystalline phases are formed in a bundle like shape at low GaCl Phthalocyanine concentration, 0.5 mol%. The bundle morphology is transformed to Co-elongated fiber or wafers like shape at higher concentration. The morphology of crystalline elongated structure recommend the material to be used in different potential applications such as the field of tissue engineering or bio scaffolds applications.

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