Mesoporous silica/ceria-silica composite and method for preparing same

Abstract

The present invention relates to a mesoporous silica/ceria-silica composite and a method for preparing a mesoporous composite and, more specifically, to a mesoporous silica/ceria-silica composite which is composed of mesoporous silica having a hexagonal or cubic structure and ceria having a hexagonal structure provided on a surface and pores of the mesoporous silica, the oxidation state of the ceria being Ce.sup.4+ and Ce.sup.3+.

Claims

1. A mesoporous silica/ceria-silica composite comprising a mesoporous silica having a hexagonal structure or a cubic structure and a ceria having the hexagonal structure and provided on a surface and in a pore of the mesoporous silica, wherein oxidation states of the ceria are Ce.sup.4+ and Ce.sup.3+, wherein, in the oxidation states of the ceria, the Ce.sup.3+ has a content of 10.2 mole % to 23.8 mole % based on a total cerium, and the Ce.sup.4+ has a content of 76.2 mole % to 89.8 mole % based on the total cerium.

2. The mesoporous silica/ceria-silica composite of claim 1, wherein a mole ratio of Ce of the ceria to Si of the silica is in a range of 0.001 to 0.5.

3. The mesoporous silica/ceria-silica composite of claim 1, wherein the mesoporous silica has a pore volume of 0.20 cm.sup.3/g to 0.40 cm.sup.3/g.

4. The mesoporous silica/ceria-silica composite of claim 1, wherein the mesoporous silica/ceria-silica composite has a BET specific surface area of 250 m.sup.2/g to 600 m.sup.2/g.

5. A method of preparing a mesoporous silica/ceria-silica composite, the method comprising: mixing and stirring a cationic surfactant, a silica precursor, and a cerium precursor; preparing the mesoporous silica/ceria-silica composite by calcining a mixed solution after performing a hydrothermal reaction for the mixed solution; and reducing the prepared mesoporous silica/ceria-silica composite, wherein the reducing is performed at a temperature of 850° C. to 900° C. for 3 hours to 6 hours, wherein a structure of mesoporous silica/ceria-silica composite is stable while the reducing is performed.

6. The method of claim 5, wherein the cationic surfactant includes hexadecyl trimethyl ammonium bromide (CTAB) or hexadecyl trimethyl ammonium chloride (CTACl).

7. The method of claim 5, wherein the silica precursor includes tetraethyl orthosilicate (TEOS) or tetramethyl orthosilicate (TMOS).

8. The method of claim 5, wherein the cerium precursor includes one selected from the group consisting of cerium hydroxide (Ce(OH).sub.4), cerium nitrate (Ce(NO.sub.3).sub.3), and cerium sulfate (Ce.sub.2(SO.sub.4).sub.3, Ce(SO.sub.4).sub.2).

9. The method of claim 5, wherein a mole ratio of the cerium precursor to the silica precursor is in a range of 0.001 to 0.5.

10. The method of claim 5, wherein the stirring is performed at a rate of 200 rpm to 600 rpm for 30 min. to 1440 min.

11. The method of claim 5, wherein the hydrothermal reaction is performed at a temperature of 80° C. to 120° C. for 20 hours to 48 hours.

12. The method of claim 5, wherein the calcining is performed under air at a temperature of 500° C. to 600° C. for 4 hours to 6 hours.

13. A mesoporous silica/ceria-silica composite comprising a mesoporous silica having a hexagonal structure or a cubic structure and a ceria having the hexagonal structure and provided on a surface and in a pore of the mesoporous silica, wherein the ceria is reduced through heat treatment and the ceria is present in oxidation states of Ce.sup.3+, and wherein the ceria has diffraction patterns which are matched with that of Ce.sub.4.667Si.sub.3O.sub.13 in a structure similar to an apatite structure having a hexagonal unit lattice.

14. The mesoporous silica/ceria-silica composite of claim 13, wherein the Ce.sup.3+ has a content of 10.2 to 100 mole % based on a total cerium.

Description

DESCRIPTION OF DRAWINGS

(1) FIG. 1 is a flowchart showing a method of preparing a mesoporous silica/ceria-silica composite according to the present invention.

(2) FIG. 2 illustrates FE-SEM photographs of the mesoporous silica/ceria-silica composite according to the present invention.

(3) FIG. 3 illustrates high-magnification TEM photographs to analyze the nano-structure particles of the mesoporous silica/ceria-silica composite according to the present invention and the size thereof.

(4) FIG. 4 illustrates TEM photographs showing the mesoporous silica/ceria-silica composite powders according to the present invention.

