Effect of Water Content and MgO / ADP Ratio on the Properties of Magnesium Phosphate Cement

Abstract

Materials such as magnesium phosphate cement (MPC) have attracted significant attention of researchers, therefore, understanding the effects of dosage parameters, such as water content and MgO/NH₄H₂PO₄ ratio on phase formation is essential for obtaining cementitious matrices with improved performance. In the present work MgO was sintered at 900 °C and 1110 °C in a conventional oven, and the effect of water concentration and MgO/NH₄H₂PO₄ (or ADP) ratio on the properties of MPC was evaluated in terms of phase formation by X-ray diffraction, pore size distribution, mechanical properties, and microstructure. For less-reactive MgO (calcined at 1100 °C) with a high MgO/ADP ratio, increased water content did not cause additional solubilization of ADP or formation of more hydrated phases, although the cement porosity increased. Compositions with more reactive MgO (calcined up to 900 °C) formed dittmarite (NH₄MgPO₄.H₂O) independent of water content. Higher water content and MgO calcination temperature were associated with increased MPC setting time and decreased mechanical strength due to higher porosity.

Keywords:
magnesium phosphate cements; sintering; water content; microstructure; properties

1. Introduction

Sintering of ceramic materials is an important research topic, although this process entails significant energy consumption and cost when implemented at a large scale. The energy demand and the resource consumption are some of the environmental issues that have generated a major interest in the modern society^1,2. Chemically bonded materials, such as ordinary Portland cement (OPC), can be used as an alternative to sintering ceramic materials. Formed by hydraulic chemical reactions, this material acquires mechanical resistance at ambient temperature, is low in cost, and is useful for applications that consume significant material.

However, there is a gap between the properties of OPC and those of sintered ceramics³. The use of reactive magnesium oxide (MgO) as a cement binder can provide some advantages over OPC due to its lower calcination temperatures (700 ºC to 1000 ºC vs. 1450 ºC)^4,5. Although sintered ceramics are more expensive than OPC, these ceramics have superior mechanical properties and are much more stable in acidic atmospheres or at elevated temperatures. Unfortunately, not all applications are entirely satisfied by either class of materials, indicating a need for other materials with intermediate properties such as chemically bonded phosphate ceramics (CBPCs), to fill this gap⁶.

CBPCs are formed by reactions between acid phosphate (such as potassium, ammonium, or aluminum) and metal oxide (such as magnesium, calcium, and zinc). These reactions form phosphoric bonds, as first discovered in the first half of the 20^th century with the emergence of dental cements (zinc phosphates). According to MA et al.², two types of MPCs are used in engineering practice and academic research; one of them uses ammonium dihydrogen phosphate (ADP), whereas the other uses potassium dihydrogen phosphate (KDP) as the phosphate component.

The refractory industry has used this knowledge to develop chemically bonded refractories, either at room temperature, or thermally induced at low temperatures⁷. Kingery⁸ analyzed the reactions of various inorganic oxides with a phosphoric acid solution. These studies concluded that amphoteric, or slightly basic cations with small ionic radii, are the most effective options for the formation of chemically bonded ceramics. These studies described the phosphoric chemical bond as having an essential inorganic character that could be achieved by the following three mechanisms: chemical reaction of a siliceous material with phosphoric acid, chemical reaction of a metal oxide with phosphoric acid, and direct addition (“in situ”) or formation of acid phosphates.

Sugama and Kukacka⁹ and Sugama¹⁰ developed cements consisting of magnesium and ammonium phosphate, as well as calcium aluminate, both utilized for the rapid repair of damaged structures. More recently, researchers have developed magnesium and potassium phosphate cements that are used for the treatment of hazardous solid waste^6,11.

The raw materials are mixed at an ambient temperature, and exothermic reactions immediately produce the ammonium and magnesium phosphate phases. These phases are hydrated and insoluble in water.

