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Article

Effect of Non-Calcined Sugarcane Bagasse Ash as an Alternative Precursor on the Properties of Alkali-Activated Pastes

by
Leila Nóbrega Sousa
1,
Pâmella Fernandes Figueiredo
1,
Sâmara França
1,
Marcos Vinicio de Moura Solar Silva
2,
Paulo Henrique Ribeiro Borges
1 and
Augusto Cesar da Silva Bezerra
1,*
1
Federal Center for Technological Education of Minas Gerais, Belo Horizonte 30421-169, Brazil
2
Cemig Geração e Transmissão S.A., Belo Horizonte 30190-924, Brazil
*
Author to whom correspondence should be addressed.
Molecules 2022, 27(4), 1185; https://doi.org/10.3390/molecules27041185
Submission received: 23 December 2021 / Revised: 27 January 2022 / Accepted: 3 February 2022 / Published: 10 February 2022
(This article belongs to the Special Issue 2nd Edition: Advances in Alkali-Activated Materials)
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Abstract

:
BFS-MK-based alkali-activated materials are well established as an alternative for sustainable and green construction. This work aims to collaborate and encourage the use of biomass ashes, such as sugarcane bagasse ash (SCBA), as a precursor in alkali-activated materials (AAM). This ash is a rich source of aluminosilicate, which is a primary requirement for this application. In addition, this waste is still an environmental liability, especially in developing countries, and with a large volume of annual production. Thus, in this research, alkali-activated pastes (AA) were produced using sugarcane bagasse ash (SCBA), granulated blast furnace slag (BFS) and metakaolin (MK) as precursors. In addition, environmental gains were encouraged with energy savings, with no extra reburn or calcination steps in the SCBA. Thus, the precursors were characterized by laser granulometry, X-ray fluorescence spectrometry (XRF), X-ray diffraction (XRD), scanning electron microscopy (SEM) and Fourier transform infrared spectroscopy (FTIR). The pastes were produced by mixing the precursors with the activator, composed of a mixture of sodium hydroxide 8 mol/L and sodium silicate. Aiming to study the incorporation of SCBA, all samples have a precursor/activator ratio and a BFS/(BFS + MK) ratio constant of 0.6. The compressive strength analysis, FTIR, XRD, TGA, SEM and isothermal calorimetry analyses pointed out the occurrence of alkaline activation in all proposed samples for curing times of 7, 28 and 91 days. The sample GM0.6-BA0 (15% SCBA) achieved the highest compressive strength among the samples proposed (117.7 MPa, at 91 days), along with a good development of strength throughout the curing days. Thus, this work presents the properties of alkaline-activated pastes using SCBA as a sustainable and alternative precursor, seeking to encourage the use of raw materials and alternative waste in civil construction.

1. Introduction

The three-dimensional inorganic polymeric chain structure of the alkali-activated material (AAM) is formed from the reaction of a solid aluminosilicate in a strongly alkaline solution [1]. The possibility of applications for this material is wide, such as in paste, mortar and reinforced concrete [2,3]. In general, precursors can be from natural sources, by-products and industrial residues [1]. Blast furnace slag (BFS) and metakaolin (MK) are the most widely used materials as aluminosilicate sources for AAM. BFS is a by-product of the steel industry, and as it is composed of network-forming anions, such as (SiO4)4− and (AlO4)5−, and network-modifying cations, such as Ca2+, Al3+ and Mg2+ [3], its alkaline activation has been extensively studied. Moreover, metakaolin is generated from the calcination of kaolin, being composed mainly of SiO2 and Al2O3, and the process results in a disordering of the structure, and in the release of aluminum and silicon, which makes the MK structure highly reactive. In recent decades, research has been carried out with different wastes and by-products, such as rice husk ash [4,5], red mud [6], iron tailings [7], reclaimed asphalt pavement [8,9], eucalyptus biomass ash [10], sugarcane bagasse ash [11,12], among others. These works are encouraged by the growing search of the civil construction sector to incorporate sustainability into its processes and products. Some changes are already being applied, and the alkali-activated material shows promise as an alternative to Portland cement in several applications [13,14].
Basically, sugarcane bagasse ash is a residue from sugarcane mills, and it is commonly produced in the cogeneration boilers after the use of bagasse as fuel to produce electricity [15]. Its importance lies in the fact that this plant is the raw material for important consumed products, i.e., sugar and alcohol. The joint production of Brazil, India, China and Thailand corresponds to more than 75% of the world sugarcane production; Brazil alone produced more than 752 mil ton in 2019 [16]. However, as for most agricultural residues, the disposal of this ash is a huge issue, as it is still disposed in landfills in most sugar and ethanol mills, causing environmental damage in water, air and land [17]. It is well known that one of the difficulties in the wide reuse of solid waste, such as SCBA, is the variability of the characteristics of these materials due to geographic and processing variability [18]. In general, SCBA contains cellulose, hemicellulose and lignin [18] and research from different countries shows that the main content of inorganic compounds of SCBA are SiO2, Al2O3 and CaO [19,20,21,22]. The conditions under which the bagasse is burned in the boiler (600–800 °C) for electricity generation produces ash with polymorphic and amorphous crystalline phases [21,23,24,25].
Preliminary studies have shown the feasibility of using this ash as a precursor for alkali activation binder [11,12,26,27,28,29,30]. Castaldelli et al. [12] and Pereira et al. [29] studied the partial replacement of granulated blast furnace slag (BFS) by SCBA, while Tippaysam et al. [11] and Castaldelli et al. [28] studied the binary system fly ash and SCBA. Yadav et al. [26] studied the partial replacement of metakaolin (MK) by SCBA and Tchakouté et al. [30] evaluated the utilization of sodium waterglass from SBCA as activator for producing MK-based geopolymer. Recently, Akbar [27] used SBCA as exclusive precursor for geopolymer production reinforced with propylene fibers. As can be seen, all these works used at most a binary mixture for the geopolymers production and, in addition, only Castaldelli et al. [12] used SCBA in the way it was collected at the factory. All other works carried out the reburning of the ash or SCBA calcination under a controlled environment. For that reason, this works aims to evaluated the feasibility of using non-calcined SCBA as a precursor in a ternary alkali-activated material with MK and BFS.
Thus, in this research, the effect of addition of SCBA on the properties of pastes formulated with MK and BFS (BFS:(BFS + MK) ratio of 0.6) was investigated. The paste samples were produced by mixing the precursors with the activator, composed of a mixture of sodium hydroxide 8M and sodium silicate; moreover, SCBA was ground to increase its reactivity, due to the increase in the surface area. Thus, this work aims to collaborate with the studies of SCBA and, therefore, encourage the reuse of biomass ashes, the disposal of which leads to environmental problems, especially in underdevelopment countries.

