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Journal of Thermal Analysis and Calorimetry

, Volume 108, Issue 3, pp 1085–1092 | Cite as

Complex investigations of structural and thermal properties of silica-titania adsorbents

  • J. Skubiszewska-Zięba
  • B. Charmas
  • R. Leboda
  • V. A. Tertykh
  • V. V. Yanishpolskii
Open Access
Article

Abstract

Mesoporous titanium-containing silicas with different Titania contents were investigated. The structural parameters of the materials were characterized by low-temperature adsorption/desorption of nitrogen and X-ray diffraction analysis. The thermodesorption of water using the quasi-isothermal thermogravimetry as well as the differential scanning calorimetry were used to characterize thermal and surface properties of these materials. The adsorbed water layers and the concentration of weakly and strongly bound water as well as the surface free energy on the adsorbent/water interfaces were calculated. It was stated that the increase of Titania content causes a gradual decrease of specific surface area and formation of biporous structure inside the tested materials. The water thermodesorption from the surface proceeds in two or three stages, which is connected mainly with pore distribution and TiO2 content. One can observe the increase of the total surface free energy (ΔG Σ) with the increasing TiO2 content, but the largest ΔG Σ value at the adsorbent/strongly bound water interface is exhibited by the adsorbent of intermediate content (30%) of TiO2. Freezing temperature of water contained in the pores of the studied materials is connected largely with their porous structure. Due to the well developed porous structure, the water freezing process is a multi-stage one.

Keywords

Mesoporous titanosilicas Porous structure Q-TG DSC Water layers Surface free energy 

Introduction

The rapid development of research on the preparation of ordered mesoporous materials began in the early 1990s [1], when the Mobil Corporation has reported new method of materials designated as M41S synthesis. Such materials are characterized by high specific surface area and well developed porous structure with ordered framework and narrow pore size distribution. The structure of mesoporous materials allows using them as host materials, catalyst for reactions of large molecules [2] and chromatographic materials. They can be modified by incorporation of different metals in the form of elements, ions or oxides which can create or enlarge the activity inside the pores. The incorporation of ions of transition metals into the framework of such materials (especially titanium) gives additional special catalytic properties [3, 4, 5, 6, 7, 8, 9, 10, 11].

Silica-titania materials (STM) possessing different compositions and physico-chemical characteristics are widely used as fillers, pigments, catalysts, catalyst supports, etc. [3, 12, 13, 14] They also demonstrate photocatalytic and oxidative activity [15, 16]. Mesoporous titania-silica materials can be prepared by three methods [17]: (1) one-pot synthesis (the metal precursor is added directly to a silicon source and metal becomes part of the wall structure) [6, 18], (2) template ion-exchange (the ion template in as-prepared material is exchanged with other metal ions from the solution) [19] as well as (3) post-synthesis modification (numerous Si–OH groups react with the organometallic complex or another source of metal) [20, 21]. It is known that the synthesis techniques used for preparation (sol–gel, high-temperature hydrolysis, chemical vapor deposition CVD) strongly affect the structure and properties of STM. Titania-silicas can possess (a) complex structure both in the bulk and at the surface layer, as it is in the fumed ST or (b) separated phases of TiO2 and SiO2 with a clear-cut phase boundary when one of these oxides is formed on another, which is a substrate (e.g., using the CVD technique). Naturally, the activity of solids in various adsorption and catalytic processes is affected by many factors, i.e., porous structure, chemical nature of surface functional groups and their natural distribution and concentration [22, 23, 24]. The surface and sorption properties of such materials depend strongly on the degree of hydration, i.e., the amount of bound and physically adsorbed water. Many studies suggest that the water contained in pores of such materials changes its physicochemical properties because of interactions with the solid surface [25, 26, 27]. Thus, studying the phase transitions of water bound to the surface of such materials we obtain additional information about their porous structure and the nature of the surface.