(5) FIG. 5 illustrates graphs showing the analysis results by a TEM EDX in order to examine the chemical composites of mutually different particles.

(6) FIG. 6 is a graph showing the analysis result of the nano-structure of the mesoporous silica/ceria-silica composite according to the present invention by small angle X-ray scattering (SAXS).

(7) FIG. 7 illustrates graphs showing a nitrogen adsorption-desorption isothermal curve of the hexagonal mesoporous silica/ceria-silica composite according to the present invention, and the pore size distribution of the composite, respectively.

(8) FIG. 8 illustrates graphs showing X-ray diffraction patterns of the hexagonal mesoporous silica/ceria-silica composite according to the present invention.

(9) FIG. 9 is a graph showing scattering and reflection ultraviolet-visible absorbance spectra of the hexagonal mesoporous silica/ceria-silica composite according to the present invention.

(10) FIG. 10 illustrates graphs showing X-ray photoelectron (XPS) measurement results of the hexagonal mesoporous silica/ceria-silica composite according to the present invention.

(11) FIG. 11 is a graph showing an SAXS spectrum of a reduced silica/ceria-silica composite according to the present invention.

(12) FIG. 12 illustrates graphs showing nitrogen adsorption-desorption isothermal curves of the reduced hexagonal and cubic silica/ceria-silica composites according to the present invention, and the pore size distribution of the composite, respectively.

(13) FIG. 13 illustrates graphs showing wide angle X-ray diffraction patterns of the reduced hexagonal and cubic mesoporous silica/ceria-silica composites according to the present invention.

BEST MODE

(14) Hereinafter, an exemplary embodiment of the present invention will be described in detail with reference to accompanying drawings.

(15) The advantages, the features, and schemes of achieving the advantages and features of the disclosure will be apparently comprehended by those skilled in the art based on the embodiments, which are detailed later in detail, together with accompanying drawings.

(16) However, the present invention is not limited to embodiments disclosed hereinafter, but realized in various forms. The present embodiments are provided to make the disclosure of the present invention perfect and to let those skilled in the art completely comprehend the scope of the present invention, and defined within the scope of accompanying claims of the present invention.

(17) Further, in the following description, the details of the generally-known technology that makes the subject matter of the present invention unclear will be omitted in the following description.

(18) The present invention provides a mesoporous silica/ceria-silica composite including a mesoporous silica having a hexagonal structure or a cubic structure and a ceria having the hexagonal structure and provided on a surface and in a pore of the mesoporous silica, wherein oxidation states of the ceria are Ce.sup.4+ and Ce.sup.3+.

(19) According to the mesoporous silica/ceria-silica composite of the present invention, a plurality of pores exist in a hexagonal or cubic silica template, and ceria is bonded to the surface and the inside of the pores of the template. The ceria is formed in the hexagonal and cubic structures, and the oxidation states of the ceria become Ce.sup.4+ and Ce.sup.3−. Most parts of Ce.sup.4− may be changed to Ce.sup.3+ through the reduction process thereafter.

(20) The mesoporous silica/ceria-silica composite according to the present invention has improved strength and biocompatibility due to a silica template having a plurality of mesoporous. In addition, ceria is bonded to the surface and the inside of the pores of the silica template to prevent the ceria from being agglomerated to be enlarged and aged. In addition, the composite has Ce.sup.3+ representing a great radical scavenging effect.

(21) In the mesoporous silica/ceria-silica composite, a mole ratio of Ce of the ceria to Si of the silica is in the range of 0.001 to 0.5. In the oxidation states of the ceria, the Ce.sup.3+ has a content of 10.2 mole % to 23.8 mole % based on a total cerium, and the Ce.sup.4+ has a content of 76.2 mole % to 89.8 mole % based on the total cerium. Further, in the mesoporous silica/ceria-silica composite according to the present invention, the mesoporous silica has a pore volume of 0.20 cm.sup.3/g to 0.40 cm.sup.3/g, and the BET specific surface area of 250 m.sup.2/g to 600 m.sup.2/g.

(22) Further, the present invention provides a method of preparing a mesoporous silica/ceria-silica composite, including mixing and stirring a cationic surfactant, a silica precursor, and a cerium precursor,

(23) preparing the mesoporous silica/ceria-silica composite by calcining a mixed solution after performing a hydrothermal reaction for the mixed solution, and

(24) reducing the prepared mesoporous silica/ceria-silica composite.

(25) FIG. 1 is a flowchart showing a method of preparing a mesoporous silica/ceria-silica composite according to the present invention. Hereinafter, the method of preparing the mesoporous silica/ceria-silica composite will be described in detail with reference to FIG. 1.

