# Influence of Molybdenum Content and MoOx

Authors: Alberto Hernández Zapién; Juan Manuel Hernández Enríquez; Ricardo García Alamilla; Guillermo Sandoval Robles; Ulises Páramo García; Luz Arcelia García Serrano
Journal: Advances in Materials Science and Engineering
 (2014)

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## Abstract

The present work proposes to study the incorporation of molybdenum into the zirconium oxide precursor (Zr(OH)4), in order to analyze its possible repercussions on the textural and structural zirconia properties (ZrO2). For this, the Zr(OH)4 was synthesized by the sol-gel method and modified with 5, 10, and 15 wt% of molybdenum into the stabilized oxide. The synthesized materials were dried at 120°C for 24 h and then were calcined at 600°C for 3 h. The characterization of the solids was carried out by thermal analysis, X-ray diffraction, nitrogen physisorption, infrared spectroscopy, and scanning electron microscopy. The thermal analyses results showed that the change from the amorphous to the crystalline phase of ZrO2 is shifted to higher temperatures due to the presence of molybdenum content. Tetragonal phase was identified for all synthesized materials, showing a decrease in crystallinity as a function of the metal content. The textural properties were improved due to the incorporation of molybdenum into the ZrO2 structure, developing specific surface areas which are above up to four times the area of pure ZrO2. The synthesized materials presented spherical morphology with particle sizes less than 1 µm, with a change of this morphology for high metal
contents (15 wt%) being observed.


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## Body

## 1. Introduction

Catalysis is a crucial science for the chemical industry development. About 80% of manufactured chemicals are obtained by processes that require the use of a catalyst [1]. Specifically, in the oil refining industry, in processes such as isomerization and alkylation of light paraffins, which involve solid-gas reactions, require solid acid catalysts with adequate specific surface area and high thermal stability [2–5], which may be improved by manipulating some variables during the precursor synthesis. Zirconium oxide (ZrO2) has been widely studied for this type of reactions because of its acid-base properties [6–9]. This catalytic support can be synthesized via precipitation, microemulsion, hydrothermal synthesis, supercritical synthesis, pyrolysis, microwave, and the sol-gel route [10–12]. The sol-gel method has gained great diffusion since it allows preparing materials with high purity, homogeneity, and controlled final properties [13, 14]. The precursor of zirconium oxide (Zr(OH)4) can be obtained through the sol-gel method using metallic alkoxides, showing high specific surface area after being synthesized; however this parameter decreases by effect of thermal treatments to which the material is subjected for obtaining the stabilized oxide [15, 16] and this evinces its poor thermal stability. In the literature it has been reported that the stability and the specific surface area of zirconium oxide are enhanced by the addition of some promoter agents in its structure (SO
4
2
-, PO
4
3
-
, and BO
3
3
- ions), which also stabilize the tetragonal phase of ZrO2 and improve their acidic properties [2, 17–19]. However, the main disadvantage that arises when using SO
4
2
- and BO
3
3
- ions as modifiers of ZrO2 structure is the susceptibility to evacuation from the material surface when it is subjected to high thermal treatments (T
>
600°C), which leads to a decrease in the specific surface area and a possible change of the crystalline structure [20–22]. Reddy et al. [20] have reported that the addition of Al2O3 also acts as a stabilizer of the phase previously cited. The same effect has been observed in the ZrO2 with the addition of certain metal oxides such as La2O3, CeO2, Y2O3, Yb2O3, and CaO; however, these materials confer certain basic properties [23–25]. Although it has been observed that the incorporation of these stabilizing agents improves the textural and structural properties of the material, high weight percentages have a negative impact on them [26].With the aim of improving the textural and structural properties of zirconia and trying to avoid the problems associated with loss of doping agent during thermal treatment of the material, this work proposes the incorporation of molybdenum into the structure of zirconium oxide in the form of molybdate species (MoO
x
y
-), synthesizing the material by the sol-gel method and varying the metallic charge in the oxide synthesized in 5, 10, and 15 wt%.