2. Results and Discussion

The appearance of samples presented different colors due to the different amounts of SCBA (Figure 1), ranging from gray-brown in the GM0.6-BA0 sample to black in the other samples. The black color of the samples is due to the presence of SCBA.
Figure 2 illustrates the analysis of micromorphology of alkali-activated pastes after 28 days of curing by SEM. In general, all the samples presented good matrix densification. However, as the analyses were performed after the compressive strength, the presence of cracks was observed in all samples. The GM0.6-BA0 sample (Figure 2a) shows a compact and cohesive matrix, and the presence of a large number of pores. These pores are likely due to the incomplete expulsion of air during the molding process. In samples GM0.6-BA15 and GM0.6-BA30 (Figure 2b,c), a more cohesive microstructure was formed, compared to other samples. In GM0.6-BA45 (Figure 2d) images, the presence of unreacted fibers and particles from the SCBA can be identified. These particles impaired the homogeneous development of the matrix due to a lesser dissolution rate of particles and, consequently, the formation of products, such as CASH-type gel [31]. Comparing the images obtained for samples GM0.6-BA0 to GM0.6-BA45, an increase in the addition of SCBA resulted in a more heterogeneous material. Thus, the presence of unreacted particles, pores and voids probably caused a reduction in strength. Then, it can be assumed that the filling effect occurred by crystalline particles [32,33]. The presence of quartz (silica crystalline phase) in the system is able to contribute to build a cohesive agglutinating phase through the incorporation of this phase in the gel network [34].
The average values of water absorption (%), apparent porosity and bulk density (%) at 91 days of curing are shown in Figure 3. Comparing samples from GM0.6-BA0 to GM0.6-BA45, the apparent porosity and water absorption enhance as the content of SCBA increase, as also observed by other authors [11,35,36].
The effect of SiO2:Al2O3 and CaO:SiO2 ratios caused by SCBA had an important role in GM0.6-BA015 and GM0.6-BA030 replacements, in order to induce an increase in compressive strengths, and a low water absorption and apparent porosity. However, at higher levels of substitution, GM0.6-BA45 and GM1-BA50, a negative effect stands out, causing a higher water absorption and apparent porosity (Figure 3). This was in accordance with the compressive strength results (Figure 4), suggesting that the samples with major water absorption and apparent porosity also had the lowest compressive strength.
Regarding the compressive strength, Figure 4 illustrates the average of each mix for each curing time (7, 28 and 91 days), corresponding to the average of four tests with their respective standard deviations. In the present research, it is observed that all mix proportions showed the development of compressive strength within the curing time, showing a continuous occurrence of reaction. FTIR (Figure 5) and XRD (Figure 6) analysis suggested that one of these products may be an amorphous gel (CASH and/or NASH), which has strong binder properties. Moreover, the addition of SCBA caused a reduction in the compressive strength cured at the age of 7 days. Besides that, at this age, the compressive strength of GM0.6-BA030 is higher than GM0.6-BA015, which may be related to the SCBA contribution as a silica source for the polymerization increase producing more ion linking and, consequently, strength development. However, at early ages, when there is an excess of silicon in the solution, the reactions are delayed, resulting in a slower strength gain or even no benefit for the material strength [37,38,39]. Note that the increasing SCBA consequently increases the SiO2:Al2O3 ratio and decreases the AA pastes’ compressive strength [40], being more intense in the GM0.6-BA45 sample at 28 days of age (reduction of 52%).
As can be seen, there was an increase of 17% in GM0.6-BA015 at 28 days and 4% in GM0.6-BA030 at the same age, suggesting that the addition of SCBA up to 30% in this type of AA paste is beneficial for mechanical performance. GM0.6-BA015 and GM0.6-BA030 cured at the ages of 28 days reached the highest compressive strength when compared to others at the same age. In addition, GM0.6-BA015 sample reached almost 100 MPa at 28 days, a value that is only reached by GM0.6-BA0 after 91 days of curing. GM0.6-BA45 paste has a slower development, remaining practically stable up to 28 days, followed by a slight growth at 91 days. Although GM0.6-BA45 and GM1-BA50 pastes have reached the lowest strength values in this work, they are still considered high comparing with other studies using SCBA in AAM [11,12]. Furthermore, all tested activated alkaline pastes meet the international standard specifications of 28 MPa for hydraulic cement [41]; moreover, activated alkaline materials need exhibit resistance above 40 MPa to meet the Brazilian standard [42]. Analysis of variance (ANOVA) was performed in order to better understand the results obtained mathematically. Table 1 shows that all variables studied (days of curing, %SCBA and the interaction between them) show significant variation (p-value < α (0.05)). Thus, it can be seen that there is a variation in strength in relation to the SCBA content and to the curing days (7, 28 and 91 days).
In the FTIR spectra (Figure 5), it can be seen that the presence of bands between 3200–3700 cm−1 and 1630–1640 cm−1, attributed to the vibration mode groups H-OH and OH, respectively, suggesting the formation of hydrated products in the samples [43], and to the presence of free water in the sample [44]. The results were obtained after curing 91 days. The band at 775 cm−1, present in MK and SCBA, is no longer present in paste sample spectra, which may be related to the dissolution of Si-O bonds present in the amorphous phase, attributed to this band.
It can also be seen that the 900–1200 cm−1 band shifted towards lower wave numbers when compared to SCBA and MK. Since the Al-O bond is weaker and longer than the Si-O bond, this shift suggested an elongation of the Si-O-T bond (T: Al or Si) and a reduction in the bond angle, possibly caused by the replacement of Si4+ by Al3+ ions [26]. The main band in the 960 cm−1 region and the bands located in lower wave numbers (600–400 cm−1) are associated with the formation of CASH and CSH gels [45], due to asymmetric stretching vibration of Si-O-T bonds in the structure of gel-network [44]. In all AA pastes, the band located in the 1400 cm−1 region, typical of the vibration of the elongation of the C-O bond, can be attributed to the presence of carbonates [46], probably due to the presence of CaCO3. This suggests that some carbonation process could have occurred in the sample. Based on these, the process and mixtures proposed caused structural changes in the examined AA paste samples, which are attributed to the formation of a new reaction product characteristic of AAM. However, it is noteworthy that the change in the condition of the system directly impacts the reaction rate and the system equilibrium.
The XRD pattern (Figure 6) shows a crystalline phase related to the presence of quartz and calcite. The appearance of a halo between 28–30° in all analyzed samples cured at 28 days could be related to the formation of amorphous gels, such as CASH, CSH and NASH [31,45]. This was also corroborated by FTIR analysis (Figure 5). The presence of quartz is related to unreacted particles present in the precursors, mainly in SCBA and MK, as pointed out in the XRD analyzes of the precursors (Figure 6). In this line, in the alkaline activation of the binary system formed by metakaolin and BFS, dynamics of compensation occur for the formation of the binding gel, so at low alkalinity, the gel formation via MK dissolution is favored, and, on the other hand, when the solution reaches high pH, activation via BFS stands out in relation to MK [46]. Thus, the chemical analyzes suggested that the alkaline activation reaction was effective with the proposed precursors and activators, since the SCBA addition on binary system MK and BFS contributed to the appearance of new reaction products, which could be confirmed by FTIR analysis.
In the results of thermogravimetry and differential thermogravimetry analysis (TGA/DTG) (Figure 7), the remarkable weight loss occurred between temperatures of 0 and 250 °C, followed by a gradual loss up to a temperature of 1000 °C. The weight loss at 100 °C could be related to the evaporation of free water. The total weight losses in pastes GM0.6-BA0, GM0.6-BA015, GM0.6-BA030, GM0.6-BA45 and GM1-BA50 were 13.70, 17.97, 14.54, 16.15 and 17.07%, respectively. The lower weight loss could be related to a denser microstructures, since looser particles allow free and chemically bound water to be released more easily [47]. The decomposition and dehydration of aluminosilicate gels and organic content was noticed around ~100–200 °C, with the evaporation of water from the system, followed by up to ~600 °C with the release of chemically bound water, continuing at approximately 800 °C [48,49,50]. Among the SBCA pastes, the highest weight loss associated to GM0.6-BA015 could be related to higher aluminosilicate gel formation in this material, while the lowest (GM0.6-BA030 and GM0.6-BA45) could be related to lower formation. Furthermore, decompositions between 400 and 800 °C can be related to carbonates, as calcite, which decompose into CaO and CO2, which was more expressive in GM1-BA50 [36,51].
Understanding the evolution of heat provides important information about the processes involved during the reactions. The alkaline activation process involves several steps, which occur both serially and simultaneously [52]. The isothermal calorimetry heat may indicated the formation of reaction products, as shown in Figure 8. Whitin the first hours, the interaction of the precursor particles with the activator releases a significante amount of heat. The total heat released after 72 h was higher for samples GM0.6-BA015 and GM0.6-BA0, followed by GM1-BA50, GM0.6-BA030 and GM0.6-BA45, being 43.3, 41.7, 41.2, 38.3 and 34.8 J/g, respectively. It can be seen that in the cumulative heat, for all pastes, there is a markedrelease of heat up to ~30 h of testing, suggesting that during this period, new reaction products were being produced. Thus, increasing the ash content caused a growing in the cumulative heat, especially in the initial hours ( ~15 h).
The heat flow and cumulative heat (Figure 8) are lower than those reported for cement-based materials [53,54,55], which is commonly over 100 J/g. The low heat released is considered beneficial, as it decreases the potential for thermal cracking and shrinkage [56]. A higher cumulative heat associated with GM0.6-BA15 could be related to the higher aluminosilicate formation, while a lower cumulative heat is associated with GM0.6-BA45 and lower aluminosilicate formation. This result is supported by the compressive strength result. The characteristic of the peaks and the stage (hours) in which they occur vary according to the alkali-activated system studied, and may also presents as two or three exothermic peaks [57,58,59,60]. The single peak shown in Figure 8 could be related to a possible overlapping of the peaks, followed by a progressive release of the reaction products, as pointed out by other authors [61,62]. The occurrence of a single peak is related to the combination of particle wetting steps and a rapid dissolution and precipitation of reaction products [58,59], probably caused by high alkalinity. In this line, the reaction products are continuously formed, as the Ca2+ ions are gradually released into solution, since while the solubility of silica and alumina increases with increasing pH, the solubility of calcium decreases [59,63]. The results indicate that there was a gradual formation of products, which provided the development of material strength within curing ages, corroborating compressive strength results (Figure 4). Besides that, among the GM0.6 pastes, the one with lower calcium content and higher silicon content (GM0.6-BA45) shows lower reactivity, which may indicate that these ions directly influence the reactions rate in these materials.