The main product of these reactions is a crystalline phase called struvite (NH₄MgPO₄.6H₂O), formed according to Equation 1 as follows:

$$MgO\left(s\right)+N{H}_4{H}_{2}P{O}_4\left(s\right)+5H_{2}O\left(l\right)\to MgN{H}_{4}P{O}_4.6H_{2}O\left(s\right)$$ (1)

Other phases, such as dittmarite (NH₄MgPO₄.H₂O), stercorite [Na(NH₄)HPO₄.4H₂O] and schertelite [(NH₄)₂MgH₂(PO₄)₂.4H₂O] are ordinarily observed during the hydration reaction; whereas hanaite [(NH₄)₂Mg₃(HPO₄)₄.8H₂O], newberyite [MgHPO₄.3H₂O], and other phosphate hydrates are found less frequently¹².

Struvite (NH₄MgPO₄.6H₂O) is thermally stable in air, although this phase loses the H₂O and NH₃ molecules from its structure and decomposes at a temperature of 55 °C, forming an amorphous phase chemically represented by MgHPO₄. This phase can be rehydrated in the presence of water and an ambient temperature, forming the original phase (struvite) and other amorphous and/or crystalline phases¹³.

According to Abdelrazig and El-Jazairi¹³, the amount of principal reactants has a significant influence on the crystalline phases that are to be formed following the reaction; these phases are directly related to the mechanical resistance to the compression of cement. The amount of the principal reactants also influences the physical characteristics of the material, such as porosity and bulk density.

Considering the volume of water added to the mixture, cements with higher water/cement (w/c) ratios have larger pore volumes, and lower compressive strengths^14,15, in agreement with the Griffith Law. Abdelrazig and El-Jazairi¹⁴ also observed changes in the geometry of struvite (NH₄MgPO₄.6H₂O) crystals with increasing amounts of water, specifically the formation of needles followed by tabular plates. The formation of needles during crystallization is known to provide adequate mechanical properties.

Ammonium dihydrogen phosphate (NH₄H₂PO₄), or ADP, reacts with magnesium oxide in the presence of water in an acid-base reaction. Recent studies^16,17 report that the amount of hydrates decrease with an increasing amount of NH₄H₂PO_4; therefore, the strength of the magnesium phosphate cement (MPC) theoretically decreases. The strength of the MgO grains is significantly larger than that of the phosphate hydrates. Therefore, the lower the amount of ADP, the higher the strength of the MPC paste; given there is a sufficient amount of phosphate hydrates surrounding the MgO grains thoroughly^16,17.

Xu et al.¹⁸ studied the reaction mechanism of the magnesium potassium phosphate cement (MKC) with a high magnesium-to-phosphate ratio and observed that this high Mg/PO₄ molar ratio suppresses the formation of potassium-free magnesium phosphate hydrates and that K-struvite is possibly formed mainly with more phosphate than the theoretical value. Furthermore, the water/solid (w/s) ratio plays a crucial role on governing the reaction path of MKP cements. MA et al.² observed when the water content is kept constant, at a magnesium-to-phosphate value equivalent to 6, the cement consists of the lowest porosity and smallest critical pore diameter, and the highest compressive strength and lowest intrinsic permeability.

Recent studies have evaluated the effect of boric acid (H₃BO₃) content¹⁹, MgO/ADP ratio²⁰, and microwave calcination of MgO^21,22 on the properties and durability²³ of MPCs. Therefore, since a consolidated dosage method for MPCs has not been reported yet, this study aims to evaluate the influence of water content and MgO/ADP ratio on the properties of MPC using MgO calcined at different temperatures, formation reactions (setting time and phases formed), microstructure, porosity, and mechanical strength of these materials.

2. Materials and Methods

2.1 Materials

The materials used were raw materials with commercial purity, although raw materials with a high purity were used when necessary to assist in the analysis of phase formation. The primary materials used were MgO, ADP (NH₄H₂PO₄), and H₃BO₃ (setting time retarder).

2.1.1 Magnesium oxide

MgO (basic component) needed to be calcined due to its high surface area. MgO was calcined using a Termolab BL 260/03 oven, with a heating rate of 10 °C/min.

Rezaei et al.²⁴ calcined MgO at 700 °C for 2 h, yielding unsatisfactory results. Sonat el al.²⁵. calcined the MgO at temperatures between 700 °C and 1100 °C, and found that the calcination temperature had a significant effect on the strength values for shorter residence times (2 h), whereas the strength of samples subjected to 6 h of calcination did not change significantly between the temperature range of 700 ºC to 900 ºC. In this study, two distinct temperatures of 900 ºC and 1100 °C were selected, and the dwell time was fixed to 2 h.