## 2. Materials and Methods

### 2.1. Synthesis of ZrO2

The synthesis of zirconium oxide was carried out using the sol-gel method. A solution of zirconiumn-butoxide, 80 wt%, in 1-butanol was subjected to constant agitation and reflux at 65°C for 1 h. The step of hydrolysis is subsequently completed by slowly adding water/1-butanol solution dropwise. The condensation of the resulting gel was carried out keeping the system for 2 h under the same conditions of synthesis. The material obtained was aged at room temperature for 72 h and dried at 100°C for 24 h, obtaining the precursor hydroxide (Zr(OH)4). The heat treatment of the material was performed at a calcining furnace at 600°C for 3 h.


### 2.2. Synthesis ofMoO
x
y
-/ZrO2

Once synthesized, the zirconium hydroxide is proceeded to impregnate it with an ammonium heptamolybdate solution by the incipient wetness technique, attempting to deposit metal loadings in the stabilized oxide of 5, 10, and 15 wt% of molybdenum. Impregnated hydroxides were dried at 100°C for 24 h and calcined in air dynamic atmosphere for 3 h at 600°C. The nomenclature of the synthesized materials is based on the load of the deposited metal, being as follows: 5%Mo/ZrO2, 10%Mo/ZrO2, and 15%Mo/ZrO2.


### 2.3. Characterization Materials

Synthesized materials were characterized by thermogravimetry, X-ray diffraction, nitrogen physisorption, infrared spectroscopy, and scanning electron microscopy. Thermal analyses were performed on a TA Instruments Thermogravimetric Balance STD2960 Simultaneous DSC-TGA, using an extra dry air flow rate of 10 mL/min and a heating rate of 10°C/min. The diffraction patterns were obtained in an X-ray Bruker Advance D800 diffractometer which used CuKα radiation (λ
=
1.5406 Å) and a graphite monochromator in the secondary beam; the intensities of the diffraction lines were obtained in the range of 0–70° in 2-theta scale, with steps of 0.02° and 2.4 s per point. Infrared spectroscopy was carried out in a Fourier Transform Spectrometer (Perking-Elmer Spectrum One) with transparent wafers containing the sample to be analyzed and KBr as a binder; spectra were recorded at a resolution of 4 cm−1 and by coadding 16 scans. The textural characterization of the solids was determined in an Automatic Micromeritics ASAP2405NV1.03 of 6 channels and to determine the morphology of the materials a scanning electron microscope JEOL, model JSM-6390LV, at 30 KV coupled to an X-ray detector was employed.


## 2.1. Synthesis of ZrO2

The synthesis of zirconium oxide was carried out using the sol-gel method. A solution of zirconiumn-butoxide, 80 wt%, in 1-butanol was subjected to constant agitation and reflux at 65°C for 1 h. The step of hydrolysis is subsequently completed by slowly adding water/1-butanol solution dropwise. The condensation of the resulting gel was carried out keeping the system for 2 h under the same conditions of synthesis. The material obtained was aged at room temperature for 72 h and dried at 100°C for 24 h, obtaining the precursor hydroxide (Zr(OH)4). The heat treatment of the material was performed at a calcining furnace at 600°C for 3 h.


## 2.2. Synthesis ofMoO
x
y
-/ZrO2

Once synthesized, the zirconium hydroxide is proceeded to impregnate it with an ammonium heptamolybdate solution by the incipient wetness technique, attempting to deposit metal loadings in the stabilized oxide of 5, 10, and 15 wt% of molybdenum. Impregnated hydroxides were dried at 100°C for 24 h and calcined in air dynamic atmosphere for 3 h at 600°C. The nomenclature of the synthesized materials is based on the load of the deposited metal, being as follows: 5%Mo/ZrO2, 10%Mo/ZrO2, and 15%Mo/ZrO2.


