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Morphology evolution and quantitative analysis of β-MoO3 and α-MoO3

  • Lu Wang , Meng-Chao Li , Guo-Hua Zhang EMAIL logo and Zheng-Liang Xue EMAIL logo
Published/Copyright: November 30, 2020
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High Temperature Materials and Processes
From the journal High Temperature Materials and Processes Volume 39 Issue 1

Abstract

The morphology evolution from monoclinic molybdenum trioxide (β-MoO3) to orthorhombic molybdenum trioxide (α-MoO3) and quantitative analyses of their mixtures were examined. It was found that the morphology (from spherical to elliptical shape) and color (from green to white) displayed obvious changes when β-MoO3 converted to α-MoO3 in ambient air at 773 K. The transformation from β-MoO3 to α-MoO3 resulted from a change of the internal crystalline structure. The mass percent of β-MoO3 in MoO3 mixtures showed an excellent linear relationship with the relative intensity ratio of the strongest peaks in X-ray diffraction patterns. This approach provides a simple and time-saving method to evaluate the amount of β-MoO3, which is a promising material in catalyst and electrochemical applications, in such mixtures. This finding may provide guidance for the analysis of catalytic performance of MoO3 mixtures. In addition, it was found that β-MoO3 can be easily decomposed into suboxides such as MoO2 and Mo4O11 in pure argon gas atmosphere. The possible decomposition mechanism of β-MoO3 is discussed.

Keywords: morphology; molybdenum trioxide; quantitative analysis; decomposition

1 Introduction

Transition metal oxides, such as V2O5, CrO3, WO3, and MoO3, show several types of complex structures, formed mainly by two- or three-dimensional frameworks of octahedral or tetrahedrals [1,2,3]. Among these materials, MoO3 has been recognized as a promising material for a rapidly increasing number of applications such as chemical synthesis, petroleum refining, gas sensor devices, photoluminescence, photochromism, electrochromism, smart windows, catalysis, and display devices [4]. MoO3 has different structures that can be divided into four polymorphs [5,6,7,8,9]: (1) thermally stable orthorhombic phase, α-MoO3; (2) metastable monoclinic phase, β-MoO3; (3) metastable phase at high-pressure conditions, β′-MoO3; and (4) hexagonal phase, h-MoO3. In all these MoO3 structures, the MoO6 octahedron is the primary unit, and its arrangement results in differences in the structures. The two most commonly studied polymorphs are α-MoO3 and β-MoO3; however, β-MoO3 is believed to possess more novel and enhanced properties in catalysis and electrochemical applications when compared with α-MoO3 [10]. It is regrettable that the synthesis of pure β-MoO3 is usually difficult at ambient conditions [11,12], whereas mixtures of α-MoO3 and β-MoO3 are much easier to produce [13,14,15,16]. To make full use of the mixtures of α-MoO3 and β-MoO3 that are usually produced, it is necessary to quantitatively analyze the mixtures and evaluate the amount of β-MoO3, which may be an evaluation index, and to better understand the properties of the mixtures.

X-ray diffraction (XRD) is widely used for the quantitative analysis of geological samples [17,18]. Hillier [19] conducted the accurate quantitative analysis of clay and other minerals in sandstones by XRD using the relative intensity ratio (RIR), which gave accuracy within ±3 mass% at the 95% confidence level. Vaverka and Sakurai [20] investigated the composition of steelmaking slag, and the amount of free lime was determined by the X-ray powder diffraction and the standard addition method. Recently, Shu et al. [21] adopted the quantitative XRD analysis to calculate the ratio of mass percentages of reactant (CaWO4) and product (W) from the intensities of the strongest peaks, from which fractional conversion was calculated, thus enabling the kinetics of reduction of CaWO4 by Si to be successfully described.

Although many methods have been used for quantitative determination of different sample mixtures, XRD is nondestructive, and the samples can be used for other chemical analyses. However, there are no specific reports on the quantitative relationship between α-MoO3 and β-MoO3. In the present study, the quantitative XRD analysis was used to determine the quantitative relationship between α-MoO3 and β-MoO3 and to evaluate the amount of β-MoO3 in mixtures. The morphology evolution from β-MoO3 (spherical) to α-MoO3 and the possible decomposition mechanism of β-MoO3 were also elucidated.

