ABSTRACT

Glass composition of fixed values of the structural factor R(CdO/B₂O₃) = 0.5 and K(SiO₂\B₂O₃) = 0.5 in borosilicate glass modified by CdO has been studied by different techniques. The amorphous structure of as prepared glass was confirmed by both XRD and EDP spectroscopy. The amorphous samples were treated thermally to be transformed to suitable type of crystalline glass ceramic. Based on SEM and TEM data, the bulk crystallized network was developed by treating the glasses at high treatment route (950˚C - 1100˚C) for a specific time (8 hours). Crystalline Al₄B₂O₉ and Al₁₈B₄O₃₃ whisker phases are simply detected by X-ray diffraction spectroscopy. The scanning and transmission electron microscopes (SEM and TEM) have confirmed that aluminum borate crystalline phases in the form of whiskers (rods) species are the main formed type. Both size and concentration of the whisker species were increased with increasing temperature of thermal heat treatment. Formation of this type of crystals (whiskers) leads to interlocking microstructure and as a direct result, an increase in hardness number, glass transition temperature is simply evidenced. Glass-ceramics synthesized in this study can be applied as high temperature resistant materials because their microstructures can resist micro-cracking upon indentation. The crack length due to indentation process is reduced by increasing concentration of crystalline road or whisker like structure.

Keywords:

Glasses and Glass Ceramics, Whisker Phases, Crystalline Structure-X-Diffraction

1. Introduction

Ceramic or glass ceramics in the systems SiO₂-Al₂O₃, Al₂O₃-B₂O₃ and Al₂O₃-B₂O₃-SiO₂ [1] [2] [3] [4] [5] have been considered as important and versatile compounds. Their properties include high thermal stability, very low thermal expansion, low heat conductivity, high creep and corrosion resistance and high stiffness [1] [2] [3] . Special attention has been paid toward glass ceramics containing some specific types of crystals. In this regard whiskers type is useful substance applied to resist deformation and crack propagation in materials [2] [3] [4] [5] . Whisker is generally referred to a certain phase with high aspect ratio (i.e. length/diameter). Presence of crystals of road like shapes in the glass ceramic matrix reinforces its network structure [5] [6] [7] . The direct growth of dispersed whiskers in a glass matrix to form a glass-ceramic leads to improvements of material properties especially mechanical properties. This includes increased fracture toughness, hardness and improved thermal shock resistance [2] [4] [5] . Aluminum borate whiskers are considered to have great potentials for fabricating hard and tough topographical microstructures stable for applications.

The crystallization behavior of glasses in the Al₂O₃-B₂O₃-SiO₂ system has recently been investigated [4] [5] . It was showing that whisker of aluminum borate phase was crystallized out above glass transition temperature of the as-prepared glass. Several studies have reported that the bulk crystallization of borosilicate glasses can be affected by different factors, for example change of the glass composition, thermal heat treatment and irradiation processes. All have a great effect on bulky crystallization of the glass or glass ceramics [2] [3] [4] [8] [9] [10] . Crystalline Al₄B₂O₉ and Al₁₈B₄O₃₃ phases are simply formed in aluminum borosilicate glasses by effect of heat treatment [2] [4] [11] .

The size of aluminum borate whiskers/rods increases with increasing time of thermal treating. Usually the whisker/rod-like crystals are uniformly oriented throughout the microstructure in the heat treated samples [2] [8] [9] [10] [11] . This led to a structure characterized with several types of sub crystals which are joint together firmly and hence an increase in hardness and fracture toughness is observed. As a result, the microstructure of such materials can resist micro-cracking and scratching upon indentation.

This work is aimed to determine the phase evolution, microstructures, micro hardness and crack propagation in the investigated glass and glass ceramics. The additional aim of this study is to shed more light on the effect of thermal heat treatments process on mechanism of formation of (Al₁₈B₄O₃₃) and Al₄B₂O₉) whisker phases which have refractory properties and corrosion resistance [1] [12] [13] .

2. Experimental

2.1. Samples Preparation

Glass of composition B₂O₃-SiO₂-Al₂O₃-CdO was prepared using a melt-annealed route. Mixtures of analytical grade SiO₂ (Prince Minerals Ltd., UK), H₃BO₃, Al₂O₃ and CdO (all Sigma-Aldrich) were melted in an aluminum crucible for 1 h at 1420˚C in an electric furnace. After melting, the liquid was rapidly poured between stainless steel plates and directly annealed at 400˚C to enhance the crystallization process. The as obtained samples were obtained in an amorphous state as confirmed by powder X-ray diffraction experiments. Heat treatment was applied on the as-obtained glass using a heating and cooling rate of 5˚C/min. The temperature was hold at fixed values (950˚C, 1000˚C and 1100˚C) for a fixed time for 8 hours.

2.2. Measurements

XRD diffraction patterns were carried out on aBrucker Axs-D8 spectrometer. Emitting source of type (λCuKα) has been utilized. The numerical data was steeply accumulated with a small scanning step, 2θ rang of 5˚ - 70˚ and a dwell time of 0.4 seconds have been applied. The obtained X-ray diffraction spectra were revised to reference samples related to standards which were gathered by the technique of powder diffraction and standards (JCDPS).