The original MgO provided by Buschle & Lepper S.A. had a specific surface area of 46.02 m²/g, unitary mass of 1.34 kg/dm³, and specific gravity of 2.79 kg/dm³.

2.1.2 Ammonium dihydrogen phosphate

Ammonium dihydrogen phosphate (NH₄H₂PO₄), or ADP, reacts with MgO in the presence of water in an acid-base reaction. The ADP used, provided by LabSynth, had a surface area of 0.68 m²/g, unitary mass of 0.79 kg/dm³, and specific gravity of 1.87 kg/dm³.

2.1.3 Boric acid

Retardants increased the setting time and decreased the intensity of the exothermic reaction during the initial setting and hardening stage by delaying the setting time of reactions, improving the working conditions, and providing the necessary time required for the reactions to complete, thereby effectively forming phosphates²⁶. Therefore, chemical retardants are utilized in large-scale mixing operations. Commercial H₃BO₃ (provide by LabSynth) containing approximately 98% H₃BO₃ was used.

2.2 Methods

2.2.1 Material characterization

The materials were characterized by X-ray diffractometry (XRD) (Rigaku Geigerflex ME 210GF2 Diffractometer, configured with CuKα radiation, 40 kV of voltage, 100 mA of current, 10°–80° 2θ scanning, and 4°/min of scanning speed), X-ray fluorescence (XRF - Philips PW1480 X-ray Fluorescence Spectrometer), Fourier transform infrared spectroscopy (Bruker Tensor 27 FTIR spectrometer, wavenumber range of 4000 to 450 cm⁻¹), and scanning electron microscopy (Philips SEM, model XL 30 FEG, gold coating) to evaluate the phase and chemical compositions. Before performing XRD, XRF and FTIR tests, the samples were ground to a grain size of less than 75 μm.

Relevant physical parameters such as the particle size distribution (Horiba sedentary model CP5000), mercury porosimetry (Porosizer 9320, Micromeritics), specific surface area estimated by BET (using a Micrometrics Gemini 2370 V1.02 equipment), and specific gravity (Helium Pycnometer Accupyc 1330 V2.01 from Micrometrics) were determined.

2.2.2 Dosage and molding of specimens

Two cement compositions were prepared following the calcination of MgO. Each of these compositions had different mass proportions of MgO/NH₄H₂PO₄ and water contents (40% to 80%), as shown in Table 1.

Table 1
Compositions used to evaluate the effect of the water and ADP (NH₄H₂PO₄) contents in magnesium phosphate cement compositions.

Composition *	MgO	ADP	MgO/ADP	H2O	Boric
	(%, in mass)	(%, in mass)	Ratio	(%, in mass) **	Acid (%) ***
C_01 - 40% H2O	70	30	2.33	40	15
C_01 - 50% H2O				50
C_01 - 60% H2O				60
C_01 - 70% H2O				70
C_01 - 80% H2O				80
C_04 - 40% H2O	55	45	1.22	40	15
C_04 - 50% H2O				50
C_04 - 60% H2O				60
C_04 - 70% H2O				70
C_04 - 80% H2O				80

• ^*
  Stoichiometric composition for the formation of 100% struvite (NH₄MgPO₄.6H₂O) is composed by 26% and 74% ADP, in mass.
• ^**
  % relative to the mass of MgO + NH₄H₂PO₄
• ^***
  % in relation to the mass of MgO (calcined at 900 ºC / 2 h and 1100 ºC / 2 h)

The amount of retardant (H₃BO₃) added was 15% of the total mass of MgO, based on the studies of Yang and Wu²⁷. Since these compositions had different concentrations of MgO, the amount of retardant varied for each composition.

Test specimens were molded by mixing three base materials, i.e., MgO, NH₄H₂PO₄, and H₃BO₃, in different proportions with water at room temperature for 1 min. From this mixture, cubic specimens with dimensions of 3 × 3 × 3 cm³ were molded using a vibratory table, except for the specimens used for the measurement of mechanical strength, which were molded into cylindrical molds (φ 25 mm × 50 mm). The cubic specimens were used to extract pieces and evaluate the phases formation (XRD, FTIR), the morphology (SEM) and pore size distribution (MIP) of MPC compositions.