2 Materials and experimental procedures

2.1 Raw materials (β-MoO3)

Pure ultra-fine β-MoO3 (green), prepared by the method of sublimation [22,23], was used. The X-ray diffraction pattern of the sample is shown in Figure 1. The intensity of the strongest peak for this sample was located at 2θ = 23.04° with a reflection of (011). Field-emission scanning electron microscopy (FE-SEM) images of samples at different magnifications are shown in Figure 2. All powders appeared to have a spherical shape and fine crystalline size although their size was nonuniform.

Figure 1 X-ray diffraction pattern of the studied β-MoO3 sample.
Figure 1

X-ray diffraction pattern of the studied β-MoO3 sample.

Figure 2 Filed-emission scanning electron micrographs of the studied β-MoO3 sample with different magnifications: (a) 20000 times; (b) 50000 times.
Figure 2

Filed-emission scanning electron micrographs of the studied β-MoO3 sample with different magnifications: (a) 20000 times; (b) 50000 times.

2.2 Preparation of α-MoO3

The transformation temperature from β-MoO3 to α-MoO3 obtained from the previous literature [9,10,15] is around at 673–723 K. Therefore, in the present study, α-MoO3 was prepared by roasting β-MoO3 at 773 K in the air; the higher roasting temperature was used to complete the transformation within a short time and to control the MoO3 vapor. After confirming that the prepared products were all pure α-MoO3, samples were prepared for morphology observation and used to synthesize mixed MoO3 specimens.

2.3 Preparation of mixtures of β-MoO3 and α-MoO3

To identify the quantitative relationship between β-MoO3 and α-MoO3, standard mixtures with a mass ratio (W) of β-MoO3 to the total mass of β-MoO3 and α-MoO3 that varied from 0 to 1 were prepared, i.e.:

(1)W=mβ-MoO3mβ-MoO3+mα-MoO3,

where W was in the range of 0–1.

After carefully weighing and mixing β-MoO3 and α-MoO3 based on the specified mass ratio, the mixtures were homogenized for 30 min by milling in an agate mortar and then subjected to the quantitative XRD analysis.

The total mass of mixtures of β-MoO3 and α-MoO3 was fixed at 500 mg. The morphologies of β-MoO3 and α-MoO3 were observed by FE-SEM (ZEISS SUPRA 55, Oberkochen, Germany). Phase compositions were analyzed by the XRD (Model TTR III, Rigaku Corporation, Japan) using Cu Kα-filtered radiation with a scanning speed of 6°/min and scanning step of 0.02°.

3 Results and discussion

3.1 Crystalline modification and morphology evolution

Figure 3 shows the XRD pattern of the roasted products. It can be seen that pure α-MoO3 can be prepared by roasting β-MoO3 at 773 K in air. In addition, the color was converted from green to white, which demonstrated that the transformation from β-MoO3 to α-MoO3 is photochromic. The intensity of the strongest peak of α-MoO3 was located at 2θ = 27.36° with a reflection of (021). FE-SEM micrographs of the as-prepared α-MoO3 at different magnifications are shown in Figure 4. The morphologies of the as-prepared α-MoO3 no longer maintained the perfect spherical shape of β-MoO3 as shown in Figure 2. Numerous spiral fringes formed around the oval α-MoO3 particles, which led to the formation of a layer structure.

Figure 3 X-ray diffraction pattern of the as-prepared α-MoO3.
Figure 3

X-ray diffraction pattern of the as-prepared α-MoO3.

Figure 4 Field-emission scanning electron micrographs of the as-prepared α-MoO3 with different magnifications: (a) 15000 times; (b) 50000 times.
Figure 4

Field-emission scanning electron micrographs of the as-prepared α-MoO3 with different magnifications: (a) 15000 times; (b) 50000 times.

The changes of the morphology and the color on conversion from β-MoO3 to α-MoO3 indicated that the structures of the two phases were different. The crystal structure of β-MoO3 shown in Figure 5 indicated that β-MoO3 has a ReO3-type structure in which the MoO6 octahedrons only share corners with each other; each oxygen atom is shared by two octahedrons. In contrast, the crystal structure of α-MoO3 (α-MoO11O22O33) has a unique two-dimensional layer structure in which each layer is built up of MoO6 octahedrons connected along ac-planes by common edges and corners to form zigzag rows and along ab-planes by common corners only, as shown in Figure 6. The interlayer interaction is weak and bounded in the a-axis direction by van der Waals forces. The transformation from β-MoO3 to α-MoO3 is explained by the metal off-center displacement toward O1 (and a little less toward O2) centers, which is stabilized by an increase in covalence between the Mo and O atoms [24]. When heating β-MoO3 at T = 773 K in air, the crystals mainly grow by coalescence with neighboring crystallites, driven by the heat treatment process, and the crystal has a tendency to form a layer structure, so the morphology of α-MoO3 has many spiral fringes.

