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Article

Concrete/Glass Construction and Demolition Waste (CDW) Synergies in Ternary Eco-Cement-Paste Mineralogy

by
Raquel Vigil de la Villa Mencía
1,
Moises Frías
2,
Sagrario Martínez Ramírez
3,
Lucía Fernandez Carrasco
4 and
Rosario García Giménez
1,*
1
Departamento de Geología y Geoquímica, Geomateriales Unidad Asociada CSIC-UAM, Universidad Autónoma de Madrid, 28049 Madrid, Spain
2
Eduardo Torroja Institute for Construction Science (IETcc-CSIC), 28033 Madrid, Spain
3
Institute for the Structure of Matter (IEM-CSIC), 28006 Madrid, Spain
4
Department of Civil and Environmental Engineering, Barcelona TECH, Universitat Politécnica de Catalunya, 08034 Barcelona, Spain
*
Author to whom correspondence should be addressed.
Materials 2022, 15(13), 4661; https://doi.org/10.3390/ma15134661
Submission received: 15 June 2022 / Revised: 29 June 2022 / Accepted: 30 June 2022 / Published: 2 July 2022
(This article belongs to the Section Construction and Building Materials)
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Abstract

:
The study described sought further understanding of the synergies in a mix of CDW pozzolans, containing (calcareous and siliceous) concrete and glass waste, used to prepare ternary eco-cement paste bearing 7% of the binary blend at concrete/glass ratios of 2:1 and 1:2. The mineralogical phases in the 2-day, 28-day, and 90-day cement matrices were identified and monitored using XRF, XRD-Rietveld, SEM-EDX, FT-IR, and NMR. The findings showed that changes in the reaction kinetics in the ternary blended pastes relative to OPC pastes depended on the nature of the recycled concrete and the glass content. Adding the binary mix bearing calcareous concrete (at a ratio of 2:1) favoured ettringite, portlandite, and amorphous phase formation, whilst the blends with siliceous concrete favoured C-S-H gel formation. Monocarboaluminate was detected in the 90-day siliceous concrete and glass pastes in amounts similar to those found in the reference OPC paste.

1. Introduction

Cement manufacture, which accounts for 12% to 15% of all industrial energy consumed worldwide and 5% to 7% of carbon dioxide (CO2) emissions, is one of the priority targets for lowering energy consumption and the generation of greenhouse gases [1].
One avenue for enhancing energy and environmental efficiency, while raising cement sustainability, is to use industrial waste as a partial replacement. Worldwide waste management has come to acquire vital importance, for the steep growth in the demand for natural resources is placing enormous pressure on the environment and society. One outcome has been the coining of new phrases in cement nomenclature such as green cement, the name applied to binders with a low clinker content and smaller carbon footprint than ordinary Portland cement (OPC). All such new eco-cements bear industrial waste as partial cement replacements. In light of their importance, these new cements are being studied as a priority line of research in initiatives such as the European Commission’s circular economy strategies, the European Environment Agency’s Green Deal, the United Nations’ Agenda 2030, and the general pursuit of carbon neutrality by 2050.
