Influence of hydrothermal conditions on the phase composition of materials from the system MgO-Al2O3-SiO2-H2O


This work directly links the performance with the phase evolution in the MgO-Al2O3-SiO2-H2O system during the hydrothermal treatment. Cement-free refractory binders, considered as alternative to calcium aluminate cements, with the chemical compositions fine-grained mixtures of MgO-Al2O3, MgO-Al2O3-SiO2, and MgO-SiO2 reactive powders were subjected conversion from dry mixture to hydrated matrix at ca. 240 °C under autogenous water vapor pressure for 56 h. The main purpose of this approach is to simulate the thermal behavior of the hydrated castable matrix belonging to the MgO-Al2O3-H2O, MgO-Al2O3-SiO2-H2O, and MgO-SiO2-H2O systems when exposed to heat treatment of large-format precast monolithic refractories. The phase compositions of the hydrated samples were determined by X-ray diffraction (XRD) technique using CuKα radiation. The FT-IR scans were used to evaluate the functional groups of the hydrated materials. Thermal decomposition mechanism and microstructure were examined by coupled DSC-TG-EGA (MS) and SEM-EDS, respectively. It is shown through presented results that boehmite (AlO(OH)), brucite (Mg(OH)2), and magnesium- and aluminum-layered double hydroxide-like phase ([Mg6Al2(OH)18 4.5H2O]) were formed via hydrothermal synthesis in the MgO-Al2O3-H2O system. Chrysotile (Mg3[Si2−xO5](OH)4−4x) was detected in the MgO-SiO2-H2O binder system as a main phase and in the MgO(rich)-Al2O3-SiO2-H2O binder system as secondary phase. For the sample with the Al2O3 excess, two magnesium aluminum silicate hydroxides ((Mg,Al)6(Si,Al)4O10(OH)8, Mg5Al2Si3O10(OH)8), together with MgAl(OH)14 xH2O, Mg(OH)2, and AlO(OH), were formed in the MgO-Al2O3(rich)-SiO2-H2O binder system. Since the type of hydrates contributed to the thermal stability of the binder matrixes, the valuable practical results concern mainly on the optimization of heat treatment process of state-of-the-art CaO-free matrixes being considered as precursors in the low-temperature synthesis of high refractory phases like spinel and forsterite.


Aluminum, magnesium, and silicon oxides are one of the main raw materials for refractory industry. Traditionally, aluminum oxide (alumina), magnesium oxide (magnesia), and silicon oxide (silica) are used in shaped refractory materials in the oxide form or as components of many refractory phases. Alumina and silica are also very popular raw materials in castables, although magnesia has also recently increased in popularity in this application as a result of the growing popularity of basic castables. Although the use of these oxides as aggregates in refractory castables is well characterized, there is still a lack of knowledge about their behavior as hydraulic binding materials during a heat treatment.

Increased interest in binding materials based on reactive oxide powders is connected with the trend towards resignation from cements, especially calcium aluminate cements which is still one of the main raw materials for refractory castables. Calcium aluminate cements consist of calcium oxide which can form low melting phases at a higher temperature [1, 2]. Calcium aluminate cement can be successfully replaced by binding materials based on reactive magnesium, aluminum, and silicon oxides in powder as well as in colloidal suspension. In the Al2O3-MgO-SiO2 system, we can obtain different binding materials depending on its chemical composition. Those materials, based on several hydraulic phases like M-S-H phase, M-A-S-H phase (M = MgO, A = Al2O3, S=SiO2, H=H2O), brucite, double magnesium aluminum hydroxide, and gibbsite, can be successfully utilized in many kinds of castables [3,4,5]. These phases can play a meaningful role in synthesis of spinel and forsterite on early stage of firing process and facilitate formation of ceramic bond [6].

There are many works on the behavior of binding materials based on the reactive oxides MgO, Al2O3, and SiO2 in reaction with water but the influence of water vapor pressure on changes that take place during a heat treatment of the binding materials is not yet widely understood. This aspect is particularly important in the refractory castables based on this type of binders. The aim of this study was to evaluate the behavior of hydraulic binding materials based on mix magnesia, alumina, and silicon oxides, under elevated temperature and water vapor pressure conditions.