The aim of this article was to investigate the effect of chemical compositions (SiO2/TiO2) and the porosity of a series of silica-titania adsorbents on the structure of adsorbed water layers.

Experimental

Titania-silica samples (containing from 1 to 70 mol % of TiO2) were prepared by using the templating approach to synthesize mesoporous silica-based molecular sieves partly substituted with titanium-large-pore analogs of titanium silicalite. The reaction of TEOS and Ti(i-OC3H7)4, as SiO2 and TiO2 precursors, with octadecyltrimethylammonium chloride (ODTMA) as a template was performed. The ratio of ODTMA: (SiO2 + TiO2) was equal to 0.27. The details of the preparation procedure were described in [14].

The characterization of synthesized samples was performed by nitrogen adsorption/desorption isotherms measured at 77 K using the ASAP 2405 Micromeritics apparatus. The specific surface area (S BET, Table 1) was calculated using the BET equation [28] at p/p o between 0.06 and 0.2 (where p and p o denote the equilibrium and saturation pressure of nitrogen, respectively). The pore volume V p was determined at p/p o ≈ 1. The average pore radius (R ave) was calculated using a cylindrical pore model R p = 2V p/S BET. Pore volume distributions in the function of their radius were calculated according to the Barrett-Joyner-Halenda (BJH) method [29]. On the basis of this dependence the dominant pore radius (R dom) was determined. The X-ray diffraction analysis (XRD) was performed using the automated diffractometer DRON-3M, Cu–Kα radiation.
Table 1

Structural parameters of silica-titania adsorbents

Sample

TiO2 content/mol %

S BET/m2/g

V p/cm3/g

R ave/nm

R dom/nm

ST1

1

924

0.47

1.0

1.04

ST15

15

805

0.45

1.1

1.04; 2.13

ST30

30

702

0.52

1.5

1.14; 2.02

ST50

50

529

0.59

2.3

1.89

ST70

70

353

0.45

2.6

2.43

Thermodesorption of water from the surface of investigated samples was carried out under quasi-isothermal conditions (Q-TG) in the range of 293–573 K using a Derivatograph C (Paulik, Paulik and Erdey, MOM, Hungary). Before the Q-TG measurements the water vapor was adsorbed on the surface of studied samples at room temperature (293 K) for 72 h. Then the weighed portions (about 50 mg) of adsorbents were placed in the special spherical platinum crucible of the derivatograph. The experimental data of quasi-thermogravimetric measurements correspond to water mass loss in accordance with temperature changes. When measurements are performed over a temperature range without any chemical reactions leading to changes in the sample mass then the Δm = f(T) dependence reflects changes in concentration of the substance present on the adsorbent surface under equilibrium. These data were used as initial ones for calculation of energetic characteristics of the tested samples. This method was described precisely in [30, 31]. On the basis of the obtained data, total concentrations of water adsorbed on the surface of studied adsorbents (mg/g) were calculated. The number of statistical monolayers "n" of water was determined from the formula:
$$ n = \frac{{TG_{\max } N_{\omega } }}{{S_{\text{BET}} M}} $$
(1)
where ω—the surface occupied by one adsorbed water molecule (assumed 0.09 nm2, N—the Avogadro number, S BET—the specific surface area of the tested adsorbents (m2/g), TG max—the maximum mass loss at 573 K (mg/g), M—molar mass of water (18 g/mol).

Thermal properties of the silica-titania adsorbents were performed using Differential Scanning Calorimetry (DSC PYRIS Diamond Perkin Elmer, USA). The DSC method was used to indicate the energetic effects of the interfacial phenomena, which takes place during freezing of strongly and weakly bound water connected with the surface of tested adsorbents.