2.2.3 Composition characterization

To characterize the compositions, indirect measurements of the setting time were performed as proposed by Hall and Stevens²⁶. In addition, the compositions were characterized by X-ray diffractometry (XRD), FTIR, scanning electron microscopy (SEM), mechanical strength testing, and mercury intrusion porosimetry (MIP).

According to the Brazilian standard NBR NM 65:2003 (“Portland Cement - Determination of Setting Time), measurement of the setting time should be performed using the Vicat apparatus. However, recent studies^{3,11,19-23,26,28-30} have shown that the setting time for magnesium phosphate cements can be indirectly determined by calorimetry assays. These authors observed a direct relationship between the results obtained by calorimetric measurements and using the Vicat apparatus. Since the formation of the hydrated phases in cements is an exothermic reaction, the temperature measurements during hardening results in indirect data that can provide comparative values of setting time. In this study, a Raytec MT infrared pyrometer was used to perform such measurements at random time intervals until a reduction in the mixture temperature could be verified.

The phases of the cement were identified by XRD in experiments using the Rigaku Geigerflex ME 210GF2 diffractometer, copper targets of 40 kV and 40 mA, and a monochromatic graphite filter system. A diffraction spectrum was obtained in the range of 2θ 5°–75° at 2°/min. The phases in the samples were identified using the DIFFRAC plus-EVA software; its database follows the Joint Committee on Power Diffraction Standards (JCPDS) system.

The values of axial compression correspond to the average of 5 values for each magnesium phosphate composition that was obtained 28 days after molding, using an Instron 5500R universal testing machine, and a displacement rate of 1.5 mm/min. Values that differed by more than 5% from the average were not considered, and substituted for the results of new samples.

3. Results and Discussion

3.1 Material characterization

The chemical compositions of MgO, ADP, and H₃BO₃ are shown in Table 2.

Table 2
Chemical compositions of magnesium oxide (MgO), ammonium dihydrogen monophosphate (NH₄H₂PO₄, ADP) and boric acid (H₃BO₃), estimated by XRF (oxides).

Component	Material
(Oxide)	MgO	ADP	H3BO3
MgO (%)	78.19	---	---
SiO2 (%)	0.52	---	---
Fe2O3 (%)	0.13	---	---
CaO (%)	1.18	---	---
Al2O3 (%)	0.30	---	---
MnO (%)	0.02	---	---
P2O5 (%)	0.02	60.67	---
Na2O (%)	< 0.01	---	---
K2O (%)	< 0.01	---	---
TiO2 (%)	0.04	---	---
B2O3 (%)	---	---	56.4
LOI a (%)	19.61	---	---

• ^a
  LOI = loss on ignition

The chemical purity of MgO provided by the manufacturer was 96.28%, which was close to the experimental value, 97.26%. The significant loss on ignition (LOI) could be indicative of both, the high concentration of MgO in the form of MgCO₃ or Mg(OH)₂, as well as the large amount of water adsorbed on the MgO particles.

Figure 1 shows the X-ray diffractograms of MgO powders in two conditions: precipitated, and after different calcination temperatures (900 ºC and 1100 ºC, for 2 h).

Figure 1
X-ray diffractograms of MgO powders in two conditions: precipitated and after calcination at different temperatures (900 ºC and 1100 ºC, for 2 h).

Figure 1 shows that as the calcination temperature is increased, the diffraction peaks have smaller widths and larger intensities. According to Kingery and Francois³¹, this observation is directly related to the average crystallite size of the particles of the powder in question. Thus, the calcined powder at 1100 °C/2 h had a larger crystallite size and greater crystallinity than others. Furthermore, no secondary phases such as magnesium carbonates or hydroxides were present in these diffractograms; they may be present at levels below the equipment detection capacity, or in less crystalline forms. Thus, significant LOI in these MgO powders was associated with the presence of large amounts of adsorbed water on the particles in the powders.