3. Materials and Methods

3.1. Materials

Granulated blast furnace slag (BFS), metakaolin (MK) and sugarcane bagasse ash (SCBA) were used as solid precursor in this work to develop AA pastes (Figure 9) samples. MK was supplied by Metacaulim do Brasil, Jundiaí, Brazil, and SCBA from sugar mill BEVAP Bioenergia, João Pinheiro, Brazil. These raw materials were dried in an oven at 100 ± 5 °C for 24 h in order to increase the surface area, and consequently, the chemical reactivity [21]. SCBA exhibits a black color (Figure 9c), which signifies a high unburnt carbon content due to inefficient combustion of biomass [64].
The reduction of SCBA particle size contributes to the development of more homogeneous and dense matrices, with better packing of particles and smaller pores [65,66], resulting in a more efficient alkaline activation by providing amorphous silicates to the alkaline solution and the formation of a structured of sodium aluminosilicate hydrate (NASH) or calcium silicate hydrate (CASH)-type network [27]. NASH is formed by precursors with low calcium content, whereas CASH is produced by high-calcium precursors [7]. These geopolymerization products are directly related to the mechanical and durability of AAM [67,68]. Thus, after previous laboratory tests, the ash was ground in a high-performance planetary mill at 300 rpm (in 500 mL pots and 16 zirconia oxide spheres of 10 mm diameter) for 12 min (after time trials of 2, 4, 6, 8, 10 and 12 min). The particle size distribution of precursor was obtained by laser diffraction analysis using CILAS 1090 [69]. The mean particle size (Dm) of the precursor is around 25 μm, being 24.07, 22.14 and 28.36 μm for MK, BFS and SCBA, respectively (Figure 10).
The chemical oxides in SCBA, MK and BFS (Table 2) were identified by X-Ray fluorescence (XRF) Shimadzu equipment (Tokyo, Japan). The loss on ignition (LOI) value of 11.5% is similar to other research studies that reported values more than 10% for SCBA without further treatment [12,22,26].
The oxide composition showed that silica (SiO2) and alumina (Al2O3) are the main oxides identified in MK and SCBA (Table 2), while BFS also exhibits a high calcium oxide (CaO) and Fe2O3 content. In this way, the XRD pattern (Figure 11) shows that quartz (SiO2, COD 969013322) is the main crystalline phase in SCBA, and this could be related to sand adhered to the bagasse in the crop field [70]. The baseline of the diffractogram has a deviation, suggesting a proportion of an amorphous phase in the sample. This amorphous hump could be related to amorphous silica present in bagasse composition and the presence of carbon of unburned material [71]. Moreover, the MK diffractogram identified crystalline phases illite (COD 969013719), kaolinite (COD 969009235) and muscovite (COD 969006330). The BFS presented a vitreous phase identified as an amorphous hump in the 20°–35° region [12,31], along with crystalline phases as calcite (COD 969009668), akermanite (COD 969006942) and hematite. The main crystalline phases of MK are muscovite and quartz. In addition, MK exhibits a high content of crystalline phases, which could reduce its reactivity [72].
The FTIR spectra of the precursors (Figure 12) identified wave numbers between 2000 and 400 cm−1. The main peak is located in the region of 900–1200 cm−1 and it is associated to Si-OT asymmetrical stretching vibrations (T being Si or Al tetrahedral) [73]. In MK, this peak is around 1030 cm−1 and is deeper than the peaks in SCBA and BFS, which are located in the 1040 cm−1 and 910 cm−1 band, respectively. Moreover, in BFS spectra, a shoulder is signed around 870 cm−1, which is associated with Al-O asymmetric stretching [74] present in the vitreous phase [43]. Carbonate traces are identified at 1430 and 710 cm−1 and are associated with the O-C-O asymmetric elongation mode of the CO32− anion group [75]. In MK and SCBA, the band located at 770 cm−1 is associated with the Al-O elongation vibration, and in the regions of 500–400 cm−1 with the vibration of the Si-O-Al and Si-O-Si bond [57,70,76] and also with the bending of amorphous silica [26]. The appearance of Si-O bands identified in the SCBA spectrum can be related to the presence of quartz in the material, as also identified by XRD analysis (Figure 11c).
Morphology of precursors particles were observed that BFS and MK had particles with different size and shapes (Figure 13a–c). The images were obtained by a scanning electron microscope (SEM) TM-3000 Hitachi equipment (Tokyo, Japan) under low vacuum with a backscattered electron detector and electron acceleration voltage of 15 kV. The presence of sugarcane bagasse fibers (Figure 13c) can be related to a partial or unburnt particle, and it is in accordance with an LOI value of 11.5% (Table 2).