High-purity, reagent grade magnesium oxide powder (MgO ≥ 98% from Acros Organics), commercial reactive alumina powder (d50 ≤ 1 μm, RG 4000 from Alamtis), and microsilica (SiO2 ≥ 98% Microsilica 971 U from Elkem) were used as raw materials. Powders of the raw materials were mixed in different mass ratios and homogenized. After homogenization, the mixtures were subjected to hydrothermal synthesis at the temperature of 240 °C under autogenous water vapor pressure for 56 h. The sample compositions are presented in Table 1. The samples, obtained after a hydrothermal treatment, were washed several times with cold acetone to remove the free water and then examined. The samples were examined by thermal analysis DSC-TGA-EGA in the range from 20 up to 1000 °C (Netzsch STA 449 F5 with QMS 403D), XRD analysis carried out in range 5–90° 2θ (Philips PanalyticalX’Pert-Pro), FTIR analysis performed in MIR range (Brucker 70 V), and SEM-EDS analysis (Nova Nano SEM 200 Fei with EDAX EDS analyzer).

Table 1 Samples composition

Results and discussion

According to XRD analysis shown in Fig. 1 and summarized in Table 2, the phase composition is quite varied. The results of the analyses of samples after a hydrothermal treatment indicate the presence of different kinds of hydroxides and oxide hydroxide. In each sample, XRD analysis shows brucite in different amounts depending on the sample’s chemical composition. In the case of samples with the presence of SiO2 (samples 12, 13, 15), phases from serpentine group (chrysotile) as well as mixed chlorite-serpentine group (with some substitutions of aluminum) can be identified. In sample 13, the evidence of presence of the MSH phase, three wide effects in range 2θ = 15–30°, 2θ = 35–39°, 2θ = 58–62° can also be observed [7]. In samples 13 and 15, MgO can be identified. The presence of MgO is unexpected but can be connected with the anti-hydration properties of microsilica.

Fig. 1

XRD analysis of studied samples

Table 2 Phase composition of the studied samples

The XRD patterns of the samples with Al2O3 (samples 11, 12, 15) reveal boehmite but there was no evidence of the gibbsite presence, although it would be an expected phase in reaction of Al2O3 with water under atmospheric pressure [8]. In the place of gibbsite, magnesium aluminum hydroxide hydrate can be identified but its amount is rather low in respect to boehmite. The absence of gibbsite may indicate that during the hydrothermal treatment of the studied binders (e.g., inside castables), boehmite rather than gibbsite is formed. Gibbsite that has already been created probably transforms into boehmite or reacts with brucite to form double hydroxide, a new compound with a layered character. This would generally be positive in regard to application of these binders in the refractory castables, due to the less-hydrated character of this phases and elongated time of water evacuation from the material.

In the presence of carbon dioxide, double hydroxide magnesium and aluminum can probably form hydrotalcite-like minerals [9] but on XRD spectra in studied samples there was no evidence of such a reaction although it should be emphasized that hydrotalcite produces a similar XRD spectrum to double magnesium-aluminum hydroxide.

These findings were confirmed by a thermal analysis. As it is shown on the thermal curves in Fig. 2, different kinds of water occur in all samples, and it is also confirmed by the IR spectra. Water released in the endothermic effect in the temperature range around 100–150 °C can be connected with free water but in this range, zeolitic water can also be released [9, 10]. The amount of released water in this range slightly exceeds 2%. At around 200 °C, an endothermic effect occurs probably related to the decomposition of magnesium aluminum hydroxide hydrate (except sample 13) [10]. At a temperature of around 400 °C, the decomposition of brucite follows, connected (in the sample with SiO2) with the decomposition of less thermally stable part of the MSH phase [6, 10]. At the temperature of around 550 °C, boehmite is decomposed as well [11].

Fig. 2

Thermal analysis of studied samples

The MSH phase present in sample 13 is connected with minerals from serpentine group, which can be treated as a product of transformation of the MSH phase in hydrothermal conditions. Decomposition of the layer structure of serpentine minerals (sample 13) as well as serpentine-chlorite minerals (samples 12, 15) is connected with the endothermic effect at around 600 °C. At a higher temperature, for sample 13, we can also observe an exothermic effect at a temperature of around 840 °C, connected with the synthesis of magnesium silicate probably forsterite [6, 12]. The mass changes in the temperature range, connected with the corresponding thermal effects, are presented in Table 3.