## 2.3. Characterization Materials

Synthesized materials were characterized by thermogravimetry, X-ray diffraction, nitrogen physisorption, infrared spectroscopy, and scanning electron microscopy. Thermal analyses were performed on a TA Instruments Thermogravimetric Balance STD2960 Simultaneous DSC-TGA, using an extra dry air flow rate of 10 mL/min and a heating rate of 10°C/min. The diffraction patterns were obtained in an X-ray Bruker Advance D800 diffractometer which used CuKα radiation (λ
=
1.5406 Å) and a graphite monochromator in the secondary beam; the intensities of the diffraction lines were obtained in the range of 0–70° in 2-theta scale, with steps of 0.02° and 2.4 s per point. Infrared spectroscopy was carried out in a Fourier Transform Spectrometer (Perking-Elmer Spectrum One) with transparent wafers containing the sample to be analyzed and KBr as a binder; spectra were recorded at a resolution of 4 cm−1 and by coadding 16 scans. The textural characterization of the solids was determined in an Automatic Micromeritics ASAP2405NV1.03 of 6 channels and to determine the morphology of the materials a scanning electron microscope JEOL, model JSM-6390LV, at 30 KV coupled to an X-ray detector was employed.


## 3. Results and Discussion

### 3.1. Thermal Analysis

Figure1 shows the TG profile of the synthesized zirconium hydroxide, with three significant weight losses being observed: the first two localized in the range from room temperature to 200°C associated with the evacuation of surface water and alcohol used during the synthesis as well as with the water occluded in the porous structure of the material; these weight losses are related to the exits located on the DTG curve at 60 and 85°C and to the endothermic signals located on the DTA profile at 75 and 190°C (Figure 2) [27]. The third weight loss occurs in the range of 250–450°C and involves two different processes, the first one attributed to the combustion of organic compounds observed at 298°C on the DTG curve and associated with endothermic signals appearing on the DTA profile at 276 and 301°C; the second process located on the DTA curve at 421°C is related to the dehydroxylation of the material as well as the phase transformation of zirconium hydroxide from an amorphous state to a crystalline phase [16, 28].Figure 1
TGA and DTG profiles of Zr(OH)4.Figure 2
TGA and DTA profiles of Zr(OH)4.Thermogravimetric analysis of pure and modified zirconium hydroxide with molybdenum can be seen in Figure3. This figure shows that in the range from room temperature to 700°C the modified materials have a lower weight loss compared to the unmodified material; this could be related to an exchange of OH– groups by MoO
x
y
- species verified during the zirconium hydroxide step impregnation; these species attached to the zirconium oxide structure improve its stability. For the modified materials an additional weight loss occurs from 700 to 1000°C that could be related to the volatilization of molybdenum and its respective abandonments from the zirconium oxide structure due to the fact that the molybdenum has a vapor pressure of 40 mmHg at 892°C [29, 30] and this weight loss is increased depending on the metal content in the support and is associated with the exits of matter located at around 900°C in the DTG curves reported in Figure 4.Figure 3
TGA profiles of Zr(OH)4 and MoO
x
y
-/Zr(OH)4.Figure 4
DTG profiles of Zr(OH)4 and MoO
x
y
-/Zr(OH)4.The modified materials with molybdenum have a similar behavior compared to pure zirconium hydroxide in the differential thermal analysis in the range from room temperature to 400°C (Figure5) and the major difference resides in the signal attributed to the possible change of crystalline phase; this exothermic peak occurs at about 420°C for the unmodified material (Figure 2) but is shifted a higher temperatures due to the presence and content of molybdenum, results that are consistent with those reported by Sohn et al. [31]. In the case of the modified materials, the exothermic peak shows on the DTA curves up at 450°C under the same heating conditions. So far, it appears that the molybdate species (MoO
x
y
-) retard the phase transformation process due to the interaction between these species and the zirconium oxide surface causing differences in the observed exotherms. There is no weight loss during the phase transformation process (Figure 3).Figure 5
DTA profiles ofMoO
x
y
-/Zr(OH)4.