(26) The method of preparing the mesoporous silica/ceria-silica composite according to the present invention includes a step of mixing and stirring a cationic surfactant, a cerium precursor and a silica precursor (S100).

(27) In this case, the cationic surfactant, the cerium precursor and the silica precursor may be dissolved in de-ionized water, ammonium hydroxide (NH.sub.4OH), and ethanol. In detail, preferably, after dissolving the cationic surfactant into the de-ionized water, the ammonium hydroxide, and the ethanol and stirring the result, the silica precursor is added and stirred, and a ceria precursor is added and stirred. This is because the cationic surfactant, the silica precursor, and the ceria precursor may be sequentially dissolved as described so that the cationic surfactant, the silica precursor, and the ceria precursor may be sufficiently dissolved.

(28) The cationic surfactant is added to a mesoporous silica template in order to form a pore. The cationic surfactant, which severs as a cationic surfactant (CH.sub.3(CH.sub.2).sub.nN.sup.+(CH.sub.3).sub.3) including hydrophobic alkyl chain and hydrophilic amine, may include hexadecyl trimethyl ammonium bromide (CTAB) or hexadecyl trimethyl ammonium chloride (CTACl). The cerium precursor may include one selected from the group consisting of cerium hydroxide (Ce(OH).sub.4), cerium nitrate (Ce(NO.sub.3).sub.3), and cerium sulfate (Ce.sub.2(SO.sub.4).sub.3, Ce(SO.sub.4).sub.2), and the silica precursor may include tetraethyl orthosilicate (TEOS) or tetramethyl orthosilicate (TMOS).

(29) In addition, according to the method of preparing the mesoporous silica/ceria-silica composite of the present invention, the mole ratio of the cerium, precursor to the silica precursor is in the range of 0.001-0.5. If the mole ratio is less than 0.001, a free radical scavenging effect and catalytic activity may be significantly degraded. If the mole ratio exceeds 0.5, cerium particles may be agglomerated, or the strength of a silica template may be degraded.

(30) The stirring is preferably performed at a rate of 200-600 rpm for 30-1440 min. If the stirring rate is less than 200 rpm, a nano-structure may not be uniformly formed. Accordingly, it is preferred that the stirring rate is 600 rpm or less when considering the shape of a reactor and reaction stability. The reason for time limitation has been described above.

(31) The method of preparing the mesoporous silica/ceria-silica composite according to the present invention includes a step of preparing the mesoporous silica/ceria-silica composite by calcining the mixed solution after making a hydrothermal reaction for the mixed solution (S200).

(32) In this case, preferably, the hydrothermal reaction is performed at the temperature of 80-120° C. for 20-48 hours. If the hydrothermal reaction is made at the temperature of less than 80° C., the bonding strength between silica and ceria may be weakened, and the bonding strength among silica particles may be weakened. If the hydrothermal reaction is made at the temperature of 120° C. for more than 48 hours, not only the bonding between the silica and the ceria, but also the bonding between silica particles may be decomposed.

(33) In addition, preferably, the calcining is performed under air at the temperature of 500-600° C. for 4-6 hours. If the calcination is performed at the temperature of less than 500° C., the cationic surfactant is not removed, so that the mesoporous composite structure may not be prepared. If the calcination is performed at more than 600° C., the surfactant may be sufficiently removed. Accordingly, the calcimining temperature is 600° C. or more in terms of energy efficiencies.

(34) The method of preparing the mesoporous silica/ceria-silica composite according to the present invention includes a step of reducing the prepared mesoporous silica/ceria-silica composite (S300).

(35) The reducing is preferably performed at the temperature of 850-900° C. for 3-6 hours. If the reducing is performed at the temperature of less than 850° C., an oxidation state of Ce.sup.4+ may not be reduced into Ce.sup.3+. If the reducing is performed at the temperature of more than 900° C., the bonding between silica and ceria may be decomposed, so that the nano-structure may not be maintained. The reason for the reduction time limitation is the same as the reason for the temperature limitation.

(36) Further, in reduction, mixture gas including 5-10 volume % of nitrogen gas based on hydrogen gas may be used. If the nitrogen gas is contained in less than 5 volume %, the composite may not be smoothly reduced, so that the oxidation state of cerium may not be changed. If the nitrogen gas is contained in more than 10 volume %, explosion hazard may be increased due to an excessive amount of nitrogen gas.