Figure 2 shows the morphology obtained by SEM for the investigated MgO powders. As expected, higher calcination temperatures led to an increase in the mean particle size. Unlike calcined powders, which have well defined spherical surfaces, powders without calcination (precipitates) present irregular surfaces. This irregularity and relatively small size is responsible for the high surface area and adsorption of large amounts of water on the surface of these powders.

Figure 2
Morphology obtained by SEM of MgO (A) without calcination, (B) calcined at 900 ºC for 2 h, and (C) calcined at 1100 ºC for 2 h.

Figure 3 shows the particle size distribution of the tested MgO powders. These results are in agreement with the expected results; an increase in the mean particle size due to a higher calcination temperature was observed, according to Figure 2. However, by comparing Figures 2 and 3, the agglomerates present in these powders were not adequately dispersed (Figure 2A) despite the powders being passed through a 200-mesh screen followed by the subjection to ultrasonic dispersion for three minutes. As shown in Figures 2B and 2C, it is possible to observe the aggregated particles as a consequence of the sintering process. This result occurred because the average particle size in Figure 2 was much lower than that observed in Figure 3, especially for precipitated powders and those calcined at 900 °C.

Figure 3
Particle size distribution of precipitated (non-calcined) MgO powders and those calcined at 900 ºC and 1100 ºC for 2 h.

The precipitated powder (without calcination) and MgO sample calcined at 900 °C / 2 h and 1100 °C / 2 h had a bimodal and monomodal particle size distribution, respectively. This occurred due to the high surface area of the precipitated powders for powders calcined at 900 ºC/2 h, which easily formed a few large agglomerates in addition to the existing aggregates. For powders calcined at 1100 ºC/2 h, the monomodal particle size distribution probably represented hard agglomerates (aggregates), resulting from presintering, as observed in the microscopic analysis (Figure 2C).

Table 3 shows the densities and specific surface areas of MgO powders precipitated and calcined at different temperatures.

Table 3
Density and specific surface area of MgO powders precipitated and sinterized at different temperatures

MgO Powder	Density (g/cm3)	Specific Surface Area BET (m2/g)
Precipitated	2.79	46.02
(without sinterization)
Sinterized at 900 ºC / 2 h	3.34	24.68
Sinterized at 1100 ºC / 2 h	3.53	7.87

There was a gradual increase in the density and decrease in the surface area of calcined MgO powders, as the calcination temperature increased with density approaching the theoretical value of 3.58 g/cm^{3 24}. It was also observed that an increase in the calcination temperature led to a decrease in the specific surface area values and consequently, high reactivity of noncalcined (precipitated) powders. A decrease in the surface area values with an increase in the calcination temperature was indicative of the increased average particle size and/or agglomeration, reducing its reactivity.

Thus, the MgO powder calcined at 1100 °C / 2 h had lower solubility than that calcined at 900 °C / 2 h, due to a higher average particle size (lower specific surface area) and crystallinity.

3.2 Composition characterization

Figure 4 shows the XRD results of compositions C_01 and C_04 that were prepared from MgO powders calcined at 900 °C / 2 h and 1100 °C / 2 h, respectively, using different water contents and MgO/ADP ratios.

Figure 4
X-ray diffractograms of compositions C_01 and C_04 prepared from MgO powders calcined at (A and B) 900 ºC / 2 h and (C and D) 1100 ºC / 2 h, respectively, with different water contents. (Phases: + struvite; ▲ dittmarite; ○ MgO).

Compositions C_01 and C_04 (Figures 4A and 4B) were prepared with MgO calcined at 900 °C/2 h with different water contents, and had a tendency to form dittmarite (NH₄MgPO₄.H₂O), which was a result of the increased surface area of MgO calcined at 900 °C than that calcined at 1100 °C. When water adsorbed on the surface of this oxide, the water concentration was insufficient for the complete formation of struvite (NH₄MgPO₄.6H₂O) due to the short setting time of these cements.