### 3.2. X-Ray Diffraction

The X-ray diffraction patterns of pure and modified zirconium oxide are presented in Figure6. Usually zirconium oxide as support involves three crystalline phases: monoclinic, tetragonal, and cubic. The zirconium oxides obtained by calcining pure and modified Zr(OH)4 at 600°C during 3 h are predominantly of tetragonal structure with diffraction lines at 30.17, 35.28, 50.34, 60.14, and 63.04° on the 2-theta scale. This observation was consistent with the crystallographic card JCPDS 00-050-1089. Generally it is accepted that, for the modified zirconium oxide with oxoanions, the nature of the surface species and the crystalline phase of the support depend on the oxoanions loading [32]. It can be seen in Figure 6 that the molybdenum content strongly influences the crystallinity of the samples. An increase in molybdenum content results in lowering of crystallinity, which may be attributed to the suppression of crystallite growth induced by the presence of molybdenum species. In the same way as observed previously in the literature, the molybdenum species present at zirconium oxide structure were able to stabilize the tetragonal phase and promote the resistance to crystal sintering [17, 18, 33]. The absence of characteristic peaks corresponding to the molybdenum trioxide in the materials 5%Mo/ZrO2 and 10%Mo/ZrO2 implies that the metallic species are interacting with the zirconium oxide structure or they are highly dispersed on its surface. According to the diffractogram of the material 15%Mo/ZrO2, a high loading of molybdenum appears to influence the appearance of the monoclinic phase, which is related to the signal at 45.21° in the 2-theta scale (JCPDS 00-072-1669) as well as the formation of MoO3 crystals with orthorhombic structure, identified with the signal 2
θ
=
23.27° which also appears on the X-ray pattern of the molybdenum trioxide of Figure 7 (JCPDS 00-005-0508).Figure 6
XRD patterns of ZrO2 and MoO
x
y
-/ZrO2, (■) tetragonal ZrO2, (□) monoclinic ZrO2, and (●) orthorhombic MoO3.Figure 7
XRD pattern of MoO3.


### 3.3. Textural Properties

The nitrogen adsorption-desorption isotherms of ZrO2 and MoO
x
y
-/ZrO2 samples are shown in Figures 8 and 9, together with the corresponding pore size distribution, depicted in Figures 10 and 11. The textural characterization data of the samples are included in Table 1. The adsorption isotherm to pure zirconium oxide is of type IV according to Brunauer-Emmett-Teller classification typical of mesoporous materials, showing either a hysteresis cycle loop type H3; this hysteresis is usually found on solids consisting of aggregates or agglomerates of particles forming slit shaped pores. The materials modified with molybdenum developed an isotherm reflecting the presence of micro- and mesoporosity, common features of types I and IV isotherms, with reduced hysteresis loops being also observed [34, 35]. The molybdenum-modified materials show a specific surface area that exceeded up to four times the value obtained to pure zirconium oxide (30 m2/g). With the increase of the molybdenum content from 5 to 10 wt%, the specific surface area of the material is increased from 118 to 143 m2/g. This implies that the presence of molybdenum plays a very important role in the stability of the porous material. However, further increase in molybdenum loading to 15 wt% resulted in a decrease of the specific surface area to 129 m2/g. Probably, when the molybdenum content increases beyond 10 wt%, pore blocking takes place due to the presence of an excessive amount of this metal and also can be related to the formation of MoO3 surface crystals which was confirmed by X-ray diffraction. The pore size distribution of the synthesized materials has been determined by BJH method applied to desorption isotherm branch. The curves of the pore size distribution showed a bimodal distribution for pure zirconium oxide centered on the mesoporous region, changing this for MoO
x
y
-/ZrO2 materials to the region micro/mesoporous.Table 1
Specific surface area and porous structure parameters of the synthesized materials.
Material
Surface area(m2/g)
Pore diameter(Å)
Pore volume(cm3/g)
ZrO2
30
56
0.046
5%Mo/ZrO2
118
41
0.067
10%Mo/ZrO2
143
34
0.100
15%Mo/ZrO2
129
38
0.089Figure 8
Nitrogen adsorption-desorption isotherm of ZrO2.Figure 9
Nitrogen adsorption-desorption isotherms ofMoO
x
y
-/ZrO2 materials.Figure 10
Pore size distribution of ZrO2.Figure 11
Pore size distribution ofMoO
x
y
-/ZrO2 materials.