3.2. Methods

Paste Samples’ Preparation and Characterization

It is well known that BFS and MK are precursors commonly used in AAM; thus, the present work seeks to understand the effect of SCBA incorporation in the MK-BFS system. The alkali-activated paste samples were formulated (Table 3) with varied content of SCBA (45, 30, 15 and 0%) and a constant GBFS:(GBFS + MK) ratio of 0.6. After laboratory tests, the activator:precursor ratio was set at 0.60 and the mixtures were cured at 25 ± 5 °C.
The alkali activator solution was a mixture of sodium hydroxide (NaOH, 8 mol/L) and sodium silicate solution (Na2O 14.86%, SiO2 32.07%, H2O 52.16%), with a total modulus (SiO2/Na2O molar ratio) of 1.43, in accordance with the range of values used by other authors in the alkali activation [77] of agro-industrial wastes [11,12,26,47]. Table 3 illustrates the mix proportion and the oxides ratios of all pastes. The SiO2:Al2O3 ratio ranged from 5.26 to 6.85, reaching 10.14 in the GM0-BA50 sample.
A wide range of SiO2:Al2O3 ratios proved to be efficient for alkaline activation [40,78], which coincides with the ratio range found in this work. It can be seen that, due to the high content of SiO2 in its composition, increasing the addition of SCBA increases the SiO2:Al2O3 ratio. Furthermore, the CaO content in the system drastically reduces in samples GM0.6-BA45 and GM0-BA50. The GM0-BA50 sample reached a compressive strength average of 1.5 MPa, and also disaggregated easily with handling. Because of this, only the mixture with 50% SCBA–50% BFS (GM1-BA50) continued in this study. This sample fragility was caused by the insufficient chemical interaction between the raw materials, which may be related to the cure temperature, since some systems require thermal curing to develop an early strength [57,79].
Thus, to prepare the pastes, the solid part was mixed in a planetary mixer for 1 min to homogenize the precursors. Then, the activator solution was added and mixed at low speed for 2 min. The fresh pastes were poured into cylindrical metal molds (25 × 50 mm) and vibrated in the vibration table in order to release entrapped air bubbles. The samples were cured at room temperature for 24 h; the surface was covered with glass plates to avoid water evaporation. After this period, the samples were demolded and stored in a closed container until they reached the curing ages of 7, 28 and 91 days.
The crystalline mineralogical characterization of raw materials (MK, SCBA and BFS) and pastes was obtained by X-Ray diffraction (XRD) Shimadzu equipment (Tokyo, Japan) using Cu-kα (λ = 1.5418 Å), at 40 kV and 30 mA, and an angle measurement interval (2θ) between 10°and 80° and step size of 0.02; for phase identification, the Match! 3 software was used [80] with the Crystallography Open Database (COD) revision no. 254652. FTIR, compressive strength, SEM analyses, water absorption and calorimetry techniques were performed in the pastes after curing time. Fourier Transform Infrared Spectroscopy (FTIR) analysis was performed with IR-Prestige-21 Shimadzu equipment; the spectrum wavelengths ranged between 4000 cm−1 and 400 cm−1 [7,69]. Moreover, the microscopy experiments of paste samples were performed on a scanning electron microscopy (SEM) model Hitachi TM-3000 (Tokyo, Japan) under low vacuum with a backscattered electron detector and electron acceleration voltage of 15 kV.
Thermogravimetric analysis (TGA) Hitachi equipment (Tokyo, Japan) was performed with the temperature range of 25 °C–1000 °C at 10 °C/min in a nitrogen environment at 60 mL/min purge rate in a STA7300 instrument. Samples were crushed, transferred immediately to an alumina crucible and held under isothermal conditions. The hydration heat evolution of paste samples was assessed by isothermal calorimetry, I-calorimeter Cal-4000 4 channel Calmetrix equipment (Arlington, MA, USA), at a temperature of 23 °C, for 72 h of reaction. In this analysis, fresh paste was mixed externally and immediately placed in the calorimeter. The samples were composed of 15 g of precursors and 9 g of activators, keeping the activators:precursors ratio 0.6 for all tests. For the mechanical characterization, a compressive strength test was conducted according to Brazilian standard NBR 7215 [81] at curing ages of 7, 28 and 91 days, with an increasing stress rate of 0.25 MPa/s in an EMIC DL 30000 universal test machine (São José dos Pinhais, Brazil), and the programs TESC and Vmaq were used. Variance analysis (ANOVA) of the compressive strength results were conducted using the software package Minitab 17 to validate the results. The water absorption, apparent porosity, bulk density (dry and saturated) and apparent density were performed and calculated based on Brazilian standard NBR 9778 [82].

4. Conclusions

This work studies the feasibility of using sugarcane bagasse ash as a precursor in alkali-activated pastes in a ternary system, with metakaolin and granulated blast furnace slag. The conclusions drawn from the physical, chemical, and mechanical characterizations obtained in this study are as follows:
  • SCBA can be used as a precursor in alkali-activated pastes in a ternary cement with a metakaolin and granulated blast furnace slag (BFS/(BFS + MK) ratio of 0.6. The high SiO2/Al2O3 ratio and presence of crystalline particles contributed to the development of AA pastes;
  • XRD analysis revealed the appearance of a typical hump around 28–30 in all samples cured at 28 days, suggesting the formation of a typical AAM gel. This statement is also confirmed by other analyses, such as FTIR, TGA and SEM;
  • The addition of SCBA had an important role in GM0.6-BA015 and GM0.6-BA030, increasing the compressive strength without causing a significant effect on water absorption, porosity and bulk density;
  • The increase in the SCBA content causes a reduction in strength and a considerable increase in water absorption, as occurred with samples GM0.6-BA45 and GM1-BA50. However, compared with other works using OPC and international standards, these samples showed expressive strength.
Research such as this allows the options to expand the possibilities for precursors in AAM. This enables, therefore, implementation of SCBA as precursor according to regional availability, leading to environmental benefits and adding value to waste that is still deposited in landfills. However, it is noteworthy that there are still obstacles to overcome regarding the practical applicability of the large-scale use of SCBA in building materials, such as the variability in geographic distribution, transport and logistics costs and diversity of materials processing in sugarcane mills, among others. Therefore, further research on processing and parameter optimization for the application in AAM is highly recommended.

Author Contributions

L.N.S.: Conceptualization, investigation, writing—original draft preparation, acquisition and analysis of data; P.F.F.: writing—original draft preparation and data acquisition; S.F.: investigation and acquisition of data; M.V.d.M.S.S.: funding acquisition and project administration; P.H.R.B.: funding acquisition and project administration; A.C.d.S.B.: Conceptualization, methodology, supervision, funding acquisition, writing—review and editing and project administration. All authors have read and agreed to the published version of the manuscript.

Funding

This work was supported by the Energy Company of Minas Gerais (CEMIG) and the National Electric Energy Agency (ANEEL) for funding through the PD ANEEL CEMIG GT616 project [grant number GT616], Minas Gerais State Research Foundation (FAPEMIG) [grant number APQ-03739–16], National Council for Scientific and Technological Development (CNPq) [grant number PQ 315653/2020–5] and the Brazilian Federal Agency for Support and Evaluation of Graduate Education (CAPES) [grant number 001].

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

The data presented in this study are available on request from the corresponding author.

Acknowledgments

The authors gratefully acknowledge BEVAP Bioenergia for providing the material for this study.

Conflicts of Interest

The authors declare no conflict of interest.

Sample Availability

Samples of the compounds presented in the paper are available from the authors.