Results and discussion

Low-temperature adsorption/desorption of nitrogen and pore volume distribution functions in respect to their radius for the silica-titania adsorbents are presented in Fig. 1. As follows from the course of the curves of adsorption–desorption isotherms (Fig. 1a), the smaller is the TiO2 content in the sample mass, the larger is contribution of micropores. The ST1 adsorbent is microporous, the adsorption isotherm reaches plateau at higher values of pressure and does not exhibit a hysteresis loop. With the TiO2 increase in the sample mass, drop in the micropore volume is observed. For the adsorbents ST15 and ST30 the structure becomes bimodal, i.e., we can observe two peaks corresponding to narrower pores on the curve of pore volume distribution with respect to their average radius (Fig. 1b). These values are: R = 1.04 nm and 2.13 nm for ST15, as well as R = 1.14 and 2.02 nm for ST30 samples, respectively. The isotherms of the samples ST50 and ST70 are characterized by much lower adsorption in the range of low relative pressures and distinct hysteresis loops in that of high relative pressure. This gives a reflection in the course of the pore volume distribution functions on which we observe single peaks with the values of dominant radius R dom equal to 1.89 and 2.43 nm for ST50 and ST70, respectively. The XRD analysis reveals that TiO2 is in the form of anatase. The structural parameters of these adsorbents are shown in Table 1.
Fig. 1

Low-temperature adsorption/desorption of nitrogen (a) and pore volume distribution functions in respect to their radius (b) for the silica-titania adsorbents

Figure 2 shows the experimental curves of water thermodesorption from the surface of the studied adsorbents as well as the DTG curves indicating the process rate depending on temperature. As can be seen larger the TiO2 content is, the less complex is the thermodesorption of water from the pores. Three stages of this process are observed for the adsorbents ST1, ST15, and ST30 but only two for ST50 and ST70. Thermodesorption of weakly bound water from the ST50 and ST70 samples proceeds at lower temperatures and the inflection point occurs at 110 °C (Fig. 2). The other part of the water desorbs monotonically without visible stages pointing to a quick process. However, in the case of ST1 and ST15 the amount of weakly bound water is significantly smaller than that of strongly bound water desorbing at higher temperatures (above 110 °C). The intermediate properties with respect to the proportion of weakly and strongly bound water are exhibited by ST30. Figure 2 shows the distinct differences in the course of vertical parts of the curves (desorption at different temperatures) as well as in the horizontal parts corresponding to differentiated sorption capacities of these adsorbents for water molecules. A good illustration is the summary picture presenting the curves of the water thermodesorption course in the temperature function (Fig. 3).
Fig. 2

The Q-TG and Q-DTG curves of water thermodesorption from the tested adsorbents

Fig. 3

The course of water mass loss curve as a function of the temperature increase

The shape of water thermodesorption curves correlates well with the courses of pore distribution functions with respect to their effective radius (Fig 1b). As can be seen the adsorbents ST1 and ST15 possessing mainly pores of narrow dimensions retain water molecules more strongly than the adsorbents ST50 and ST70 which exhibit porosity in the area of wider pores. However, the intermediate adsorbent ST30 is characterized by the balanced proportion between narrow pores and wide pores as evidenced by the TG curve course (Fig. 3).