Existing European legislation [2] addresses the partial replacement of cement with mineralogical additions from industrial waste, focusing in particular on those exhibiting pozzolanicity and which are consequently usable for the manufacture of binary and ternary eco-cements. Blended cements are known to be mechanically stronger and more durable than unadditioned binders [3,4,5,6].
The vast volumes of construction and demolition waste (CDW) generated globally is one of the types of industrial waste that has attracted the greatest researcher attention in recent years. Such waste is primarily applied as a recycled aggregate in eco-mortar and eco-concrete manufacture, which requires huge quantities of such materials [7,8,9,10,11]. The use of concrete waste as coarse aggregate is presently envisaged in many countries’ structural legislation and codes [12,13,14,15].
Concrete waste is crushed and sieved to different particle size distributions for commercialisation. Coarse aggregate is used for the aforementioned applications as well as for other industrial activities (roads, concretes, embankments), whilst, for want of any industrial use, the fines (< 5mm) are simply stockpiled, unprotected in management plant yards.
A number of research teams [16,17,18,19,20,21], studying the scientific–technical viability of partially replacing cement with such fines, reported no substantial change in end-product chemistry or strength relative to OPC.
Due to their moderate pozzolanicity, further benefit might be drawn from fines if blended with highly pozzolanic mineralogical additions such as silica fume, activated rice-husk ash, bagasse ash, and glass [20,21,22]. Glass is a non-crystalline, non-biodegradable ceramic that owes its high silica content (and indirectly, its properties) to non-crystalline silicates bearing variable amounts of oxides such as CaO, Na2O, K2O, and Al2O3 [23,24]. Approximately 10 Mt of today’s worldwide glass output of 130 Mt [25] end up in landfills.
Soda–lime glass, the predominant type of glass, contains 66% to 75% SiO2, 12% to 17% Na2O, and 6% to 12% CaO [26]. Its high reactive silica content informs its speedy pozzolanic reaction when added to cement, with the formation of secondary C-S-H gels in addition to those generated during anhydrous cement phase hydration [27,28].
Recent studies have attested to the substantial synergies between glass and concrete CDW fines, where the primary hydration product has been identified as C-S-H gels with sodium in their composition. Such products are characterised by a more highly polymerised structure than those generated in the absence of waste [27].
To carry that line of research further, this study explored the synergies between two types of pozzolanic CDWs in a pozzolan/cement system bearing 7% of the addition at concrete/glass ratios of 1:2 and 2:1. The respective pastes were cured up to a total of 90 days. The ternary cements were characterised and the hydrated phases monitored using X-ray fluorescence (XRF), laser granulometry, Rietveld-refined X-ray diffraction (XRD), Fourier-transform infrared spectroscopy (FT-IR), nuclear magnetic resonance spectroscopy (NMR), thermogravimetric analysis/differential thermal analysis (TG/DTA), and scanning electron microscopy/energy dispersive X-ray analysis (SEM/EDX). The respective findings will play a significant role in the microstructure and engineering performance of future eco-mortars and eco-concretes.