References

  1. Provis, J.L. Alkali-activated materials. Cem. Concr. Res. 2018, 114, 40–48. [Google Scholar] [CrossRef]
  2. Silva, G.J.B.; Santana, V.P.; Wójcik, M. Investigation on mechanical and microstructural properties of alkali-activated materials made of wood biomass ash and glass powder. Powder Technol. 2021, 377, 900–912. [Google Scholar] [CrossRef]
  3. Palomo, A.; Krivenko, P.; Garcia-Lodeiro, I.; Kavalerova, E.; Maltseva, O.; Fernández-Jiménez, A.; Krivenko, P.; Garcia-Lodeiro, I.; Palomo, A.; Kavalerova, E.; et al. A review on alkaline activation: New analytical perspectives. Mater. Constr. 2014, 64, e022. [Google Scholar] [CrossRef] [Green Version]
  4. Alnahhal, M.F.; Hamdan, A.; Hajimohammadi, A.; Kim, T. Effect of rice husk ash-derived activator on the structural build-up of alkali activated materials. Cem. Concr. Res. 2021, 150, 106590. [Google Scholar] [CrossRef]
  5. Font, A.; Soriano, L.; Moraes, J.C.B.; Tashima, M.M.; Monzó, J.; Borrachero, M.V.; Payá, J. A 100% waste-based alkali-activated material by using olive-stone biomass ash (OBA) and blast furnace slag (BFS). Mater. Lett. 2017, 203, 46–49. [Google Scholar] [CrossRef] [Green Version]
  6. Hoang, M.D.; Do, Q.M.; Le, V.Q. Effect of curing regime on properties of red mud based alkali activated materials. Constr. Build. Mater. 2020, 259, 119779. [Google Scholar] [CrossRef]
  7. da Silva Bezerra, A.C.; França, S.; de Magalhães, L.F.; de Carvalho, M.C.R. Alkaline activation of high-calcium ash and iron ore tailings and their recycling potential in building materials. Ambient. Construído 2019, 19, 99–112. [Google Scholar] [CrossRef] [Green Version]
  8. Costa, J.O.; Borges, P.H.R.; dos Santos, F.A.; Bezerra, A.C.S.; Blom, J.; Van den bergh, W. The Effect of Reclaimed Asphalt Pavement (RAP) Aggregates on the Reaction, Mechanical Properties and Microstructure of Alkali-Activated Slag. CivilEng 2021, 2, 794–810. [Google Scholar] [CrossRef]
  9. Costa, J.O.; Borges, P.H.R.R.; dos Santos, F.A.; Bezerra, A.C.S.; Van den bergh, W.; Blom, J.; Flávio, A.; Cesar, A.; Bezerra, S.; Van Den, W.; et al. Cementitious binders and reclaimed asphalt aggregates for sustainable pavement base layers: Potential, challenges and research needs. Constr. Build. Mater. 2020, 265, 120325. [Google Scholar] [CrossRef]
  10. Teixeira, A.H.C.; Junior, P.R.R.S.; Silva, T.H.; Barreto, R.R.; da Silva Bezerra, A.C. Low-carbon concrete based on binary biomass ash-silica fume binder to produce eco-friendly paving blocks. Materials 2020, 13, 1534. [Google Scholar] [CrossRef] [Green Version]
  11. Tippayasam, C.; Boonsalee, S.; Sajjavanich, S.; Ponzoni, C.; Kamseu, E.; Chaysuwan, D. Geopolymer Development by Powders of Metakaolin and Wastes in Thailand. In Proceedings of the Advances in Science and Technology, Montecatini Terme, Italy, 6–18 June 2010; Volume 69, pp. 63–68. [Google Scholar]
  12. Castaldelli, V.N.; Akasaki, J.L.; Melges, J.L.P.; Tashima, M.M.; Soriano, L.; Borrachero, M.V.; Monzó, J.; Payá, J. Use of slag/sugar cane bagasse ash (SCBA) blends in the production of alkali-activated materials. Materials 2013, 6, 3108–3127. [Google Scholar] [CrossRef] [PubMed]
  13. Jiao, Z.; Wang, Y.; Zheng, W.; Huang, W. Effect of Dosage of Alkaline Activator on the Properties of Alkali-Activated Slag Pastes. Adv. Mater. Sci. Eng. 2018, 2018, 8407380. [Google Scholar] [CrossRef] [Green Version]
  14. Provis, J.L.; Bernal, S.A. Geopolymers and Related Alkali-Activated Materials. Annu. Rev. Mater. Res. 2014, 44, 299–327. [Google Scholar] [CrossRef]
  15. Companhia Nacional de Abastecimento (CONAB). A Geração Termoelétrica Com a Queima do Bagaço de Cana-de-Açúcar no BRASIL; Ministério da Agricultura, Pecuária e Abastecimento: Brasília, Brazil, 2011.
  16. Food and Agriculture Organization of the United Nations (FAO). Rankings—Countries by Commodity. Available online: http://www.fao.org/faostat/en/#rankings/countries_by_commodity (accessed on 22 November 2020).
  17. Ahmad, W.; Ahmad, A.; Ostrowski, K.A.; Aslam, F.; Joyklad, P.; Zajdel, P. Sustainable approach of using sugarcane bagasse ash in cement-based composites: A systematic review. Case Stud. Constr. Mater. 2021, 15, e00698. [Google Scholar] [CrossRef]
  18. Gopinath, A.; Bahurudeen, A.; Appari, S.; Nanthagopalan, P. A circular framework for the valorisation of sugar industry wastes: Review on the industrial symbiosis between sugar, construction and energy industries. J. Clean. Prod. 2018, 203, 89–108. [Google Scholar] [CrossRef]
  19. Garcia, D.C.S.; de Souza Soares, M.M.N.; da Silva Bezerra, A.C.; Aguilar, M.T.P.; Figueiredo, R.B. Microstructure and hardness of cement pastes with mineral admixture. Rev. Mater. 2017, 22, 145. [Google Scholar] [CrossRef] [Green Version]
  20. Jagadesh, P.; Ramachandramurthy, A.; Murugesan, R. Evaluation of mechanical properties of Sugar Cane Bagasse Ash concrete. Constr. Build. Mater. 2018, 176, 608–617. [Google Scholar] [CrossRef]
  21. Cordeiro, G.C.; Kurtis, K.E. Effect of mechanical processing on sugar cane bagasse ash pozzolanicity. Cem. Concr. Res. 2017, 97, 41–49. [Google Scholar] [CrossRef]
  22. Khawaja, S.A.; Javed, U.; Zafar, T.; Riaz, M.; Zafar, M.S.; Khan, M.K. Eco-friendly incorporation of sugarcane bagasse ash as partial replacement of sand in foam concrete. Clean. Eng. Technol. 2021, 4, 100164. [Google Scholar] [CrossRef]
  23. Soares, M.M.N.S.; Poggiali, F.S.J.; Bezerra, A.C.S.; Figueiredo, R.B.; Aguilar, M.T.P.; Cetlin, P.R. The effect of calcination conditions on the physical and chemical characteristics of sugar cane bagasse ash. Rem Rev. Esc. Minas 2014, 67, 33–39. [Google Scholar] [CrossRef] [Green Version]
  24. Ferreira, R.T.L.; Nunes, F.M.M.P.; Bezerra, A.C.S.; Figueiredo, R.B.; Cetlin, P.R.; Aguilar, M.T.P. Influence of reburning on the pozolanicity of sugar-cane bagasse ashes with different characteristics. Mater. Sci. Forum 2016, 869, 141–146. [Google Scholar] [CrossRef]
  25. Bezerra, A.C.d.S.; Saraiva, S.L.C.; Lara, L.F.d.S.; de Castro, L.W.A.; Gomes, R.C.; Rodrigues, C.d.S.; Ferreira, M.C.N.F.; Aguilar, M.T.P. Effect of partial replacement with thermally processed sugar cane bagasse on the properties of mortars. Rev. Mater. 2017, 22, e11785. [Google Scholar] [CrossRef] [Green Version]