For the compositions containing MgO calcined at 1100 °C / 2 h (Figures 4C and 4D), the water content did not modify the diffraction curves of composition C_01 (70% MgO), in contrast to the modified curves of composition C_04 (55% MgO). This behavior could be a consequence of excess water being available for the formation of hydrated phases when the concentration of MgO in the mixture was reduced. Composition C_01 had sufficient solubility due to the low amount of ADP present, even at low water concentrations of approximately 40%; in this case, all the ADP would be quickly consumed for the formation of hydrated phases. Increasing the water content would not lead to additional solubilization of ADP, nor the formation of more hydrated phases. However, this case did increase the porosity of the cement.

For composition C_04, lower percentages of water were associated with higher concentrations of dittmarite (NH₄MgPO₄.H₂O). Figure 4 suggests that when small amounts of water are available, the formation of dittmarite is greater since this phase is formed initially, requiring only one water molecule in its composition (NH₄MgPO₄.H₂O). When more water is available, the struvite phase (NH₄MgPO₄.6H₂O), which is thermally more stable but needs more water for its formation, is present in a greater proportional quantity reducing the amount of the dittmarite phase.

If water was present at low concentrations and added to formulations with a high surface area of MgO, there would be a lack of water for the total struvite formation. Under these conditions, dittmarite (NH₄MgPO₄.H₂O) formation would be the most prevalent phase since this phase has five fewer molecules of H₂O than struvite (NH₄MgPO₄.6H₂O). Dittmarite (NH₄MgPO₄.H₂O) is the dominant phase when the reaction is fast, whereas struvite (NH₄MgPO₄.6H₂O) dominates when the reaction is slow³².

To confirm this hypothesis, Figure 5 shows the infrared (IR) spectra of the C_04 compositions that were prepared with different water contents, and MgO calcined at 1100 °C.

Figure 5
FTIR spectra of magnesium phosphate cements with different water contents, containing MgO powders calcined at 1100 ºC.

Multiple peaks between 1400 and 1300 cm⁻¹ (ν₂ of the NH₄⁺ groups) are indicative of the strong presence of dittmarite (NH₄MgPO₄.H₂O) when the water content was 40%. A decrease in the band intensity at 3650 and 1660 cm^-−1 is also observable, which correspond to the stretching vibrations of the H₂O molecules (ν₁ e ν₃). Figure 5 shows that an increased amount of water led to the preferential formation of struvite (NH₄MgPO₄.6H₂O) than dittmarite (NH₄MgPO₄.H₂O). All these peaks were observed increasingly with increased ADP amount in the cement, indicative of the formation of the hydrated phases. Such behavior is in agreement with the results observed in Figure 4.

Finally, in addition to the 590 and 510 cm⁻¹ peaks associated with the angular deformation vibrations ν₂ and ν₄ of the same PO₄⁻³ groups, there is a strong band between 900 and 780 cm⁻¹ due to the overlapping of the peaks related to the ammonia-water bonds (higher wavelength) for the deformation of the water molecules present in the structure.

Figure 6 shows the effect of the water content on the temperature evolution of compositions C_01 (70% MgO) and C_04 (55% MgO). For compositions containing MgO powders calcined at 900 °C / 2 h and 1100 °C / 2 h, increasing the amount of added water led to increased setting time (retarding the peak temperature), independent of the composition.

Figure 6
Effect of water content on the temperature evolution of compositions containing MgO powders calcined at 900 ºC / 2 h (A) and (B) and at 1100 ºC /2 h (C) and (D).

The amount and temperature of the water used in the admixture are critical for the formation of MPC. From the viewpoint of setting time, higher water contents and lower temperatures of the water-phosphate solution lead to longer setting times for the magnesium phosphate cements. Lower temperatures of solution decrease the dissolution of the MgO grains, thereby retarding the setting time^13,15.

An increase in temperature favors the occurrence of reactions that lead to the formation of hydrated phases, which is also associated with higher surface temperatures of the samples. The same behavior is true for the types of phases formed. Since dittmarite (NH₄MgPO₄.H₂O) has a greater standard enthalpy of formation than that of struvite (NH₄MgPO₄.6H₂O), the temperature on the surface of the cement should also increase^13,15.

Composition C_01 did not show significant variations in the surface temperature of the cements, since it did not show the formation of dittmarite (NH₄MgPO₄.H₂O). This composition had low sensitivity to increasing amounts of water, and little variation in the concentration of its hydrated phases.