Figure 5 Crystal structure of β-MoO3.
Figure 5

Crystal structure of β-MoO3.

Figure 6 Crystal structure of α-MoO3.
Figure 6

Crystal structure of α-MoO3.

3.2 Determination of quantitative relationship curves

Quantitative curves were determined by using the quantitative X-ray analysis based on RIR values [18]. The ratios of the mass of β-MoO3 to the total mass of β-MoO3 and α-MoO3 were calculated by the intensities of the strongest peaks for β-MoO3 (peak (011)) and α-MoO3 (peak (021)). The XRD patterns of mixtures of β-MoO3 and α-MoO3 at different mass ratios are displayed in Figure 7. The intensity of the strongest peak of β-MoO3 gradually increased and that of α-MoO3 gradually decreased with the increase of mass ratio (W). The intensity changes are listed in Table 1. The values of Iβ/(Iβ + Iα) had a strong linear relationship with W, as shown by the results presented in Figure 8. According to these results, it is easy to obtain the mass percent of β-MoO3 in mixtures of β-MoO3 and α-MoO3.

Figure 7 X-ray diffraction patterns of mixtures of β-MoO3 and α-MoO3. (a) Changes of intensity of strongest peaks of β-MoO3 and (b) changes of intensity of strongest peaks of α-MoO3 (W represents the ratio of the mass of β-MoO3 to the total mass of β-MoO3 and α-MoO3).
Figure 7

X-ray diffraction patterns of mixtures of β-MoO3 and α-MoO3. (a) Changes of intensity of strongest peaks of β-MoO3 and (b) changes of intensity of strongest peaks of α-MoO3 (W represents the ratio of the mass of β-MoO3 to the total mass of β-MoO3 and α-MoO3).

Table 1

Changes of intensity of strongest peaks of β-MoO3 and α-MoO3 for different mixture ratios.

W00.20.40.60.81
Iβ/(a.u.)03,2156,0908,09510,43514,970
Iα/(a.u.)11,86010,3107,8055,2102,8300
Iβ/(Iβ + Iα)00.23770.43830.60840.78671
Figure 8 Plot of Iβ/(Iβ + Iα) as a function of W, the ratio of β-MoO3 to the sum of β-MoO3 and α-MoO3.
Figure 8

Plot of Iβ/(Iβ + Iα) as a function of W, the ratio of β-MoO3 to the sum of β-MoO3 and α-MoO3.

It is worth noting that another RIR method that measures the integrated peak intensity may have advantages and higher accuracy, but it is hard to accurately measure the integrated intensity and deal with interferences from other phases. In the present study, it was obvious that the strongest peak of β-MoO3 had some overlap with the small peak of α-MoO3, as shown in Figure 7(a), so it would be difficult to accurately measure the integrated intensity. If we adopted the multiple-peak separation method, it would waste a lot of time and have no practical application. Moreover, although the application of the Riveted quantitative analysis has demonstrated its excellent potential for complex samples, the time required for data processing is very long and does little to popularize its application. In contrast, the RIR method proposed in this study (measurement of the intensity of the strongest peaks of different phases) exhibits its own advantages: it is easy, quick, time-saving, and has high accuracy. Therefore, this method can be widely applied for the rough quantitative analysis of mixtures of β-MoO3 and α-MoO3. In the present study, both β-MoO3 and α-MoO3 had a small particle size (spherical or oval shaped, respectively), and so preferred orientation was eliminated. If the preferred orientation existed, for example, if peaks with a reflection of (0k0) for α-MoO3 were stronger, this method could not be applied.

3.3 Decomposition of β-MoO3

Before successfully preparing α-MoO3 by roasting β-MoO3 at 773 K in air, another method was attempted, that is, roasting β-MoO3 at 773 K in a highly pure Ar atmosphere (<5 ppm O2); however, pure α-MoO3 could not be obtained. The corresponding XRD pattern is shown in Figure 9. The roasted products were very complicated and included not only α-MoO3 but also MoO2 and Mo4O11. Here, Mo4O11 included two crystalline structures: orthorhombic Mo4O11 (o-Mo4O11) and monoclinic Mo4O11 (m-Mo4O11). In addition, the color of the roasted products was dark or gray, rather than white, which is shown in Figure 10.