  26. Yadav, A.L.; Sairam, V.; Srinivasan, K.; Muruganandam, L. Synthesis and characterization of geopolymer from metakaolin and sugarcane bagasse ash. Constr. Build. Mater. 2020, 258, 119231. [Google Scholar] [CrossRef]
  27. Akbar, A.; Farooq, F.; Shafique, M.; Aslam, F.; Alyousef, R.; Alabduljabbar, H. Sugarcane bagasse ash-based engineered geopolymer mortar incorporating propylene fibers. J. Build. Eng. 2021, 33, 101492. [Google Scholar] [CrossRef]
  28. Castaldelli, V.N.; Moraes, J.C.B.; Akasaki, J.L.; Melges, J.L.P.; Monzó, J.; Borrachero, M.V.; Soriano, L.; Payá, J.; Tashima, M.M. Study of the binary system fly ash/sugarcane bagasse ash (FA/SCBA) in SiO2/K2O alkali-activated binders. Fuel 2016, 174, 307–316. [Google Scholar] [CrossRef] [Green Version]
  29. Pereira, A.; Akasaki, J.L.; Melges, J.L.P.; Tashima, M.M.; Soriano, L.; Borrachero, M.V.; Monzó, J.; Payá, J. Mechanical and durability properties of alkali-activated mortar based on sugarcane bagasse ash and blast furnace slag. Ceram. Int. 2015, 41, 13012–13024. [Google Scholar] [CrossRef] [Green Version]
  30. Tchakouté, H.K.; Rüscher, C.H.; Hinsch, M.; Djobo, J.N.Y.; Kamseu, E.; Leonelli, C. Utilization of sodium waterglass from sugar cane bagasse ash as a new alternative hardener for producing metakaolin-based geopolymer cement. Chem. Erde 2017, 77, 257–266. [Google Scholar] [CrossRef]
  31. Sithole, T.; Tsotetsi, N.; Mashifana, T. Synthesis of Ambient Cured GGBFS Based Alkali Activated Binder Using a Sole Alkaline Activator: A Feasibility Study. Appl. Sci. 2021, 11, 5887. [Google Scholar] [CrossRef]
  32. Tavares, L.R.C.; Junior, J.F.T.; Costa, L.M.; da Silva Bezerra, A.C.; Cetlin, P.R.; Aguilar, M.T.P. Influence of quartz powder and silica fume on the performance of Portland cement. Sci. Rep. 2020, 10, 1–15. [Google Scholar] [CrossRef]
  33. MENEZES, R.M.R.O.; DA SILVA, R.M.; FIGUEIREDO, E.P.; BEZERRA, A.C.D.S.; AGUILAR, M.T.P.; CETLIN, P.R. Hydraulic binder obtained from recycled cement and sand powder. Rev. IBRACON Estrut. Mater. 2018, 11, 1178–1185. [Google Scholar] [CrossRef]
  34. Autef, A.; Joussein, E.; Gasgnier, G.; Rossignol, S. Role of the silica source on the geopolymerization rate. J. Non. Cryst. Solids 2012, 358, 2886–2893. [Google Scholar] [CrossRef]
  35. Joshaghani, A.; Moeini, M.A. Evaluating the effects of sugar cane bagasse ash (SCBA) and nanosilica on the mechanical and durability properties of mortar. Constr. Build. Mater. 2017, 152, 818–831. [Google Scholar] [CrossRef]
  36. Liang, G.; Zhu, H.; Zhang, Z.; Wu, Q. Effect of rice husk ash addition on the compressive strength and thermal stability of metakaolin based geopolymer. Constr. Build. Mater. 2019, 222, 872–881. [Google Scholar] [CrossRef]
  37. Melges, J.L.P.; Monzó, J.; Tashima, M.M.; Moraes, J.C.B.; Borrachero, M.V.; Soriano, L.; Akasaki, J.L.; Payá, J. Increasing the sustainability of alkali-activated binders: The use of sugar cane straw ash (SCSA). Constr. Build. Mater. 2016, 124, 148–154. [Google Scholar] [CrossRef] [Green Version]
  38. Moraes, J.C.B.; Tashima, M.M.; Akasaki, J.L.; Melges, J.L.P.; Monzó, J.; Borrachero, M.V.; Soriano, L.; Payá, J. Effect of sugar cane straw ash (SCSA) as solid precursor and the alkaline activator composition on alkali-activated binders based on blast furnace slag (BFS). Constr. Build. Mater. 2017, 144, 214–224. [Google Scholar] [CrossRef] [Green Version]
  39. Moraes, J.C.B.; Font, A.; Soriano, L.; Akasaki, J.L.; Tashima, M.M.; Monzó, J.; Borrachero, M.V.; Payá, J. New use of sugar cane straw ash in alkali-activated materials: A silica source for the preparation of the alkaline activator. Constr. Build. Mater. 2018, 171, 611–621. [Google Scholar] [CrossRef] [Green Version]
  40. Chindaprasirt, P.; De Silva, P.; Sagoe-Crentsil, K.; Hanjitsuwan, S. Effect of SiO2 and Al2O3 on the setting and hardening of high calcium fly ash-based geopolymer systems. J. Mater. Sci. 2012, 47, 4876–4883. [Google Scholar] [CrossRef]
  41. ASTM International C1157; Standard Performance Specification for Hydraulic Cement. ASTM International: West Conshohocken, PA, USA, 2017.
  42. NBR 16697; Cimento Portland-Requisitos. Associação Brasileira de Normas Técnicas: São Paulo, Brazil, 2018.
  43. Ismail, I.; Bernal, S.A.; Provis, J.L.; San Nicolas, R.; Hamdan, S.; van Deventer, J.S.J. Modification of phase evolution in alkali-activated blast furnace slag by the incorporation of fly ash. Cem. Concr. Compos. 2014, 45, 125–135. [Google Scholar] [CrossRef]
  44. Wang, Y.; Cao, Y.; Zhang, Z.; Huang, J.; Zhang, P.; Ma, Y.; Wang, H. Study of acidic degradation of alkali-activated materials using synthetic C-(N)-A-S-H and N-A-S-H gels. Compos. Part B Eng. 2021, 230, 109510. [Google Scholar] [CrossRef]
  45. Garcia-Lodeiro, I.; Palomo, A.; Fernández-Jiménez, A.; MacPhee, D.E. Compatibility studies between N-A-S-H and C-A-S-H gels. Study in the ternary diagram Na2O-CaO-Al2O3-SiO 2-H2O. Cem. Concr. Res. 2011, 41, 923–931. [Google Scholar] [CrossRef]
  46. Bernal, S.A.; Provis, J.L.; Rose, V.; Mejía De Gutierrez, R. Evolution of binder structure in sodium silicate-activated slag-metakaolin blends. Cem. Concr. Compos. 2011, 33, 46–54. [Google Scholar] [CrossRef]
  47. Liang, G.; Zhu, H.; Zhang, Z.; Wu, Q.; Du, J. Investigation of the waterproof property of alkali-activated metakaolin geopolymer added with rice husk ash. J. Clean. Prod. 2019, 230, 603–612. [Google Scholar] [CrossRef]
  48. Cui, Y.; Wang, D.; Wang, Y.; Sun, R.; Rui, Y. Effects of the n(H2O: Na2O eq ) ratio on the geopolymerization process and microstructures of fly ash-based geopolymers. J. Non. Cryst. Solids 2019, 511, 19–28. [Google Scholar] [CrossRef]
  49. Duxson, P.; Provis, J.L.; Lukey, G.C.; Mallicoat, S.W.; Kriven, W.M.; Van Deventer, J.S.J. Understanding the relationship between geopolymer composition, microstructure and mechanical properties. Colloids Surfaces A Physicochem. Eng. Asp. 2005, 269, 47–58. [Google Scholar] [CrossRef]
  50. Rovnaník, P.; Bayer, P.; Rovnaníková, P. Characterization of alkali activated slag paste after exposure to high temperatures. Constr. Build. Mater. 2013, 47, 1479–1487. [Google Scholar] [CrossRef]