Schertelite [Mg(NH₄)₂(HPO₄)₂.4(H₂O)] is formed as a reaction intermediate and converts into struvite or dittmarite^11,28,29, according to the reactions (2) and (3). Struvite (NH₄MgPO₄.6H₂O) and dittmarite (NH₄MgPO₄.H₂O) are chemically and structurally similar, and the transformation from one to the other does not cause any microstructural damage to the molded specimen. Thus, a higher amount of water leads to the formation of struvite (Equation 3), delaying the setting time and resulting in a matrix with less free MgO.

$$MgO+N{H}_4{H}_{2}P{O}_4+3H_{2}O\to Mg{\left(N{H}_4\right)}_2{\left(HP{O}_4\right)}_2.4\left(H_{2}O\right)$$ (2)

$$Mg{\left(N{H}_4\right)}_2{\left(HP{O}_4\right)}_2.4\left(H_{2}O\right)+MgO+7H_{2}O\to MgN{H}_{4}P{O}_4.6H_{2}O$$ (3)

Additionally, C_01 had a longer setting time represented by a delay in time at the peak temperature^9,10,18,22 than C_04 for the same water content when MgO powders calcined at 1100 °C/ 2 h were used; however, this behavior is insignificant when using MgO powders calcined at 900 °C / 2 h. The longer setting time for the C_01 composition is associated with the higher MgO/NH₄H₂PO₄ ratio, leading to the formation of a greater amount of struvite (NH₄MgPO₄.6H₂O). MgO calcined at 900 °C/2 h did not present the same behavior. Due to its high reactivity, reactions occur intensely, even with a higher MgO/NH₄H₂PO₄ ratio.

The water content exerts an important influence on the microstructure, as well as the physical and mechanical properties of the magnesium phosphate cements. Figure 7 shows the effect of water addition on the pore size distribution of these samples.

Figure 7
Effect of water content on the pore size distributions of compositions (A) and (B) containing MgO powders calcined at 900 ºC / 2 h and (C) and (D) containing MgO powders calcined at 1100 ºC / 2 h.

As expected, as the amount of water increased, the samples became more porous and had a larger pore size. Thus, when using MgO powders calcined at 900 ºC / 2 h and 1100 ºC /2 h, the cements of the C_04 composition had a lower open pore volume than those of the C_01 composition. As discussed previously, the C_04 composition used a greater amount of water to form the hydrated phases than C_01 composition (higher MgO/NH₄H₂PO₄ ratio), allowing the free water to evaporate and form pores in the material.

The microstructures of the compositions are shown in Figures 8 and 9. Regardless of the composition and calcination temperature of MgO, cements prepared with higher water contents formed struvite (NH₄MgPO₄.6H₂O) crystals with a smaller average size. Although there were no significant changes in the concentration of the hydrated phases for C_01, an increase in the water volume resulted in a decrease the size and mean diameter of the struvite crystals.

Figure 8
Microstructure of samples (A) C_01 - 40% H₂O; (B) C_01 – 60% H₂O; (C) C_01 - 80% H₂O; (D) C_04 - 40% H₂O; (E) C_04 - 60% H₂O; and (F) C_04 - 80% H₂O prepared using MgO powders calcined at 900 ºC / 2 h. (Struvite phase – S; dittmarite phase - D)

Figure 9
Microstructure of samples (A) C_01 - 40% H₂O; (B) C_01 – 60% H₂O; (C) C_01 - 80% H₂O; (D) C_04 - 40% H₂O; (E) C_04 - 60% H₂O; and (F) C_04 - 80% H₂O prepared using MgO powders calcined at 1100 ºC / 2 h. (Struvite phase – S; dittmarite phase - D)

According to several studies^12,28-30, the mechanism of phase formation in magnesium phosphate cements occurs by the solubilization of MgO in the form of Mg⁺² ions. These ions are further complexed in the form of Mg(H₂O)₆⁺² ions, replacing the adsorbed H₂O molecules on the surface of the basic oxide (MgO). The hydrated phases form only after a complex between these Mg(H₂O)₆⁺² ions and those from the ADP (PO₄⁻³ and NH₄⁺) form, followed by solubilization and then nucleation and growth reactions. That is, a higher concentration of Mg(H₂O)₆⁺² for a fixed concentration of PO₄⁻³ and NH₄⁺ (of ADP) leads to the formation of more nuclei and smaller crystals. Increasing the amount of water is known to facilitate the dissolution of MgO, which would increase the concentration of the Mg⁺² ions. The concentration of PO₄^-3 and NH₄⁺ ions was unchanged because the MgO/ADP ratio was fixed when the amount of water within a given composition was varied, resulting in a decrease in the size of the struvite (NH₄MgPO₄.6H₂O) crystals due to an increase in the amount of water.