Transmission Electron Microscopy (TEM) is a common technique used to assess the shape, size, and morphology of the bulk of the material. TEM were performed on a JEOL-JEM-2100 (Mansoura University), with an electron acceleration voltage of 200 kV. During this technique, a high energy beam of electrons is transmitted through a very thin specimen, causing interactions between the electrons and the atoms and producing the TEM images. The surface structure of samples was characterized using JEOL JSM-6510 LV electron microscope operated at accelerating voltage 30 KV, with a magnification 10× up to 400.000×. For the SEM study, the samples were coated with gold to prevent scattering of the electron beam. Hardness was obtained from a HV-1000B Vickers microhardness tester with a load of 300 g on a mirror finish surface.

3. Results

Figure 1 shows DSC curve for the as prepared sample. The crystalline temperature is evaluated to be around 940˚C. Exothermic peaks corresponding to crystallization process are dependent on the route of thermal heat treatment. Figure 2 represents XRD spectra of both as prepared and thermally treated glasses. The network structure of the as prepared glass was confirmed to be amorphous. This is can be evidenced by appearing of a broad X-ray diffraction pattern characterizing the amorphous state of the glass as is shown in Figure 2(a). The amorphous nature of as prepared sample is further confirmed by electron diffraction patterns (EDP), Figure 4(c), since there is no any diffraction due to crystalline species could be observed. Treating the glass thermally leads to formation of some types of crystalline species as is evidenced from Figures 2(b)-(d) and Figure 4(d). In this regard, some sharp diffractions are simply appeared. This leads that the applied temperature plays the role of transformation of amorphous phase into more ordered crystalline ones.

The present glass is treated thermally at higher temperature than that of crystalline one. Thermal heat treatment temperature is therefore ≥950˚C which may the proper temperatures valuable for transformation of the amorphous structure into crystalline one as is evidenced from DSC curve (Figure 1) and both XRD and EDP (Figures 2(b)-(d) and Figure 4(d)). The will formed crystalline phases are indexed to some specific type of whisker phase [1] [2] [3] [8] [10] which are distributed in the residual glass matrix.

The morphology of as prepared sample was studied by Scanning Electron Microscopy (SEM) and TEM (Figure 3 and Figure 4). The photograph of base glass is shown by Figure 3(a) which shows a homogenous morphology of the glass network. Noteworthy, heating the base glass at a specific temperature for fixed time of treating successfully led to the formation of crystalline nano-fibrous or whiskers bundles (Figure 3(b) and Figure 3(c)). Treatments at the higher temperature for the same time can simply form co-aligned and elongated nanodifused species (Figure 3(d)). The formed nano rods may contain Al₄B₂O₉ and Al1₈B₄O₃₃ nano-crystals which are considered to be useful for using the materials in the field of tissue engineering and bio scaffolds applications.

Table 1 presents the relation between the micro hardness number and tempering temperature of heat treatment. There is a significant change in the hardness number with the effect of increasing temperature of treatment. H_v is increased gradually and the values were 350 Kg/mm² for as prepared glass, 396 Kg/mm² for glass treating at 1000˚C and 485 Kg/mm² for sample heat treated at 1100˚C, respectively. The as obtained glass has a lower number of hardness. In addition, the crack length and distortion due to indentation process at the corner of diamond pyramid was also observed to be lowered by increasing treating temperature (Table 1). This may lead that the microstructure of high hardness number and lower crack length can resist crack propagation in solid materials.

3. Discussion

3.1. XRD Analysis

Several studies on oxide glasses and glass ceramics had indicated that the structure of glass network depends strongly on, morphology and crystallinity relationships [1] [14] [15] [16] . To control formation of some specific types of crystalline species, employment of sensitive and specific technique has to be required. The applied method of thermal heat treatment (THT) is considered between the most suitable routes. The THT may be applied to obtain morphology with certain desired crystalline phases characterized glass ceramics. Figure 2 presents XRD patterns of crystallized glass samples treated at different temperature (950˚C, 1000˚C and 1100˚C) for fixed time interval (8 hrs). Peaks at 2θ = 16.5˚C and 21˚C appeared in XRD curve are assigned to the semi-crystalline Al₄B₂O₉. At the same time, some new peaks were appeared at 1000˚C and 1100˚C. Then XRD curves at 1000˚C and 1100˚C showed predominating crystalline species of Al₄B₂O₉ in addition to growth of some traces of Al₁₈B₄O₃₃ [16] [17] . However the intensity of peaks increased with increasing treating temperature from 950˚C to 1100˚C. Formation of whisker crystals at temperature 950˚C and 1000˚C can be correlated with Al₄B₂O₉ phase according to XRD data as shown in Figure 2(b) and Figure 2(c). Increasing crystallization temperature led to an enhanced growth of the crystals, since both Al₄B₂O₉ and Al₁₈B₄O₃₃ [11] [16] [17] could be identified by XRD patterns of glass treated at 1100˚C (Figure 2(d)). Presence of the same crystalline species is also documented in aluminum borate glasses treated at lower temperature [11] . The formation of aluminum borates (Al₁₈B₄O₃₃ and Al₄B₂O₉) from alumina and boron oxide occurs between 600˚C and 800˚C in aluminum borate glasses [11] . But in the present investigated aluminum borosilicate glasses these phases are obtained at more higher temperature 1000˚C and 1100˚C. Thermal treating technique is the most recommended to obtain morphologies with a better crystallinity as is evidenced from Figure 2(d) and Figure 3(b). These characteristics become essential to improve the structure of the used materials.