### 3.4. FT-IR Spectroscopy

The infrared spectra of ZrO2 and MoO
x
y
-/ZrO2 samples are shown in Figures 12 and 13, respectively. A comparison of the spectra of pure zirconia with the modified samples confirms the presence of molybdate species (MoO
x
y
-). In all modified materials broad bands were observed in the region of 3600–3400 cm−1 attributed to the presence of bonded hydroxyl groups to the material chemical structure as well as a band at 1639 cm−1 that may be attributed to the bending vibrational modes of –OH groups belonging to molecular adsorbed water [36]. No stronger peaks related to these signals were observed on pure zirconium oxide spectrum. We also speculate that these water molecules can be weakly coordinated with the molybdate species which have the ability to create acidic sites. Stronger signals at 736, 660, and 591 cm−1 may be assigned to stretching vibration modes of Zr–O due to the crystalline zirconium oxide [37]. The interaction of molybdenum species with the zirconium atoms was responsible for the shift at position and intensity of these signals. Another difference between pure zirconium oxide and the modified samples was found in the absorption region of 975–820 cm−1. The dominant band at 975 cm−1 and the weak signal that appears at 912 cm−1 are characteristic of the stretching vibration modes of the Mo = O terminal bonds and the band at 821 cm−1 is associated with the vibration of Mo–O–Mo bridging bonds [38]. The increase in the intensity of these bands may be considered as a result of the molybdenum amount present in the material and also related to the increasing number of bonds.Figure 12
FT-IR spectrum of ZrO2 sample.Figure 13
FT-IR spectra ofMoO
x
y
-/ZrO2 materials.


### 3.5. Scanning Electron Microscopy

Figure14 shows the scanning electron microscopy obtained with the synthesized zirconium oxides. It can be seen that the ZrO2 exhibits spherical particles with sizes less than 1 μm and a very heterogeneous particle size distribution. The morphological characteristics of the samples are slightly modified upon molybdenum addition. The modified materials with low loadings of molybdenum (5%Mo/ZrO2 and 10%Mo/ZrO2) presented a better uniformity in particle size, being observed as materials consisting of spherical agglomerates, while the material 15%Mo/ZrO2 showed that this metal loading affected the loss of spherical morphology of the material, identifying the presence of some particles with rectangular geometries, similar to that exhibited in electron microscopy of MoO3.Figure 14
Scanning electron microscopy of ZrO2, MoO
x
y
-/ZrO2, and MoO3.


## 3.1. Thermal Analysis

Figure1 shows the TG profile of the synthesized zirconium hydroxide, with three significant weight losses being observed: the first two localized in the range from room temperature to 200°C associated with the evacuation of surface water and alcohol used during the synthesis as well as with the water occluded in the porous structure of the material; these weight losses are related to the exits located on the DTG curve at 60 and 85°C and to the endothermic signals located on the DTA profile at 75 and 190°C (Figure 2) [27]. The third weight loss occurs in the range of 250–450°C and involves two different processes, the first one attributed to the combustion of organic compounds observed at 298°C on the DTG curve and associated with endothermic signals appearing on the DTA profile at 276 and 301°C; the second process located on the DTA curve at 421°C is related to the dehydroxylation of the material as well as the phase transformation of zirconium hydroxide from an amorphous state to a crystalline phase [16, 28].Figure 1
TGA and DTG profiles of Zr(OH)4.Figure 2
TGA and DTA profiles of Zr(OH)4.Thermogravimetric analysis of pure and modified zirconium hydroxide with molybdenum can be seen in Figure3. This figure shows that in the range from room temperature to 700°C the modified materials have a lower weight loss compared to the unmodified material; this could be related to an exchange of OH– groups by MoO
x
y
- species verified during the zirconium hydroxide step impregnation; these species attached to the zirconium oxide structure improve its stability. For the modified materials an additional weight loss occurs from 700 to 1000°C that could be related to the volatilization of molybdenum and its respective abandonments from the zirconium oxide structure due to the fact that the molybdenum has a vapor pressure of 40 mmHg at 892°C [29, 30] and this weight loss is increased depending on the metal content in the support and is associated with the exits of matter located at around 900°C in the DTG curves reported in Figure 4.Figure 3
TGA profiles of Zr(OH)4 and MoO
x
y
-/Zr(OH)4.Figure 4
DTG profiles of Zr(OH)4 and MoO
x
y
-/Zr(OH)4.The modified materials with molybdenum have a similar behavior compared to pure zirconium hydroxide in the differential thermal analysis in the range from room temperature to 400°C (Figure5) and the major difference resides in the signal attributed to the possible change of crystalline phase; this exothermic peak occurs at about 420°C for the unmodified material (Figure 2) but is shifted a higher temperatures due to the presence and content of molybdenum, results that are consistent with those reported by Sohn et al. [31]. In the case of the modified materials, the exothermic peak shows on the DTA curves up at 450°C under the same heating conditions. So far, it appears that the molybdate species (MoO
x
y
-) retard the phase transformation process due to the interaction between these species and the zirconium oxide surface causing differences in the observed exotherms. There is no weight loss during the phase transformation process (Figure 3).Figure 5
DTA profiles ofMoO
x
y
-/Zr(OH)4.