For composition C_04 consisting of 40% H₂O, its struvite (NH₄MgPO₄.6H₂O) had a structure that was more fragile than that of compositions with higher water contents. At these conditions, there is a shortage of both water and time for the formation of the hydrated phases, which could lead to the formation of phases with lower crystallinity. The dittmarite (NH₄MgPO₄.H₂O) phase was also observed near the struvite (NH₄MgPO₄.6H₂O) crystals.

According to the results of the mechanical resistance tests (Figure 10), samples calcined at 900 °C had higher reactivity and superior mechanical resistance than that of samples calcined at 1100 °C, regardless of the added water content. A gradual reduction of the mechanical resistance was also observed due to the increase in water content because of higher porosity (Figure 9), which also explains the higher mechanical resistance values for the C04 compositions (lower MgO/NH₄H₂PO₄). As previously discussed, dittmarite (NH₄MgPO₄.H₂O) is the dominant phase when the reaction is fast, whereas struvite (NH₄MgPO₄.6H₂O) dominates when the reaction is slow³²; thereby dittmarite is more resistant than struvite. These results are in accordance with the XRD and FTIR results (Figures 4 and 5).

Figure 10
Axial compressive mechanical strength of magnesium phosphate cement compositions C_01 and C_04, which were prepared using MgO powders calcined at 900^oC/2h and 1100 ºC / 2 h, as a function of water content.

The binder content significantly influences the setting and hardening of the material, whereas its strength influences the mechanical properties^33,34. The amount of phosphate hydrates surrounding the MgO grains increases with the amount of NH₄H₂PO₄ present, consequently increasing the strength of the MPC^35-37.

However, several studies have shown results contrary to those presented in Figure 10. Sugama and Kukacka³⁸ studied the effect of the MgO/ADP ratio on the mechanical strength of magnesium phosphate cements and observed that the higher the amount of MgO (higher MgO/ADP ratio), the higher the mechanical resistance to compression. The same behavior was observed by Yang and Wu²⁷ as well as Sant’Anna and Morelli¹⁵. These studies suggest that the non-solubilized MgO particles are the skeleton of the cement structure, which is why higher concentrations of MgO offered better mechanical resistance. Yang and Wu²⁷ also stress that the mechanical strength of the remaining MgO grains is much higher than the strength of the hydrated phases, although it was stated that the concentration of the hydrated phases should be high enough to bind the MgO grains.

4. Conclusions

Considering the analysis of the results obtained from the experimental conditions adopted for this study, the following can be concluded:

• A higher calcination temperature is associated with a greater crystallite size, higher average particle size, and more crystalline MgO powders; although these powders had lower reactivity due to a reduction in the surface area.

• For the less reactive samples (calcined at 1100 °C) with a high MgO/NH₄H₂PO₄ ratio, an increase in the water content did not lead to additional solubilization of ADP or the formation of more hydrated phases, although the porosity of the cement increased.

• Compositions containing MgO with a higher reactivity (calcined up to 900 °C) and lower MgO/NH₄H₂PO₄ ratio present a tendency to form dittmarite (NH₄MgPO₄.H₂O) and increases the mechanical strength independent of water content, and present a gradual reduction in the mechanical strength as a consequence of the increase in water content due to higher porosity.

• A higher water content and calcination temperature of MgO were associated with a longer MPC setting time.

5. Acknowledgments

CNPq - National Counsel of Technological and Scientific Development (Brazil)

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Publication Dates

• Publication in this collection
  17 July 2020
• Date of issue
  2020

History

• Received
  14 Jan 2020
• Reviewed
  02 May 2020
• Accepted
  21 May 2020