  51. Shi, D.; Ye, J.; Zhang, W. Effects of activator content on properties, mineralogy, hydration and microstructure of alkali-activated materials synthesized from calcium silicate slag and ground granulated blast furnace slag. J. Build. Eng. 2020, 32, 101791. [Google Scholar] [CrossRef]
  52. Muñiz-Villarreal, M.S.; Manzano-Ramírez, A.; Sampieri-Bulbarela, S.; Gasca-Tirado, J.R.; Reyes-Araiza, J.L.; Rubio-Ávalos, J.C.; Pérez-Bueno, J.J.; Apatiga, L.M.; Zaldivar-Cadena, A.; Amigó-Borrás, V. The effect of temperature on the geopolymerization process of a metakaolin-based geopolymer. Mater. Lett. 2011, 65, 995–998. [Google Scholar] [CrossRef]
  53. Lorena Figueiredo Martins, M.; Roberto Ribeiro Soares Junior, P.; Henrique da Silva, T.; de Souza Maciel, P.; Peixoto Pinheiro, I.; Cesar da Silva Bezerra, A. Magnesium industry waste and red mud to eco-friendly ternary binder: Producing more sustainable cementitious materials. Constr. Build. Mater. 2021, 310, 125172. [Google Scholar] [CrossRef]
  54. Tang, P.; Chen, W.; Xuan, D.; Zuo, Y.; Poon, C.S. Investigation of cementitious properties of different constituents in municipal solid waste incineration bottom ash as supplementary cementitious materials. J. Clean. Prod. 2020, 258, 120675. [Google Scholar] [CrossRef]
  55. Ustabaş, İ.; Kaya, A. Comparing the pozzolanic activity properties of obsidian to those of fly ash and blast furnace slag. Constr. Build. Mater. 2018, 164, 297–307. [Google Scholar] [CrossRef]
  56. Mohamed, R.; Abd Razak, R.; Abdullah, M.M.A.B.; Abd Rahim, S.Z.A.; Yuan-Li, L.; Subaer; Sandu, A.V.; Wysłocki, J.J. Heat evolution of alkali-activated materials: A review on influence factors. Constr. Build. Mater. 2022, 314, 125651. [Google Scholar] [CrossRef]
  57. Sun, Z.; Vollpracht, A. One year geopolymerisation of sodium silicate activated fly ash and metakaolin geopolymers. Cem. Concr. Compos. 2019, 95, 98–110. [Google Scholar] [CrossRef]
  58. Chithiraputhiran, S.; Neithalath, N. Isothermal reaction kinetics and temperature dependence of alkali activation of slag, fly ash and their blends. Constr. Build. Mater. 2013, 45, 233–242. [Google Scholar] [CrossRef]
  59. Bernal, S.A. Effect of the activator dose on the compressive strength and accelerated carbonation resistance of alkali silicate-activated slag/metakaolin blended materials. Constr. Build. Mater. 2015, 98, 217–226. [Google Scholar] [CrossRef]
  60. Gao, X.; Yu, Q.L.; Brouwers, H.J.H. Reaction kinetics, gel character and strength of ambient temperature cured alkali activated slag-fly ash blends. Constr. Build. Mater. 2015, 80, 105–115. [Google Scholar] [CrossRef] [Green Version]
  61. Li, N.; Shi, C.; Zhang, Z. Understanding the roles of activators towards setting and hardening control of alkali-activated slag cement. Compos. Part B Eng. 2019, 171, 34–45. [Google Scholar] [CrossRef]
  62. Sun, Z.; Vollpracht, A. Isothermal calorimetry and in-situ XRD study of the NaOH activated fly ash, metakaolin and slag. Cem. Concr. Res. 2018, 103, 110–122. [Google Scholar] [CrossRef]
  63. Yip, C.K.; Lukey, G.C.; Van Deventer, J.S.J. The coexistence of geopolymeric gel and calcium silicate hydrate at the early stage of alkaline activation. Cem. Concr. Res. 2005, 35, 1688–1697. [Google Scholar] [CrossRef]
  64. Katare, V.D.; Madurwar, M.V. Experimental characterization of sugarcane biomass ash—A review. Constr. Build. Mater. 2017, 152, 1–15. [Google Scholar] [CrossRef]
  65. Cordeiro, G.C.; Toledo Filho, R.D.; Tavares, L.M.; de Moraes Rego Fairbairn, E. Ultrafine grinding of sugar cane bagasse ash for application as pozzolanic admixture in concrete. Cem. Concr. Res. 2009, 39, 110–115. [Google Scholar] [CrossRef]
  66. Jagadesh, P.; Ramachandramurthy, A.; Murugesan, R. Overview on properties of sugarcane bagasse ash (SCBA) as Pozzolan. Indian J. Geo-Mar. Sci. 2018, 47, 1934–1945. [Google Scholar]
  67. Puertas, F.; Palacios, M.; Manzano, H.; Dolado, J.S.; Rico, A.; Rodríguez, J. A model for the C-A-S-H gel formed in alkali-activated slag cements. J. Eur. Ceram. Soc. 2011, 31, 2043–2056. [Google Scholar] [CrossRef]
  68. Redden, R.; Neithalath, N. Microstructure, strength, and moisture stability of alkali activated glass powder-based binders. Cem. Concr. Compos. 2014, 45, 46–56. [Google Scholar] [CrossRef]
  69. Moreira, M.A.N.S.; Heitmann, A.P.; Bezerra, A.C.S.; Patrício, P.S.O.; de Oliveira, L.C.A.; Castro, C.S.; de Souza, P.P. Photocatalytic performance of cementitious materials with addition of red mud and Nb2O5 particles. Constr. Build. Mater. 2020, 259, 119851. [Google Scholar] [CrossRef]
  70. Pereira, A.M.; Moraes, J.C.B.; Moraes, M.J.B.; Akasaki, J.L.; Tashima, M.M.; Soriano, L.; Monzó, J.; Payá, J. Valorisation of sugarcane bagasse ash (SCBA) with high quartz content as pozzolanic material in Portland cement mixtures. Mater. Constr. 2018, 68, e153. [Google Scholar] [CrossRef]
  71. Kolawole, J.T.; Babafemi, A.J.; Fanijo, E.; Chandra Paul, S.; Combrinck, R. State-of-the-art review on the use of sugarcane bagasse ash in cementitious materials. Cem. Concr. Compos. 2021, 118, 103975. [Google Scholar] [CrossRef]
  72. Raheem, A.A.; Abdulwahab, R.; Kareem, M.A. Incorporation of metakaolin and nanosilica in blended cement mortar and concrete- A review. J. Clean. Prod. 2021, 290, 125852. [Google Scholar] [CrossRef]
  73. Criado, M.; Fernández-Jiménez, A.; Palomo, A.; Sobrados, I.; Sanz, J. Effect of the SiO2/Na2O ratio on the alkali activation of fly ash. Part II: 29Si MAS-NMR Survey. Microporous Mesoporous Mater. 2008, 109, 525–534. [Google Scholar] [CrossRef]
  74. Puertas, F.; Martínez-Ramírez, S.; Alonso, S.; Vázquez, T. Alkali-activated fly ash/slag cements. Cem. Concr. Res. 2000, 30, 1625–1632. [Google Scholar] [CrossRef]
  75. Reig, F.B.; Adelantado, J.V.G.; Moya Moreno, M.C.M. FTIR quantitative analysis of calcium carbonate (calcite) and silica (quartz) mixtures using the constant ratio method. Application to geological samples. Talanta 2002, 58, 811–821. [Google Scholar] [CrossRef]
  76. Tchakoute Kouamo, H.; Elimbi, A.; Mbey, J.A.; Ngally Sabouang, C.J.; Njopwouo, D. The effect of adding alumina-oxide to metakaolin and volcanic ash on geopolymer products: A comparative study. Constr. Build. Mater. 2012, 35, 960–969. [Google Scholar] [CrossRef]