MODE FOR INVENTION

Embodiment 1: Preparation 1 of Hexagonal Mesoporous Silica/Ceria-Silica Composite

(37) In Embodiment 1, 1.5 g of hexadecyl trimethyl ammonium bromide (4.1 mmol) was stirred in 30 ml of deionized water, 35 ml of NH.sub.4OH, and 45.6 ml of ethanol and completely dissolved. After stirring the mixing solution in a 125 ml glass container at a normal temperature for 30 min. using a magnetic bar, and 3 ml TEOS was added into the mixing solution. After stirring the mixing solution at a constant rate of 500 rpm for 30 min., 1.4 g of cerium hydroxide was added, and the mixture of the mixing solution and the cerium hydroxide was stirred at the normal temperature for 20 hours, and the mixture was subject to the hydrothermal reaction the temperature 100° C. for 24 hours in a convection oven. The mixture was filtered using a sufficient amount of deionized water to remove a surfactant, a solvent, and an unreacted material, and calcined at the temperature of 550° C. for 5 hours under the atmospheric atmosphere. In the calcination, heating was performed at the rate of 3° C./min from the normal temperature to 550° C.

(38) The heating was performed from the normal temperature to 850° C. at an average heating rate of 4.5° C./min after the calcination process. Then, the heating was constantly performed at 850° C. for five hours to reduce the mesoporous silica/ceria-silica composite. In this case, the total flow rate was 205 ml/min under the flow of 7 volume % of hydrogen diluted with nitrogen.

Embodiment 2: Preparation 2 of Hexagonal Mesoporous Silica/Ceria-Silica Composite

(39) In Embodiment 2, the hexagonal mesoporous silica/ceria-silica composite was prepared in the same manner as that of Embodiment 1 except that the cerium hydroxide was added so that the mole ratio of cerium hydroxide to TEOS was 0.4.

Embodiment 3: Preparation 3 of Hexagonal Mesoporous Silica/Ceria-Silica Composite

(40) In Embodiment 3, the hexagonal mesoporous silica/ceria-silica composite was prepared in the same manner as that of Embodiment 1 except that cerium hydroxide was added so that the mole ratio of cerium hydroxide to TEOS was 0.3.

Embodiment 4: Preparation 4 of Hexagonal Mesoporous Silica/Ceria-Silica Composite

(41) In Embodiment 4, the hexagonal mesoporous silica/ceria-silica composite was prepared in the same manner as that of Embodiment 1 except that cerium hydroxide was added so that the mole ratio of cerium hydroxide to TEOS was 0.2.

Embodiment 5: Preparation 1 of Cubic Mesoporous Silica/Ceria-Silica Composite

(42) In Embodiment 5, 1.2 g of hexadecyl trimethyl ammonium bromide (3.3 mmol) was stirred in 50 ml of deionized water, 6 ml of NH.sub.4OH, and 25 ml of ethanol and completely dissolved. After stirring the mixing solution in a 125 ml glass container at a normal temperature for 30 min. using a magnetic bar, 3 ml TEOS was added to the mixing solution. After stirring the mixing solution at a constant rate of 500 rpm for 30 min., 1.4 g of cerium hydroxide was added, the mixture of the mixing solution and the cerium hydroxide was stirred at the normal temperature for 20 hours, and the mixture was subject to the hydrothermal reaction at the temperature 100° C. for 24 hours in a convection oven. The mixture was filtered using a sufficient amount of deionized water to remove a surfactant, a solvent, and an unreacted material, and calcined at the temperature of 550° C. for 5 hours under the atmospheric atmosphere. In the calcination, heating was performed at the rate of 3° C./min from the normal temperature to 550° C. The heating was performed from the normal temperature to 850° C. at an average heating rate of 4.5° C./min after the calcination process. Then, the heating was constantly performed at 850° C. for five hours to reduce the mesoporous silica/ceria-silica composite. In this case, the total flow rate was 205 ml/min under the flow of 7 volume % of hydrogen diluted with nitrogen.

Embodiment 6: Preparation 2 of Cubic Mesoporous Silica/Ceria-Silica Composite

(43) In Embodiment 6, the cubic mesoporous silica/ceria-silica composite was prepared in the same manner as that of Embodiment 5 except that cerium hydroxide was added so that the mole ratio of cerium hydroxide to TEOS was 0.4.

Embodiment 7: Preparation 3 of Cubic Mesoporous Silica/Ceria-Silica Composite

(44) In Embodiment 7, the cubic mesoporous silica/ceria-silica composite was prepared in the same manner as that of Embodiment 5 except that cerium hydroxide was added so that the mole ratio of cerium hydroxide to TEOS was 0.3.

Embodiment 8: Preparation 4 of Cubic Mesoporous Silica/Ceria-Silica Composite

(45) In Embodiment 8, the cubic mesoporous silica/ceria-silica composite was prepared in the same manner as that of Embodiment 5 except that cerium hydroxide was added so that the mole ratio of cerium hydroxide to TEOS was 0.2.