2. Materials and Methods

2.1. Materials

Three types of CDW were chosen to prepare binary blends for the ternary cement pastes. Two consisted in fines (<5 mm) stockpiled at management plant yards, one in the region of Madrid, the by-product of processing waste concrete with natural siliceous aggregate (HsT), and the other at a yard in the Basque Country resulting from processing waste concrete from calcareous aggregate (HcG). The third waste was glass collected from a demolition site involving a residential building.
The ternary cement pastes (labelled as shown in Table 1) were prepared with a binder in which 7% of commercial cement type CEM I 42.5R (Cementos Lemona, S.A., Lemoa, Bilbao, Spain) was replaced with the binary blend of recycled CDW pozzolans containing different portions of concrete fines and glass. The 7% replacement ratio was defined on the grounds of previous research [16,27].
The XRF-determined chemical composition of the resulting binders is listed in Table 2 and their particle size distribution parameters are D10, D50, and D90 in Table 3.
Cement matrix hydration reactivity at a constant water/binder ratio of 0.5 was determined on 1 × 1 × 6 cm3 prismatic specimens following Koch–Steinegger methodology. The hydration reaction was detained after 2 days, 28 days, or 90 days by soaking the specimens in acetone for 24 h, followed by vacuum drying for a further 24 h.

2.2. Methods

The majority oxides in the blended and control cements were quantified on pressed wafers with a Philips PW-1404 X-ray fluorescence spectrometer fitted with a Sc-Mo dual anode tube, Philips, Eindhoven, The Netherlands.
Variation in cement TG/DTA was measured in 40 mg to 50 mg samples on a Texas Instruments 600 SDT analyser (New Castle, DE) in a nitrogen atmosphere, ramping the temperature at a rate of 10 °C/min.
Cement fineness was found with dry dispersion laser diffraction particle-size analysis on a Malvern Mastersizer 3000 analyser (Pananalytical, Madrid, Spain) bearing red and blue (He-Ne and LED) light sources. The measuring range was 0.01 µm to 3500 μm.
The mineralogical phases were identified with a PANalytical X’Pert PRO diffractometer (Madrid, Spain) fitted with a copper anode, a 0.5° divergence slit, and 0.5 mm receiving slit, operating at 40 mA and 45 kV. Samples were studied over a 2θ angle range of 5° to 60°. The powder method was applied, using 5% rutile as the internal standard to quantify the crystalline phases, and the proportion of amorphous matter in the samples. Quantification was performed with Match v.3 and Rietveld analysis with Fullprof software (Crystal Impact, Dr. H. Putz & Dr. K. Brandenburg GbR, Bonn, Germany) [29,30]. The mineralogical phases present were identified using Crystallography Open Database (COD) entries as a reference (Table 4).
NMR/MAS scans were recorded with a Bruker Avance-400 spectrometer (Bruker, Kontich, Germany). The recording conditions for the 29Si spectra were: resonance frequency, 79.5 MHz; rotational speed (NMR), 10 kHz; pulse length, 5 s; recycle delay, 10 s; external standard: tetramethylsilane (TMS). The respective conditions for 27Al were: resonance frequency, 104.3 MHz; rotational speed (NMR), 10 kHz; pulse length, 2 s; recycle delay, 5 s; external standard: (H2O)6+3.
Morphological and elemental microanalyses were conducted on an Inspect FEI Company scanning electron microscope (SEM) fitted with an energy dispersive X-ray (EDX) analyser and a Si/Li detector. The semiquantitative chemical analysis values shown are the mean of 10 analyses per spot.
FTIR spectra were recorded with a Bruker Alpha spectrometer operating with a He–Ne laser at a range of 450 cm−1 to 4000 cm−1. The spectroscopy-grade 1% KBr pressed wafers and reference calcined clay samples were stored overnight at 250 °C to remove any adsorbed water.

3. Results

3.1. XRD–Rietveld Analysis

The XRD–Rietveld findings for the cements analysed are provided in Table 5, Table 6 and Table 7. Anhydrous phases C3S, C2S, C3A, C4AFe, and CaCO3 were clearly identified in the original OPC paste, in addition to 8% amorphous matter. Hydrated crystalline phases including C4ACH11 (traces), ettringite (10%), and portlandite (23%) first appeared in the 2-day paste. As those percentages rose over time, the 90-day values for the hydrated phases were traces for C4ACH11, 17–23% for ettringite, and 20–29% for portlandite. The upward pattern was simultaneous with a slight increase in calcite and substantial growth in the amount of amorphous matter (Table 5).
The pastes bearing 1:2 and 2:1 HcG/glass binary blends at a replacement ratio of 7% (Table 6) exhibited the same mineralogical phases as observed in the reference OPC at all ages, although with lower anhydrous phase contents. That fact, along with the rise in the relative concentrations of ettringite, portlandite, and amorphous phase (C-S-H gels), confirmed accelerated hydration due to the filler effect induced by the additions, more prominently in the cement pastes with the smaller proportion of glass (2:1).
The effect of the presence of glass in the blend with the calcareous concrete waste (HcG) could be tracked by monitoring the variation in calcite and the amorphous phase, which declined in the 2:1 blend but rose in the blend with a higher glass content (1:2) [11,21].
From the outset, both (2:1 and 1:2) 7% HsT/glass blends exhibited the same mineralogical phases as the 7% HcG/glass blends, although the amounts forming at each age differed (Table 7). The presence of the binary siliceous blends lowered portlandite and ettringite formation and, beginning in the 28-day pastes, 5% to 7% carboaluminate was detected, whilst the amount of glass added had scarcely any effect. This type of waste was also observed to have a direct effect on the amorphous matter content, which, at 40%, was much higher than in any of the other pastes analysed. That effect denoted the pozzolanicity of siliceous concrete waste, which would enhance C-S-H gel formation within a few minutes of hydration.