Two boundary phases exist on the adsorbent surface, when water is adsorbed on it, i.e., the adsorbent/water and water/air interfaces. Thus, different reasons for a decrease in the Gibbs free energy of water at the adsorbent/water interface can be distinguished. These changes are caused by the strong adsorption of water molecules on the adsorbent surface centers (ΔG s), capillary condensation in the pores (ΔG por), and the presence of water/air interface (ΔG air) [31]. When the Gibbs free energy of adsorbed water is equal to that of water in the gas phase (this process depends on the temperature and this is the condition for evaporation of adsorbed water), water begins to desorb from the surface when its Gibbs free energy becomes equal to that of water vapor at a given temperature (enabling possibility the phase transition). The thermodynamic function of the water vapor can be calculated using the equation:
$$ \Updelta G = G - G_{\text{o}} = 0.197(T - T_{\text{o}} ) $$
(2)
where T o is the standard temperature 293 K. On the basis of \( \Updelta m_{{{\text{H}}_{2} {\text{O}}}} = f(T) \) experimental data (Q-TG) the dependences of changes in the Gibbs free energy on the concentration of the adsorbed water were determined, \( \Updelta G = f({\text{C}}_{{{\text{H}}_{ 2} {\text{O}}}} ) \).
Figure 4 presents the dependences of change of water free energy in the function of its concentration on the surface of the studied silica-titania adsorbents. The marked areas under these dependences were used to calculate the values of total surface free energy at the adsorbent/water interface (ΔG Σ). However, the parts of these areas (corresponding to low concentrations of adsorbed water) were used to calculate the surface free energy at the adsorbent/strongly bound water interface (ΔG Σ s ). The corresponding data are given in Table 2. As follows from the data in Table 2 the maximal concentration of the adsorbed water (\( {\text{C}}_{{{\text{H}}_{ 2} {\text{O}}}}^{ \max } \)) increases in the transition from the adsorbent ST1 to the adsorbent ST30 (with the increasing amount of TiO2 in the adsorbent), and then decreases in the case of ST50 and ST70. This is connected with both the structure of complex porous adsorbents and their chemical composition. The above mentioned parameters are expressed in the values of the total surface free energy at the adsorbent/water interface (ΔG Σ) and the surface free energy at the adsorbent/strongly bound water interface (ΔG Σ s ). As can be seen with the increasing content of TiO2 in the studied adsorbents, the values of total surface free energy (ΔG Σ) increase. In the case of the parameter (ΔG Σ s ), a similar tendency can be observed except to the adsorbent ST30 which is characterized by the highest value surface free energy at the adsorbent/strongly bound water interface (Fig. 5).
Fig. 4

The dependence of water free energy changes on the function of its concentration on the surface of the studied silica-titania adsorbents

Table 2

Characterization of water adsorbed on the silica-titania adsorbents surface

Sample

S BET/m2/g

\( {\text{C}}_{{{\text{H}}_{ 2} {\text{O}}}}^{ \max } \) mg/g

n

\( \Updelta G^{\text{s}} \)/kJ/mol

\( \Updelta G^{\text{b}} \)/kJ/mol

\( \Updelta G_{\Upsigma }^{\text{s}} \)/kJ/m2

\( \Updelta G_{\Upsigma }^{{}} \)/kJ/m2

ST1

924

352.4

1.15

35.4

18.6

47

261

ST15

805

362.6

1.36

37.7

16.5

86

291

ST30

702

529.8

2.27

39.0

15.0

145

438

ST50

529

478.3

2.76

37.7

16.3

92

506

ST70

353

436.2

3.72

37.3

16.7

122

710

\( {\text{C}}_{{{\text{H}}_{ 2} {\text{O}}}}^{ \max } \) is the maximal concentration of adsorbed water, n—the number of statistical adsorbed water layers, \( \Updelta G^{\text{s}} \) is a maximal value of changes in free energy for strongly adsorbed water, \( \Updelta G^{\text{b}} \) is the change in free energy of water during its evaporation from filled pores, \( \Updelta G_{\Upsigma }^{\text{s}} \) is the surface free energy at the adsorbent/strongly bound water interface, \( \Updelta G_{\Upsigma }^{{}} \) is the total surface free energy at the adsorbent/water interface

Fig. 5

The surface free energy at the adsorbent/water interface (ΔG Σ) and the number of statistical water monolayers (n) in the dependences from the TiO2 content

Figure 6 shows the dG/dM dependences as the function of statistical water monolayers, under the conditions of low coverage of adsorbent surface with water, where dG/dM is change in free energy of system with water mass changes. The value of the dG/dM derivative can be used as the analog of chemical potential in the description of isobaric process of thermodesorption. On the presented dependences one or two maxima can be observed, which indicate the formation of various types of water molecule clusters on the heterogeneous surface of the adsorbents under investigation. For the adsorbents of the smallest content of TiO2 (ST1 and ST15 samples), there occurs a smaller number of maxima compared to other adsorbents (Fig. 6). Moreover, with the increasing amount of TiO2 the observed maxima occur at thicker and thicker layers of adsorbed water, from 0.01 for ST1 up to 0.25 for the ST70 sample (Fig. 6).
Fig. 6