Experimental Example 1: Analysis of Surface and Shape of Mesoporous Silica/Ceria-Silica Composite

(46) The surface and the shape of the mesoporous silica/ceria-silica composite according to the present invention were analyzed by an FE-SEM and a TEM, and the analysis results are shown in FIGS. 2, 3, 4, and 5.

(47) As shown in FIG. 2(a), the mesoporous silica/ceria-silica composite according to the present invention (before the reduction process in Embodiment 4) is in the shape of a sphere having a diameter of about 500 nm, and the composites other than that of Embodiment 4 is in the shape of a sphere having a nano-size diameter. In addition, a large amount of nano-size particles in size smaller than those of the spherical particles was mixed with the spherical particles. FIG. 2(b) is a TEM photograph of Embodiment 1. The nano-size particles in size smaller than those of the spherical particles was appeared as being in a dark dot shape, and as being scattered among spherical particles linked to each other.

(48) FIGS. 3(a) to 3(c) are high-magnification TEM photographs to analyze the nano-structure particles and the size thereof. As shown in FIGS. 3(a) to 3(c), the spherical particles of the composites, which are prepared before the reduction process performed according to Embodiments 1 and 4, contain hexagonal and cubic porous structures having high regularity, and a large amount of aspherical particles are scattered therebetween.

(49) FIGS. 4(a) and 4(b) are TEM photographs showing the mesoporous silica/ceria-silica composite powders according to the present invention. As shown in FIG. 4(b), a large amount of aspherical particles are not shown in a uniform porous structure.

(50) FIGS. 5(a) and 5(b) are graphs showing the analysis results by a TEM EDX in order to examine the chemical composites of mutually different particles. FIG. 5(a) shows the spherical particles, and FIG. 5(b) shows the aspherical particles. As shown in FIG. 5(a), silica particles contain 50.0% of Si, 49.5% of O, and 0.5% of Ce in weight %, and the aspherical particles contain 18.9% of silicon, 25.5% of oxygen, and 55.6% of cerium. Accordingly, the mesoporous silica/ceria-silica composite according to the present invention contains mesoporous silica particles having high regularity and a small amount of cerium, and aspherical nano-particles having a large amount of cerium.

Experimental Example 2: Analysis of Surface and Shape of Mesoporous Silica/Ceria-Silica Composite

(51) The surface and the shape of the mesoporous silica/ceria-silica composite according to the present invention are analyzed through a small angle X-ray scattering (SAXS), a nitrogen adsorption-desorption isothermal curve, a pore size distribution curve, X-ray diffraction, scattering and reflection of ultraviolet-visible absorbance spectrum measurement, and X-ray photoelectron (XPS), and the analysis results are shown in FIGS. 6, 7, 8, 9, and 10.

(52) FIG. 6 is a graph showing the analysis result of the surface and the shape of the nano-structure of the mesoporous silica/ceria-silica composite according to the present invention by the small angle X-ray scattering (SAXS). As shown in FIG. 6, in the mesoporous silica/ceria-silica composite, all Ce-doped silica have 2-D hexagonal (p6mm) mesostructures having three peaks indexed with (100), (110), and (200) according to p6mm symmetric groups, and have high regularity. The d-spacing (d.sub.100) obtained from the Bragg peak having the greatest strength is slightly reduced to a value in the range of 3.905 nm to 3.820 nm. It can be understood that the crystal lattice parameter is in the range of 4.41-4.51 nm which is calculated based on 2d.sub.100/√3 from each d-spacing. In FIG. 6, a curve (a) represents a silica particle contained in the mesoporous silica/ceria-silica composite prepared when the mole ratio of Ce(OH.sub.4)/TEOS is 0.1, and recognized as being in a hexagonal lattice structure based on the peak intensity. A curve (b) represents a composite prepared in Embodiment 4 before the reduction process is performed, and curves (c), (d), and (e) represent composites prepared according to Embodiments 3, 2, and 1, respectively.