Table 3 Mass losses of the samples

Worthy of notice is the influence of SiO2 on hydration of aluminum oxide observed (Fig. 2, Table 3) on thermogravimetric curves for samples 11, 12, and 15. As it can be seen, the addition of SiO2 decreases the amount of double magnesium aluminum hydroxide and boehmite. This effect can be connected with anti-hydration properties of microsilica. Microsilica reacts with MgO creating the MSH phase which binds a part of the MgO and protects the rest of the magnesium oxide grains against further hydration. This process decreases the pH and probably influences the dissolution of Al2O3 as well as the amount of MgO that could form double hydroxide. It could be assumed that the increase in the amount of MgO in the sample should increase the hydration rate of Al2O3 while the increase in content of amorphous silica will decrease it.

The spectra of FTIR spectroscopy in Fig. 3 reveal several band characteristics for hydrated phases. In each sample, a sharp band of around 3700 cm−1 indicates the presence of brucite [13]. This finding is in good agreement with the thermal analysis results as well as with the results of XRD analysis. Moreover, a complex band above 3000 cm−1 can be connected with different kinds of water and vibration of M-OH (M-metal ion) [14]. The bands around 3200–3250 cm−1 as well as 3400–3450 cm−1 are often assigned to non-structural water vibration [15, 16], although in the range around 3450 cm−1 according to [10] also the stretching vibrations of the -OH groups attached to Mg and Al ions are located. The presence of non-structural water also indicates bands in the region 1600–1700 cm−1 [7, 10]. Bands in the range 700–1200 cm−1 can be connected with the tetrahedral layer vibration of Si(Al)-O-Si(Al), Si(Al)-O groups [15, 17]. The vibration around 1222 cm−1 in sample 13 is assigned to Si-O vibration in phyllosilicates (serpentine, MSH phase) [7].

Fig. 3

FTIR analysis of studied samples

Bands around 400–650 cm−1 can be assigned to the vibrations of M-O and M-OH in octahedral metal layer and the vibration of tetrahedral silica layer. In samples 11, 12, and 15, bands in the range 400–700 cm−1 can be associated with the Al2O3 and AlO(OH) vibrations, while in sample 13, bands in this range are assigned to the vibration of Mg-O and Si-O, and the vibrations of oxides bridges between tetrahedral and octahedral layers in magnesium silicates hydrates [10, 18].

An interesting aspect of the studied materials is the presence of carbon dioxide especially in the samples containing Al2O3. FTIR analysis shows the presence of CO32− groups of around 1400 to 1500 cm−1 [15]. A sharp band around 1350 cm−1 indicates the presence of hydrotalcite-like compounds. To this compound, also bands around 1012 cm−1, 783 cm−1, and 683 cm−1 can be assigned [10, 19]. Although the hydrothermal treatment was carried out without the access of carbon dioxide, the presence of it even in a minor amount can be decisive in terms of structure and properties of the new formed phases. This aspect of the studied materials needs further investigations.

The micrographs presented in Figs. 4, 5, 6, 7, 8 show the results of SEM-EDS analysis of the studied samples. The microstructure of the samples is varied depending on chemical composition. Sample 15 (Figs. 4 and 5) exhibits granular-shaped grains and homogeneous microstructure. According to EDS analysis, its chemical composition is varied, larger aggregates are composed mainly of Al2O3 with admixture of MgO and SiO2 (Fig. 4b, c) while smaller aggregates are richer in MgO (Fig. 5b, c). The SEM-EDS analysis of sample 13 (Fig. 6) reveals thin needle-like shaped crystals rich in Mg, probably Mg(OH)2, surrounded by compacted rounded grains of the hydraulic phases composed of SiO2 and MgO. Samples 11 (Fig. 7) and 12 (Fig. 8), with higher amount of MgO and Al2O3, have different microstructure from the previous samples. The SEM micrograph in Fig. 7a shows that two types of plate-like structures were formed as the major products of the hydrothermal treatment of sample 11. The big plate Al-rich crystals and thin Mg, Al-rich hexagonal plates were formed. The microanalysis of these smaller structures indicates the presence of the double magnesium and aluminum hydroxide (Fig. 7c). Similar morphology to sample 11 presents sample 12 (Fig. 8). Its microstructure is dominated by small plate structure, probably belonging to brucite crystals, as a main phase with some amount of Al which can suggest also presence of double magnesium and aluminum hydroxide as a secondary phase.