3.2. Morphological Studies (SEM and TEM) Microscopy

The morphology and bulk structure of as prepared glass were characterized by

scanning and transmission electron microscopy (SEM and TEM). The micrograph of base glass is presented by Figure 3(a) and Figure 4(a) which show nearly homogenous glass network. Noteworthy, treating of the amorphous borosilicate glass at a specific temperature for fixed time of treating successfully led to the formation of crystalline alumina-borate nano-fibrous or whiskers bundles (Figure 3(b) and Figure 4(b)). Treatments at higher temperature for the same time can simply form co-aligned and elongated nanodifused species (Figure 3(c)) which is transformed to more aligned thicker elongated and diffused nono-fibers or whiskers (Figure 3(d)). The well formed fibers are characterized with 15 - 20 nm thick and up to ca. 40 μm long. The formed nanofibers consisted of Al₄B₂O₉ and Al₁₈B₄O₃₃ nano-crystals, with the better-elongated shapes which are considered to be useful for using the materials in the field of tissue engineering or bio scaffolds applications.

As important advantage, this treated glass ceramics can be performed under relatively mild conditions (applied THT at 1000˚C and 1100˚C for 8 hrs). Such conditions, are often necessary to obtain high aspect ratio of elongated Al₄B₂O₉ and Al₁₈B₄O₃₃ nanofibers [18] [19] [20] , and they have been also successfully employed as templates in the transcription of nanofibrous inorganic materials and hybrid biomaterials [21] . SEM showed that the size of the well-formed crystalline species is varied with increasing heat treatment temperature. Smaller

crystals were found in samples heat treated at lower temperature. It is also reflected from the electron diffraction pattern (EDP) that the structure of the sample treated at 1000˚C is more oriented and ordered than that of as obtained glass, see Figure 4(c) and Figure 4(d). Finally, heat treatment at extra higher temperature 1100˚C resulted in partially melting of some hollow aluminumborate rods and a change in crystal morphology, see Figure 3(d). Therefore, 1000˚C is considered the suitable temperature for heat treatment process.

3.3. Microhardness Investigation

Table 1 presents the relation between the micro hardness number and tempering temperature of heat treatment. There is a significant change in the hardness number with the effect of increasing temperature of treatment. Hv is increased gradually and the values were 350 for as prepared glass, 396 for glass treating at 1000˚C and 485 Kg/mm² for sample heat treated at 1100˚C, respectively. The as obtained glass has lower number of hardness. In addition, the crack length and distortion due to indentation process at the corner of diamond pyramid was also observed to be lowered by increasing treating temperature. This may lead that the microstructure of high hardness number and lower crack length can resist crack propagation in solid materials [22] [23] .

4. Conclusion

The formation of aluminum borates (Al₁₈B₄O₃₃ and Al₄B₂O₉) crystalline phases in borosilicate glass ceramics occur between 1000˚C and 1100˚C. There is a development in microstructure and properties upon thermal heat treatment. The differential thermal analysis was carried out to evaluate the limit of the sintering process. Then the degree of crystal formation was confirmed by X-ray and electron diffraction. Finally, the developed microstructures were characterized by scanning and transmission electron microscopy. The obtained results have confirmed that Al₁₈B₄O₃₃ is the main crystalline phase. Needle grains like shape were dominant crystal type. The various heat treatment temperatures mainly influenced the content of (Al1₈B₄O₃₃ and Al₄B₂O₉) crystalline species in the glass-ceramic. Glass-ceramic treated at 1100˚C presented the highest crystallinity and hardness number and lowest crack length. SEM and TEM showed that a large number of whisker crystalline phases together with the glassy phases were evenly distributed in the network of glass ceramic treated at 1000˚C and 1100˚C. The results indicated that thermal heat treatment process creates more crystalline species of more chemical bonds which acted as a vital part in improving the holding power for the bonding of glass-ceramic bonds and increasing the glass hardness and reducing the crack concentrations.

Conflicts of Interest

The author declares no conflicts of interest regarding the publication of this paper.

Cite this paper

Behairy, A. (2019) Characteristic Studies on Whisker-Reinforced Borosilicate Glasses. New Journal of Glass and Ceramics, 9, 15-24. https://doi.org/10.4236/njgc.2019.92002

References