Figure 9 X-ray diffraction pattern of products obtained by roasting β-MoO3 at 773 K in highly pure argon atmosphere.
Figure 9

X-ray diffraction pattern of products obtained by roasting β-MoO3 at 773 K in highly pure argon atmosphere.

Figure 10 Color changes of roasted products obtained at 773 K: (a) raw β-MoO3; roasted under (b) air and (c) pure argon atmospheres.
Figure 10

Color changes of roasted products obtained at 773 K: (a) raw β-MoO3; roasted under (b) air and (c) pure argon atmospheres.

It has been reported that raw green β-MoO3 may contain a number of oxygen vacancies [25,26,27]. When roasting β-MoO3 in air, the samples have enough opportunity to interact with O2. Maximum interaction between air and β-MoO3 is important to ensure that the following chemical equilibrium is shifted to the left [28]:

(2)2MoO3⟶⟵AirAr2MoO3-x+xO2

Oxygen exchange between the lattice and air has been investigated using isotope (18O2) labeling and Raman spectroscopy, which showed that gaseous O2 is able to incorporate into the oxygen-deficient β-MoO3 [29]. Therefore, perfect α-MoO3 can be prepared under air; however, when roasting β-MoO3 in the argon atmosphere, no O2 was provided to counter the oxygen-deficient β-MoO3, which led to shifting of the chemical equilibrium (2) to the right and the production of low-valent molybdenum oxides, such as MoO2 and Mo4O11. Once the oxygen defects were exhausted, the remaining components formed perfect α-MoO3. Therefore, different molybdenum–oxygen compounds can co-exist in the roasted products created under argon atmosphere conditions. The residue of α-MoO3 also indicated that α-MoO3 cannot be decomposed under the current experiment conditions, which was further supported by the data given in Figure 11. Figure 11 shows that whether using air or argon atmosphere, pure α-MoO3 was the only phase present in the final roasted products, that is, pure α-MoO3 cannot be decomposed, but β-MoO3 can be easily decomposed into MoO2 and Mo4O11. The corresponding decomposition correlations are summarized in Figure 12.

Figure 11 X-ray diffraction patterns of products obtained by roasting highly pure α-MoO3 in different atmospheres.
Figure 11

X-ray diffraction patterns of products obtained by roasting highly pure α-MoO3 in different atmospheres.

Figure 12 Schematic of the transformation of β-MoO3 under different conditions.
Figure 12

Schematic of the transformation of β-MoO3 under different conditions.

4 Conclusions

In the present study, the morphology evolution and the quantitative analysis of β-MoO3 and α-MoO3 were clarified. It was found that the morphology and color displayed obvious changes when β-MoO3 was transformed into α-MoO3. Spherical-shaped β-MoO3 had the tendency to form oval-shaped α-MoO3 when the heating temperature was around 773 K. XRD was used to quantitatively analyze the amount of β-MoO3 in mixtures of β-MoO3 and α-MoO3. It was found that the mass of β-MoO3 in the mixtures had a strong linear relationship with the intensities of the strongest peaks of β-MoO3 and α-MoO3. This provides an easy and convenient way to determine the amount of β-MoO3 in MoO3 mixtures. This approach may provide guidance for evaluation of the catalytic efficiency of MoO3 mixtures. In addition, the decomposition of β-MoO3 under argon gas atmosphere may result from the existing oxygen defects, which may contribute to the formation of MoO2 and Mo4O11.

Acknowledgments

The authors gratefully acknowledge the financial support from the National Natural Science Foundation of China (Grant Nos. 51474141 and 51874214), Guangdong Basic and Applied Basic Research Foundation (2019A1515110361), and Hubei Young Talents Development Project (1010048).

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Received: 2018-10-11
Accepted: 2019-03-11
Published Online: 2020-11-30

© 2020 Lu Wang et al., published by De Gruyter

This work is licensed under the Creative Commons Attribution 4.0 International License.