Fig. 4

SEM-EDS analysis of sample 15—larger aggregates richer in Al. a Microstructure of the sample. b, c EDS spectra of the sample in the microarea 1 and 2 respectively

Fig. 5

SEM-EDS analysis of sample 15—smaller aggregates richer in Mg. a Microstructure of the sample. b, c EDS spectra of the sample in the microarea 1 and 2 respectively

Fig. 6

SEM-EDS analysis of the sample 13. a Microstructure of the sample. bd EDS spectra of the sample in the microarea 1, 2, and 3 respectively

Fig. 7

SEM-EDS analysis of the sample 11. a Microstructure of the sample. b, c EDS spectra of the sample in the microarea 1 and 2 respectively

Fig. 8

SEM-EDS analysis of the sample 12. a Microstructure of the sample. b, c EDS spectra of the sample in the microarea 1 and 2 respectively

Summary and conclusions

This work explains the reactivity of the binary MgO-Al2O3 and MgO-SiO2, and ternary MgO(rich)-Al2O3-SiO2 and MgO-Al2O3(rich)-SiO2 mixtures of reactive powders subjected to the hydrothermal treatment. The main goal of this approach is to simulate the thermal behavior of the hydrated cement-free pastes when exposed to heat treatment of large-format precast monolithic refractories. Structure, phase composition, microstructure, and thermal stability of the hydrated materials were investigated by FT-IR, XRD, SEM-EDS, and DSC-TG-EGA(MS) techniques, respectively. From the presented results, it was found that MgO affects the hydration behavior of Al2O3 and SiO2. Boehmite (AlO(OH)), brucite (Mg(OH)2), and magnesium- and aluminum-layered double hydroxide-like phase ([Mg6Al2(OH)18 4.5H2O]) were formed via hydrothermal synthesis in the MgO-Al2O3-H2O system, whereas Mg(OH)2 and magnesium silicate hydroxide (chrysotile) Mg3[Si2−xO5](OH)4−4x were detected in the MgO-SiO2-H2O system. Chrysotile (Mg3[Si2−xO5](OH)4−4x) together with boehmite, brucite, and magnesium aluminum hydroxide hydrate [Mg6Al2(OH)18 4.5H2O] was formed in the MgO(rich)-Al2O3-SiO2-H2O binder system. In the system with the Al2O3 excess, two magnesium aluminum silicate hydroxides ((Mg,Al)6(Si,Al)4O10(OH)8, Mg5Al2Si3O10(OH)8), together with MgAl(OH)14 xH2O, Mg(OH)2, and AlO(OH), were found in the MgO-Al2O3(rich)-SiO2-H2O binder system. The binding materials from the MgO-Al2O3-SiO2-H2O phase system are versatile binders in a wide range of the castables. Depending on the chemical compositions, they can be utilized in basic, chamotte, and alumina castables; moreover, thanks to the elimination of cements containing CaO, the new kinds of binders do not reduce the properties of the refractory materials. Considering the results of the performed analysis, it can be stated that during the hydrothermal treatment in the presence of MgO, most the aluminum oxide transforms into boehmite and magnesium aluminum hydroxide hydrate. Moreover phases like double magnesium and aluminum hydroxide and M-S-H phase act as precursors of compounds like forsterite and spinel, decreasing their synthesis temperature. Faster synthesis of these compounds facilitates also formation of the ceramic bond in the castables. The creation of boehmite instead of gibbsite is another positive factor during the heat treatment of the materials based of this kind of binders, due to the elongated water release. Elongation of water release from the castables decreases internal pressure inside the heated material and prevents it against cracks and defects. Base on this study, it can also be noticed that even small changes in the composition can lead to a fundamental change in the properties of these materials. This is applied especially to aluminum oxide hydration and decided upon phase composition of the studied materials.


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This study was founded by The National Centre for Research and Development within the framework of LIDER VIII project No. LIDER/5/0034/L-8/16/NCBR/2017.

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1. Phases from MgO-Al2O3-SiO2 phase system are very promising binders in refractory materials.

2. Hydrothermal treatment approximate conditions during heat treatment of the refractory castables.

3. During the process boehmite and double aluminium magnesium hydroxide is creating.

4. The factor which decided about reactivity of aluminium and silica oxides in studied conditions is probably content of magnesium oxide, which influence on pH of the samples.

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Prorok, R., Madej, D. Influence of hydrothermal conditions on the phase composition of materials from the system MgO-Al2O3-SiO2-H2O. J Aust Ceram Soc 56, 829–837 (2020).

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  • Binding materials
  • Hydrothermal treatment
  • Reactive oxides
  • Refractory materials