The dG/dM dependences as a function of statistical monolayers of water clusters for the silica-titania adsorbents

Figure 7 shows the influence of the adsorbed water concentration on the effective radius of evaporated drops of water for the studied adsorbents. Comparing the obtained results with the data in Table 1, one can assume that the average radius of the evaporating drop has the size close to R ave of the adsorbent. The numerical values of calculated radii should be treated with caution. The reason is that the basic assumption was the spherical shape of the drop and that the surface tension on the partition boundary is equal to that tension at the water/air interface. Actually a large part of the drop outline is limited by the adsorbent surface. For this surface there should be chosen a different value of interface tension from that of surface tension.
Fig. 7

The dependence of the effective radius of an evaporating drop on the concentration of adsorbed water

The curves reflecting the energetic effects connected with water freezing inside the pores of investigated samples are presented in Fig. 8. Water contained in the pores of materials of strong adsorption properties is characterized by quite different physicochemical properties from those of volumetric water. In the case of the adsorbents possessing a well developed structure of micropores (ST1, ST15, and ST30), the peaks of water freezing with the maximum at −42 °C are observed. This is caused by large impact of adsorbents surface (mainly micropores) on water molecules. In the case of the adsorbent with the intermediate content of TiO2 (ST30) there is observed the additional, distinctly formed peak of water freezing at −13 °C corresponding to that in the wider pores. This confirms the bimodal structure of this adsorbent. The peaks of water freezing for the ST50 and ST70 samples appear at about −22 °C, and their shapes indicate a large content of wide pores confirming the conclusion about their porous structure (Table 1; Fig. 1) and observations that water affected by the interactions with the surface of studied materials changes their physicochemical properties.
Fig. 8

DCS curves of water freezing in the pores of adsorbents containing the increasing amount of TiO2

Conclusions

From the results of low-temperature adsorption–desorption of nitrogen measurements it was stated that the surface area of the obtained adsorbents varies from 924.1 m2/g (1% TiO2) to 353.4 m2/g (70% TiO2). The increase of the TiO2 content in the silica-titania adsorbents results in the decrease of both its specific surface area and contribution of pores to its structure. The process of water thermodesorption from the surface of studied materials proceeds in two or three stages because of the pore distribution and TiO2 content. With the increase of TiO2 content in the studied adsorbents the values of total surface free energy (ΔG Σ) increase. The largest value of the free surface energy at the adsorbent/strongly bound water interface is exhibited by the adsorbent of intermediate content (30%) of TiO2. Different types of adsorbed water clusters occur with a larger extent of pores filling along with the increasing content of TiO2 in the sample. Freezing temperature of water contained in the pores of studied materials depends largely on their porous structure. Water freezing in micropores of the tested materials proceed at about −42 °C, whereas, the water contained in wider pores freezes already at −22 °C. Due to the well developed porous structure, the water freezing process is a multi-stage one.

Notes

Acknowledgements

This article was supported by the European Community FP7 under the Marie Curie International Research Staff Exchange Scheme (IRSES). Project No 230790.

Open Access

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Copyright information

© The Author(s) 2011

Authors and Affiliations

  • J. Skubiszewska-Zięba
    • 1
  • B. Charmas
    • 1
  • R. Leboda
    • 1
  • V. A. Tertykh
    • 2
  • V. V. Yanishpolskii
    • 2
  1. 1.Department of Chromatographic Methods, Faculty of ChemistryMaria Curie-Sklodowska UniversityLublinPoland
  2. 2.Institute of Surface ChemistryNational Academy of Science of UkraineKievUkraine

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