## 3.2. X-Ray Diffraction

The X-ray diffraction patterns of pure and modified zirconium oxide are presented in Figure6. Usually zirconium oxide as support involves three crystalline phases: monoclinic, tetragonal, and cubic. The zirconium oxides obtained by calcining pure and modified Zr(OH)4 at 600°C during 3 h are predominantly of tetragonal structure with diffraction lines at 30.17, 35.28, 50.34, 60.14, and 63.04° on the 2-theta scale. This observation was consistent with the crystallographic card JCPDS 00-050-1089. Generally it is accepted that, for the modified zirconium oxide with oxoanions, the nature of the surface species and the crystalline phase of the support depend on the oxoanions loading [32]. It can be seen in Figure 6 that the molybdenum content strongly influences the crystallinity of the samples. An increase in molybdenum content results in lowering of crystallinity, which may be attributed to the suppression of crystallite growth induced by the presence of molybdenum species. In the same way as observed previously in the literature, the molybdenum species present at zirconium oxide structure were able to stabilize the tetragonal phase and promote the resistance to crystal sintering [17, 18, 33]. The absence of characteristic peaks corresponding to the molybdenum trioxide in the materials 5%Mo/ZrO2 and 10%Mo/ZrO2 implies that the metallic species are interacting with the zirconium oxide structure or they are highly dispersed on its surface. According to the diffractogram of the material 15%Mo/ZrO2, a high loading of molybdenum appears to influence the appearance of the monoclinic phase, which is related to the signal at 45.21° in the 2-theta scale (JCPDS 00-072-1669) as well as the formation of MoO3 crystals with orthorhombic structure, identified with the signal 2
θ
=
23.27° which also appears on the X-ray pattern of the molybdenum trioxide of Figure 7 (JCPDS 00-005-0508).Figure 6
XRD patterns of ZrO2 and MoO
x
y
-/ZrO2, (■) tetragonal ZrO2, (□) monoclinic ZrO2, and (●) orthorhombic MoO3.Figure 7
XRD pattern of MoO3.


## 3.3. Textural Properties

The nitrogen adsorption-desorption isotherms of ZrO2 and MoO
x
y
-/ZrO2 samples are shown in Figures 8 and 9, together with the corresponding pore size distribution, depicted in Figures 10 and 11. The textural characterization data of the samples are included in Table 1. The adsorption isotherm to pure zirconium oxide is of type IV according to Brunauer-Emmett-Teller classification typical of mesoporous materials, showing either a hysteresis cycle loop type H3; this hysteresis is usually found on solids consisting of aggregates or agglomerates of particles forming slit shaped pores. The materials modified with molybdenum developed an isotherm reflecting the presence of micro- and mesoporosity, common features of types I and IV isotherms, with reduced hysteresis loops being also observed [34, 35]. The molybdenum-modified materials show a specific surface area that exceeded up to four times the value obtained to pure zirconium oxide (30 m2/g). With the increase of the molybdenum content from 5 to 10 wt%, the specific surface area of the material is increased from 118 to 143 m2/g. This implies that the presence of molybdenum plays a very important role in the stability of the porous material. However, further increase in molybdenum loading to 15 wt% resulted in a decrease of the specific surface area to 129 m2/g. Probably, when the molybdenum content increases beyond 10 wt%, pore blocking takes place due to the presence of an excessive amount of this metal and also can be related to the formation of MoO3 surface crystals which was confirmed by X-ray diffraction. The pore size distribution of the synthesized materials has been determined by BJH method applied to desorption isotherm branch. The curves of the pore size distribution showed a bimodal distribution for pure zirconium oxide centered on the mesoporous region, changing this for MoO
x
y
-/ZrO2 materials to the region micro/mesoporous.Table 1
Specific surface area and porous structure parameters of the synthesized materials.
Material
Surface area(m2/g)
Pore diameter(Å)
Pore volume(cm3/g)
ZrO2
30
56
0.046
5%Mo/ZrO2
118
41
0.067
10%Mo/ZrO2
143
34
0.100
15%Mo/ZrO2
129
38
0.089Figure 8
Nitrogen adsorption-desorption isotherm of ZrO2.Figure 9
Nitrogen adsorption-desorption isotherms ofMoO
x
y
-/ZrO2 materials.Figure 10
Pore size distribution of ZrO2.Figure 11
Pore size distribution ofMoO
x
y
-/ZrO2 materials.