(53) FIGS. 7(a) and 7(b) are graphs showing a nitrogen adsorption-desorption isothermal curve of the hexagonal mesoporous silica/ceria-silica composite according to the present invention, and the pore size distribution of the composite, respectively. In detail, FIG. 7(a) shows the nitrogen adsorption-desorption isothermal cure e, and FIG. 7(b) is a graph showing the pore size distribution. In FIG. 7, reference codes A, B, C, and D represent curves of hexagonal mesoporous silica/ceria-silica composites before the reduction process is performed, which are prepared in Embodiments 4, 3, 2, and 1. All isothermal curves are IV-type curves related to a capillary action of a mesopore under relative pressures (P/P.sub.0) ranging 0.24 to 0.32, which represents capillary condensation of nitrogen in a channel forming the hexagonal mesostructure. The capillary condensation is maintained even when cerium is contained in high content, which represents that high regularity is preserved in porous channels of Ce-doped silica particles existing in the hexagonal mesoporous silica/ceria-silica composite. A BET specific surface area of the hexagonal mesoporous silica/ceria-silica composite was in the range of 370 to 560 m.sup.2/g, and the total porous volume (V.sub.t) was in the range of 0.42 to 0.52 cm.sup.3/g. Regarding the pore size calculated through the KJS manner, as shown in FIG. 7(b), the pore size distribution of all mesoporous silica ceria-silica composites having the hexagonal structures was significantly narrow. In the graph showing the pore size distribution, the pore diameter obtained at the peak value was in the range of 3.3 to 3.4, and the wall thickness (a−D.sub.KJS) value was in the range of about 1.1-1.2 nm.

(54) FIGS. 8(a) to 8(d) are graphs showing X-ray diffraction patterns of the hexagonal mesoporous silica/ceria-silica composites according to the present invention, in detail, graphs showing the X-ray diffraction patterns of the mesoporous silica/ceria-silica composites before the reduction process is performed, which are prepared according to Embodiments 4, 3, 2, and 1. As shown in FIGS. 8(a) to 8(d), the composite prepared according to Embodiment 4 shows the complex shape of amorphous silica) (2θ=22°) and ceria. As the content of ceria is increased, a specific peak representing silica is reduced (expressed in an arrow of FIGS. 8(a) to 8(d)), and five/sixth diffraction peaks represent that the ceria has a typical face centered cubic lattice. The lattice constant of the cubic shape ceria is estimated to a=b=c=0.5434-0.5526 nm based on a (200) peak, and slightly greater than 0.5411 nm which is a lattice constant of CeO.sub.2 having a bulk shape.

(55) The increased lattice constant for the ceria-silica particle is related to the formation of the defect of silica contained in a ceria lattice. The crystal size was measured to a value in the range of 1.5-1.8 nm by applying a Scherrer equation (L=Kλ/β cos θ) based on the full width at half maximum (FWHM) of a (111) diffraction peak. The ratio of A.sub.(111)/A.sub.(200) provides information on the possibility of an appropriate orientation of a ceria crystal surface. Since a (200) plane represents a tendency of an oxygen air gap higher than that of a (111) plane as generally known in the art, the information on the ratio of Ce.sup.4+/Ce.sup.3+ may be provided. The ratio is a value in the range of 3.2-3.6, and slightly increased according to the content of cerium.

(56) FIG. 9 is a graph showing scattering and reflection ultraviolet-visible absorbance spectra of the hexagonal mesoporous silica/ceria-silica composite according to the present invention, and (a), (b), (c), and (d) of FIG. 9 are curves representing the composites prepared before the reduction process is performed according to Embodiments 4, 3, 2, and 1. As shown in FIG. 9, ceria is a semiconductor having a wide bandgap and has an ultraviolet suppression characteristic. In addition, the composite resulting from the silica is analyzed by the absorption of the ultraviolet light-visible light. In the mesoporous silica/ceria-silica composite according to the present invention, the absorbance is appeared in the wide range of 250-440 nm (2.82 eV), and the maximum absorbance peak is appeared at about 320 nm (3.87 eV).

(57) FIGS. 10(a) to 10(d) are graphs showing X-ray photoelectron (XPS) measurement results of the hexagonal mesoporous silica/ceria-silica composite according to the present invention. FIGS. 10(a) to 10(d) show the composites prepared before the reduction process is performed according to Embodiments 4, 3, 2, and 1, respectively. XPS measurement was performed to examine the oxidation state of cerium on the surface of the mesoporous silica/ceria-silica composite. In each spectrum of 3d of Ce, eight separate peaks are shown through a Gaussian fitting manner. In FIG. 10, a series of v and u peaks are shown from 3d.sub.5/2 and 3d.sub.3/2 orbitals of Ce, respectively, in which v.sub.1 and u.sub.1 peaks correspond to Ce.sup.3+, and remaining peaks correspond to Ce.sup.4+.

(58) Following table 1 shows the mole ratios of cerium hydroxide to tetraethyl orthosilicate, Ce contents, Ce molar masses, % of Ce/Si, BET specific surface areas, total pore volumes, and pore diameters in the hexagonal and cubic mesoporous silica/ceria-silica composites prepared before the reduction process is performed according to embodiments 1 to 8 of the present invention.