  77. Burciaga-Díaz, O.; Magallanes-Rivera, R.X.; Escalante-García, J.I. Alkali-activated slag-metakaolin pastes: Strength, structural, and microstructural characterization. J. Sustain. Cem. Mater. 2013, 2, 111–127. [Google Scholar] [CrossRef]
  78. Fletcher, R.A.; MacKenzie, K.J.D.; Nicholson, C.L.; Shimada, S. The composition range of aluminosilicate geopolymers. J. Eur. Ceram. Soc. 2005, 25, 1471–1477. [Google Scholar] [CrossRef]
  79. Swanepoel, J.C.; Strydom, C.A. Utilisation of fly ash in a geopolymeric material. Appl. Geochem. 2002, 17, 1143–1148. [Google Scholar] [CrossRef]
  80. Magalhães, L.F.D.; França, S.; Oliveira, M.D.S.; Peixoto, R.A.F.; Bessa, S.A.L.; Bezerra, A.C.D.S. Iron ore tailings as a supplementary cementitious material in the production of pigmented cements. J. Clean. Prod. 2020, 274, 123260. [Google Scholar] [CrossRef]
  81. NBR 7215; Cimento Portland—Determinação da Resistência à Compressão de Corpos de Prova Cilíndricos. Associação Brasileira de Normas Técnicas: São Paulo, Brazil, 2019.
  82. NBR 9778; Argamassa e Concreto Endurecidos—Determinação da Absorção de Água, Índice de Vazios e Massa Específica. Associação Brasileira de Normas Técnicas: São Paulo, Brazil, 2009.
Molecules 27 01185 g001 550
Figure 1. Samples of AA pastes (left to right: GM0.6-BA0, GM0.6-BA15, GM0.6-BA30, GM0.6-BA45 and GM1-BA50).
Figure 1. Samples of AA pastes (left to right: GM0.6-BA0, GM0.6-BA15, GM0.6-BA30, GM0.6-BA45 and GM1-BA50).
Molecules 27 01185 g001
Molecules 27 01185 g002a 550Molecules 27 01185 g002b 550
Figure 2. SEM micrograph of AA pastes after 28 days of curing. (a) GMA0.6-BA0, (b) GMA0.6-BA15, (c) GMA0.6-BA30, (d) GMA0.6-BA45, (e) GMA1-BA50.
Figure 2. SEM micrograph of AA pastes after 28 days of curing. (a) GMA0.6-BA0, (b) GMA0.6-BA15, (c) GMA0.6-BA30, (d) GMA0.6-BA45, (e) GMA1-BA50.
Molecules 27 01185 g002aMolecules 27 01185 g002b
Molecules 27 01185 g003 550
Figure 3. Average values of water absorption (a), apparent porosity (p) and bulk density (d) for samples.
Figure 3. Average values of water absorption (a), apparent porosity (p) and bulk density (d) for samples.
Molecules 27 01185 g003
Molecules 27 01185 g004 550
Figure 4. Compressive strength of samples of 7, 28 and 91 days of curing (MPa).
Figure 4. Compressive strength of samples of 7, 28 and 91 days of curing (MPa).
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Molecules 27 01185 g005 550
Figure 5. FTIR spectra for pastes after 28 days of curing.
Figure 5. FTIR spectra for pastes after 28 days of curing.
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Molecules 27 01185 g006 550
Figure 6. XRD pattern of AA paste samples.
Figure 6. XRD pattern of AA paste samples.
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Molecules 27 01185 g007 550
Figure 7. Thermogravimetric analysis of AA paste samples at 91 days.
Figure 7. Thermogravimetric analysis of AA paste samples at 91 days.
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Molecules 27 01185 g008 550
Figure 8. Heat evolution of AA paste samples at 20 °C.
Figure 8. Heat evolution of AA paste samples at 20 °C.
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Molecules 27 01185 g009 550
Figure 9. Visual analysis of (a) MK, (b) BFS and (c) SCBA.
Figure 9. Visual analysis of (a) MK, (b) BFS and (c) SCBA.
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Molecules 27 01185 g010 550
Figure 10. Particle size distribution of the precursors: (a) MK, (b) BFS and (c) SCBA.
Figure 10. Particle size distribution of the precursors: (a) MK, (b) BFS and (c) SCBA.
Molecules 27 01185 g010
Molecules 27 01185 g011 550
Figure 11. XRD patterns of precursors (a) BFS, (b) MK and (c) SCBA.
Figure 11. XRD patterns of precursors (a) BFS, (b) MK and (c) SCBA.
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Figure 12. FTIR image spectra of MK, BFS and SCBA.
Figure 12. FTIR image spectra of MK, BFS and SCBA.
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Molecules 27 01185 g013 550
Figure 13. SEM images of the precursors: (a) MK, (b) BFS and (c) SCBA.
Figure 13. SEM images of the precursors: (a) MK, (b) BFS and (c) SCBA.
Molecules 27 01185 g013
Table
Table 1. Analysis of variance (ANOVA) for the proposed samples and curing time.
Table 1. Analysis of variance (ANOVA) for the proposed samples and curing time.
Source of VariabilitySum of SquaresF Valuep Value
Days of curing12,404.1292.090.000
%SCBA12,434.6195.200.000
%SCBA days of curing5165.040.540.000
Error764.4
Total30,768.0
Table
Table 2. Chemical composition of precursors metakaolin (MK), slag (BFS) and sugarcane bagasse ash (SCBA) (mass%).
Table 2. Chemical composition of precursors metakaolin (MK), slag (BFS) and sugarcane bagasse ash (SCBA) (mass%).
SiO2Al2O3CaOFe2O3MgOK2ONa2OTiO2P2O5LOI
MK60.032.50.11.80.21.60.10.9-2.6
BFS35.35.445.824.33.0-----
SCBA65.813.62.34.51.32.0-0.90.911.5
Table
Table 3. Mix proportion and oxide ratio of the samples.
Table 3. Mix proportion and oxide ratio of the samples.
SampleGBFS/(GBFS + MK)SCBA (%)SiO2: Al2O3CaO: SiO2
GM0.6-BA00.605.260.55
GM0.6-BA150.6155.770.45
GM0.6-BA300.6306.600.40
GM0.6-BA450.6456.850.28
GM1-BA5015010.140.45
GM0-BA500 *505.100.02
* Note: 0% GBFS and 50% MK.
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Sousa, L.N.; Figueiredo, P.F.; França, S.; de Moura Solar Silva, M.V.; Borges, P.H.R.; Bezerra, A.C.d.S. Effect of Non-Calcined Sugarcane Bagasse Ash as an Alternative Precursor on the Properties of Alkali-Activated Pastes. Molecules 2022, 27, 1185. https://doi.org/10.3390/molecules27041185

AMA Style

Sousa LN, Figueiredo PF, França S, de Moura Solar Silva MV, Borges PHR, Bezerra ACdS. Effect of Non-Calcined Sugarcane Bagasse Ash as an Alternative Precursor on the Properties of Alkali-Activated Pastes. Molecules. 2022; 27(4):1185. https://doi.org/10.3390/molecules27041185

Chicago/Turabian Style

Sousa, Leila Nóbrega, Pâmella Fernandes Figueiredo, Sâmara França, Marcos Vinicio de Moura Solar Silva, Paulo Henrique Ribeiro Borges, and Augusto Cesar da Silva Bezerra. 2022. "Effect of Non-Calcined Sugarcane Bagasse Ash as an Alternative Precursor on the Properties of Alkali-Activated Pastes" Molecules 27, no. 4: 1185. https://doi.org/10.3390/molecules27041185

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