## 3.4. FT-IR Spectroscopy

The infrared spectra of ZrO2 and MoO
x
y
-/ZrO2 samples are shown in Figures 12 and 13, respectively. A comparison of the spectra of pure zirconia with the modified samples confirms the presence of molybdate species (MoO
x
y
-). In all modified materials broad bands were observed in the region of 3600–3400 cm−1 attributed to the presence of bonded hydroxyl groups to the material chemical structure as well as a band at 1639 cm−1 that may be attributed to the bending vibrational modes of –OH groups belonging to molecular adsorbed water [36]. No stronger peaks related to these signals were observed on pure zirconium oxide spectrum. We also speculate that these water molecules can be weakly coordinated with the molybdate species which have the ability to create acidic sites. Stronger signals at 736, 660, and 591 cm−1 may be assigned to stretching vibration modes of Zr–O due to the crystalline zirconium oxide [37]. The interaction of molybdenum species with the zirconium atoms was responsible for the shift at position and intensity of these signals. Another difference between pure zirconium oxide and the modified samples was found in the absorption region of 975–820 cm−1. The dominant band at 975 cm−1 and the weak signal that appears at 912 cm−1 are characteristic of the stretching vibration modes of the Mo = O terminal bonds and the band at 821 cm−1 is associated with the vibration of Mo–O–Mo bridging bonds [38]. The increase in the intensity of these bands may be considered as a result of the molybdenum amount present in the material and also related to the increasing number of bonds.Figure 12
FT-IR spectrum of ZrO2 sample.Figure 13
FT-IR spectra ofMoO
x
y
-/ZrO2 materials.


## 3.5. Scanning Electron Microscopy

Figure14 shows the scanning electron microscopy obtained with the synthesized zirconium oxides. It can be seen that the ZrO2 exhibits spherical particles with sizes less than 1 μm and a very heterogeneous particle size distribution. The morphological characteristics of the samples are slightly modified upon molybdenum addition. The modified materials with low loadings of molybdenum (5%Mo/ZrO2 and 10%Mo/ZrO2) presented a better uniformity in particle size, being observed as materials consisting of spherical agglomerates, while the material 15%Mo/ZrO2 showed that this metal loading affected the loss of spherical morphology of the material, identifying the presence of some particles with rectangular geometries, similar to that exhibited in electron microscopy of MoO3.Figure 14
Scanning electron microscopy of ZrO2, MoO
x
y
-/ZrO2, and MoO3.


## 4. Conclusions

The results of this work demonstrate that the molybdated zirconium oxide is a material with better thermal stability than pure zirconium oxide. The presence and content of molybdenum retarded the transformation of zirconium hydroxide from an amorphous state to a crystalline phase of the zirconium oxide, moving this shift to higher temperatures than 420°C for the modified materials. Both synthesis variables and calcination temperature allowed developing nanocrystalline materials with tetragonal structure characteristic of ZrO2, being the doping agent responsible for the lower crystallinity developed in the synthesized materials. The incorporation of the molybdenum into the zirconium oxide structure caused a promoting effect on its textural properties, with an increase of the specific surface area and pore volume being observed. The molybdenum-modified materials developed a specific surface area that exceeded up to four times the value obtained for pure zirconium oxide. The doping agent influenced the formation of spherical agglomerates with particle sizes smaller than 1 μm, changing the material morphology to high loadings of molybdenum. Future researches are in progress in order to study the influence of the molybdenum species interaction with the zirconium oxide structure and its effect on the acidic and catalytic properties of these materials.



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*Source: 432031-2014-12-18.xml*