(59) TABLE-US-00001 TABLE 1 BET specific Mole Ce molar surface Pore Pore ratio Ce content mass Ce/Si area volume diameter (Ce/Si) (wt %) (mmol/g) (%) (m.sup.2/g) (cm.sup.3/g) (nm) Embodiment 1 0.5 43.52 3.106 50.6 370 0.42 3.4 Embodiment 2 0.4 41.41 2.955 46.4 390 0.44 3.3 Embodiment 3 0.3 30.53 2.179 28.9 447 0.46 3.3 Embodiment 4 0.2 24.84 1.773 21.7 560 0.52 3.3 Embodiment 5 0.5 — — — 356 0.42 3.4 Embodiment 6 0.4 — — — 455 0.50 3.4 Embodiment 7 0.3 — — — 543 0.56 3.5 Embodiment 8 0.2 — — — 637 0.64 3.4

(60) As recognized from the results, the oxidation state of the ceria is mainly Ce.sup.4+(CeO.sub.2), which represents that the total cerium content reaches 80% to 90% in the composite. Since Ce.sup.3+(Ce.sub.2O.sub.3) has high reactivity and high performance as a radical scavenger, the reduction process is performed to increase the content of C.sup.3+ in the composite.

(61) Following table 2 shows the binding energies of the hexagonal mesoporous silica/ceria-silica composites prepared before the reduction process is performed according to Embodiments 1 to 4 of the present invention and integrated region ratios of peaks of the silica/ceria-silica composites.

(62) TABLE-US-00002 TABLE 2 XPS Ce 3d.sub.5/2 Ce 3d.sub.3/2 ν.sub.0 ν.sub.1 ν.sub.2 ν.sub.3 μ.sub.0 μ.sub.1 μ.sub.2 μ.sub.3 Embodiment Peak allocation Ce.sup.4+ Ce.sup.3+ Ce.sup.4+ Ce.sup.4+ Ce.sup.4+ Ce.sup.3+ Ce.sup.4+ Ce.sup.4+ Embodiment 4 Binding 884.3 886.5 890.9 900.4 902.8 904.3 909.1 919.0 energy (eV) Peak 10.7 11.0 14.5 15.9 7.1 5.9 18.9 16.0 region (%) Embodiment 3 Binding 883.6 886.2 889.8 899.3 901.9 903.8 909.3 918.8 energy (eV) Peak 9.0 8.8 18.3 10.0 8.4 15.0 13.4 17.1 region (%) Embodiment 2 Binding 883.9 886.1 890.2 899.6 902.2 904.5 909.7 918.6 energy (eV) Peak 10.1 10.9 15.5 8.9 11.3 11.7 14.5 17.1 region (%) Embodiment 1 Binding 884.5 887.0 889.0 900.2 902.9 905.6 909.9 919.3 energy (eV) Peak 7.2 2.3 29.3 10.5 12.3 7.9 14.4 16.1 region (%)

(63) As shown in table 2, the ratios of Ce.sup.3 to the total contents of the cerium are represented as 10.2 mol % in Embodiment 1, 22.6 mol % in Embodiment 2, 23.8 mol % in Embodiment 3, and 16.9 mol % in Embodiment 4, respectively.

Experimental Example 3: Analysis of Surface and Shape of Silica/Ceria-Silica Composite Before Reduction Process is Performed

(64) In order to examine the shape and the surface of the silica/ceria-silica composite after the reduction process is performed according to the present invention, the shape and the surface of the silica/ceria-silica composite are analyzed by the SAXS spectrum, a nitrogen adsorption-desorption isothermal curve, a pore size distribution of the composite, and a wide angle X-ray diffraction pattern, and the analysis results are shown in FIGS. 11 to 13.

(65) FIG. 11 is a graph showing an SAXS spectrum of the reduced silica/ceria-silica composite according to the present invention. In FIG. 11, reference code (a) represents a silica/ceria-silica composite prepared according to Embodiment 1, and reference code (b) represents a silica/ceria-silica composite prepared according to Embodiment 2. As shown in FIG. 11, 2-D hexagonal and 3-D cubic mesostructure silica particles having high regularity in the reduced composite maintain the SAXS spectrum of the composite before the reduction process is performed. In FIG. 11, reference number (a) may represent (100), (110) and (200) of a p6mm symmetry group. In addition, d-spacing (d.sub.100) and a unit lattice parameter are obtained as 3.588 nm and 4.14 nm, respectively, which are smaller than 3.820 nm and 4.41 nm of the composite before the reduction process is performed. In FIG. 11, reference number (b) may represent (211), (220), (321), (400), (420), (332), (422) and (431) reflections, which correspond to a double continuity cubic (Ia3d) mesostructure. In addition, d-spacing (d.sub.211) and a unit lattice parameter are obtained as 3.331 nm and 8.16 nm, respectively, which are smaller than 3.672 nm and 9.00 nm of the composite before the reduction process is performed. Due to the reduction process, the composites of Embodiments and 5 are shrunken in structure by 6.11 and 9.3, respectively.