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  50. Microstructure evolution of TC4 powder by spark plasma sintering after hot deformation
  51. The effect of M (M = Ce, Zr, Ce–Zr) on rolling microstructure and mechanical properties of FH40
  52. Phase evolution and oxidation characteristics of the Nd–Fe–B and Ce–Fe–B magnet scrap powder during the roasting process
  53. Assessment of impact mechanical behaviors of rock-like materials heated at 1,000°C
  54. Effects of solution and aging treatment parameters on the microstructure evolution of Ti–10V–2Fe–3Al alloy
  55. Effect of adding yttrium on precipitation behaviors of inclusions in E690 ultra high strength offshore platform steel
  56. Dephosphorization of hot metal using rare earth oxide-containing slags
  57. Kinetic analysis of CO2 gasification of biochar and anthracite based on integral isoconversional nonlinear method
  58. Optimization of heat treatment of glass-ceramics made from blast furnace slag
  59. Study on microstructure and mechanical properties of P92 steel after high-temperature long-term aging at 650°C
  60. Effects of rotational speed on the Al0.3CoCrCu0.3FeNi high-entropy alloy by friction stir welding
  61. The investigation on the middle period dephosphorization in 70t converter
  62. Effect of cerium on the initiation of pitting corrosion of 444-type heat-resistant ferritic stainless steel
  63. Effects of quenching and partitioning (Q&P) technology on microstructure and mechanical properties of VC particulate reinforced wear-resistant alloy
  64. Study on the erosion of Mo/ZrO2 alloys in glass melting process
  65. Effect of Nb addition on the solidification structure of Fe–Mn–C–Al twin-induced plasticity steel
  66. Damage accumulation and lifetime prediction of fiber-reinforced ceramic-matrix composites under thermomechanical fatigue loading
  67. Morphology evolution and quantitative analysis of β-MoO3 and α-MoO3
  68. Microstructure of metatitanic acid and its transformation to rutile titanium dioxide
  69. Numerical simulation of nickel-based alloys’ welding transient stress using various cooling techniques
  70. The local structure around Ge atoms in Ge-doped magnetite thin films
  71. Friction stir lap welding thin aluminum alloy sheets
  72. Review Article
  73. A review of end-point carbon prediction for BOF steelmaking process
https://doi.org/10.1515/htmp-2020-0093
Keywords for this article
morphology; molybdenum trioxide; quantitative analysis; decomposition
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  48. Development and experimental research of a low-thermal asphalt material for grouting leakage blocking
  49. A downscaling cold model for solid flow behaviour in a top gas recycling-oxygen blast furnace
  50. Microstructure evolution of TC4 powder by spark plasma sintering after hot deformation
  51. The effect of M (M = Ce, Zr, Ce–Zr) on rolling microstructure and mechanical properties of FH40
  52. Phase evolution and oxidation characteristics of the Nd–Fe–B and Ce–Fe–B magnet scrap powder during the roasting process
  53. Assessment of impact mechanical behaviors of rock-like materials heated at 1,000°C
  54. Effects of solution and aging treatment parameters on the microstructure evolution of Ti–10V–2Fe–3Al alloy
  55. Effect of adding yttrium on precipitation behaviors of inclusions in E690 ultra high strength offshore platform steel
  56. Dephosphorization of hot metal using rare earth oxide-containing slags
  57. Kinetic analysis of CO2 gasification of biochar and anthracite based on integral isoconversional nonlinear method
  58. Optimization of heat treatment of glass-ceramics made from blast furnace slag
  59. Study on microstructure and mechanical properties of P92 steel after high-temperature long-term aging at 650°C
  60. Effects of rotational speed on the Al0.3CoCrCu0.3FeNi high-entropy alloy by friction stir welding
  61. The investigation on the middle period dephosphorization in 70t converter
  62. Effect of cerium on the initiation of pitting corrosion of 444-type heat-resistant ferritic stainless steel
  63. Effects of quenching and partitioning (Q&P) technology on microstructure and mechanical properties of VC particulate reinforced wear-resistant alloy
  64. Study on the erosion of Mo/ZrO2 alloys in glass melting process
  65. Effect of Nb addition on the solidification structure of Fe–Mn–C–Al twin-induced plasticity steel
  66. Damage accumulation and lifetime prediction of fiber-reinforced ceramic-matrix composites under thermomechanical fatigue loading
  67. Morphology evolution and quantitative analysis of β-MoO3 and α-MoO3
  68. Microstructure of metatitanic acid and its transformation to rutile titanium dioxide
  69. Numerical simulation of nickel-based alloys’ welding transient stress using various cooling techniques
  70. The local structure around Ge atoms in Ge-doped magnetite thin films
  71. Friction stir lap welding thin aluminum alloy sheets
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  73. A review of end-point carbon prediction for BOF steelmaking process
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