(66) FIGS. 12(a) and 12(b) are graphs showing nitrogen adsorption-desorption isothermal curves of the reduced hexagonal and cubic silica/ceria-silica composites according to the present invention, and the pore size distribution of the composite, respectively. In detail, FIG. 12(a) is a graph showing the nitrogen adsorption-desorption isothermal curve, and FIG. 12(b) is a graph showing the pore size distribution. In FIGS. 12(a) and 12(b), reference numbers A and B are curves showing the reduced mesoporous silica/ceria-silica composites prepared according to Embodiments 1 and 5, respectively. All isothermal curves are IV-type curves related to the capillary condensation of mesopores. The range of relative pressure (P/P.sub.0) for the capillary condensation is reduced by 0.02 as compared with that of the composite before the reduction process is performed. Although a hysteresis phenomenon is not observed in the isothermal curve of the hexagonal composite, the slight hysteresis phenomenon is appeared in the isothermal curve of the cubic composite under the relative pressure of 0.4 to 1.0. In addition, as recognized from FIG. 12(b), all reduced composites show narrow pore size distribution. In the reduced hexagonal composite, the BET specific surface area is 264 m.sup.2/g, the total pore volume is 0.29 cm.sup.3/g, and the pore diameter is 3.0 nm. In the reduced cubic composite, the BET specific surface area, the total pore volume, and the pore diameter are 287 m.sup.2/g, 0.28 cm.sup.3/g, and 2.9 nm, respectively. As shown in the nitrogen adsorption analysis, the porosity and the pore size are reduced due to the reduction process at the high temperature except for the wall thickness of 1.1-1.2 nm.

(67) Following table 3 shows the mole ratios of cerium hydroxide to tetraethyl orthosilicate, Ce contents, Ce molar masses, % of Ce/Si, BET specific surface areas, total pore volumes, and pore diameters in the reduced hexagonal and cubic mesoporous silica/ceria-silica composites.

(68) TABLE-US-00003 TABLE 3 BET specific Mole Ce molar surface Pore Pore ratio Ce content mass Ce/Si area volume diameter Embodiments (Ce/Si) (wt %) (mmol/g) (%) (m.sup.2/g) (cm.sup.3/g) (nm) Embodiment 1 0.5 45.29 3.232 54.4 264 0.29 3.0 Embodiment 5 0.5 45.82 3.270 55.6 287 0.28 2.9

(69) FIGS. 13(a) and 13(b) are graphs showing wide angle X-ray diffraction patterns of the reduced hexagonal and cubic mesoporous silica/ceria-silica composites according to the present invention, and, in detail, showing composites according to Embodiments 1 and 5 subject to the reduction process. As shown in FIGS. 13(a) and 13(b), two diffraction patterns are substantially identical to each other. However, the two diffraction patterns are not identical to a pattern of a typical cubic cerium dioxide, which represents that a new crystal phase is not created. The diffraction patterns are matched with that of Ce.sub.4.667Si.sub.3O.sub.13 in a structure similar to an apatite structure having a hexagonal unit lattice, which represents that an amount of CeO.sub.2 in the reduced mesoporous silica/ceria-silica composite is negligible, and almost parts of Ce in the composite is oxidized to Ce.sup.3−. The amounts of Ce in the reduced hexagonal and cubic mesoporous silica/ceria-silica composites are 3.232 mmol/g and 3.270 mmol/g, respectively, which are substantially identical to those in the composites before the reduction process is performed.

(70) Although detailed embodiments of the mesoporous silica/ceria-silica composite according to the present invention and the method of preparing the same have been described, those skilled in the art will appreciate that various modifications, additions and substitutions are possible, without departing from the scope and spirit of the invention as disclosed in the accompanying claims.

(71) Therefore, those skilled in the art should define the scope of the present invention by accompanying claims and equivalents thereof without the limitation to the embodiments described above.

(72) In other words, the above-described embodiments are provided for illustrative purposes, and the scope of the present invention is defined by the claims instead of the detailed description. In addition, those skilled in the art should understand that all variations and modifications derived from the meaning and the scope of the claims, and the equivalents of the claims fall within the scope of the present invention.