3.2. SEM/EDX Morphological Analysis

SEM/EDX exploration identified non-crystalline phases in all the pastes associated with fibrous C-S-H gels which, once formed, served as a growth substrate for ettringite fibres and portlandite plates (Figure 1). All the phases at issue grew in size with time [28].
The 7% HsT/glass sample (Figure 2, left) was observed to be denser, more compact, and less porous than 7% HcG/glass paste (Figure 2, right), which was more porous, particularly between the portlandite plates and ettringite fibres, with the appearance of many interphase voids. The appearance of ettringite occurs throughout the sample and its fibrous nature is what produces the appearance of holes as the entire space is not covered by a steric impediment in growth. It must be taken into account that the observation has been made on a small scale and that it is a reproduction of what happens when the observation is larger.
EDX microanalysis of the C-S-H gels showed both blended pastes to contain aluminium. The C-S-H gels in the 2:1 blends exhibited lower Ca/Si and Al/Si ratios than found in OPC gels (Table 8), although the difference was narrower in the pastes’ calcareous concrete waste (7% HcG/glass). Those findings denote silicon uptake in the C-S-H gels, more notably in the pastes prepared with siliceous concrete waste.

3.3. TG/DTA Analysis

The variations in the TG/DTA thermogravimetric readings for the 28-day and 90-day ternary hydrated cements are depicted in Figure 3. All the pastes exhibited very similar thermal behaviour, with three distinct endothermal zones. A first was recorded at 50 °C to 300 °C, temperatures typically associated with the dehydroxylation of the main hydrated phases, formed during cement hydration, as well as with the pozzolanic reaction [29]. The most prominent band in this zone (112 °C) would be attributable to C-S-H gel dehydroxylation, whilst ettringite would dehydroxylate at <100 °C, the bound water in carboaluminate at 155 °C, and carboaluminate at 180 °C to 210 °C. A third small endothermal band at 370 °C to 375 °C was also identified with C-S-H gel dehydroxylation.
The second endothermal zone, stretching from 400 °C to 550 °C and peaking at 463 °C, was typical of portlandite dehydroxylation and the third, at 550 °C to 750 °C with a peak close to 720 °C, of carbonate decarbonation [31].
By the TG/DTA analysis, all the 28-day and the 90-day cement pastes were similar, irrespective of the binary blend added. At 28 days, only a minor difference was observed in the endothermal range 50 °C/400 °C, where the OPC paste had a greater mass loss than the ternary pastes, possibly as a result of the dilution effect and low (HsT and HcG) CDW activity [11]. In the 90-day samples, the TG/DTA curves were nearly identical with no qualitatively perceptible differences.
The mass loss recorded from the TG/DTA curves at temperature intervals 50/400 °C, 400/550 °C, and 550/750 °C is listed in Table 9, which also gives the relative portlandite content of each sample, given the 7% replacement of the reference OPC.
According to the data in Table 9, mass loss in the ternary cements was slightly lower than in the OPC at 50 °C to 400 °C (C-S-H, ettringite and Ca(OH)2 dehydroxylation), with a somewhat wider difference at 28 days. That observation was related to the filler effect and low pozzolanicity of the binary blends, for the Ca(OH)2 values (400 °C to 550 °C) were practically the same. The effect was corroborated by the relative (to OPC) portlandite content values, which were greater (positive values) than they should have been after replacing 7% OPC with the additions at hand. The relative portlandite content was higher in the ternary pastes where glass prevailed (1:2) in the binary blend than where concrete waste prevailed (2:1). That observation would be related to portlandite insolubility, intensified by the uptake from the medium of the sodium ions present in the recycled glass [22].
Weight loss was greater at 50 °C to 400 °C in the 90-day materials, in keeping with the formation of more C-S-H gel with hydration time. Whilst loss was greater in the 28-day OPC than in the 28-day blended cements, the 90-day values were similar, denoting gel formation during the pozzolanic reaction.

3.4. FTIR Analysis

The results on hydration as monitored with FTIR (Figure 4) corroborated the XRD findings, while adding no further information on amorphous phase formation. The Si-O tetrahedral group bending vibrations peaking at 452 cm−1 and the same group’s stretching vibrations at 900 cm−1 to 1000 cm−1 denoted the presence of silicates. The samples with the 2:1 replacement exhibited the highest proportion of hydrated phase, attested to by the relative intensity of the portlandite bands at approximately 3645 cm−1 and the bands at approximately 3443 cm−1 associated with the OH groups in C-S-H gels. The 1:2 sample blends exhibited more intense carbonate (primarily calcite)-induced bands at 1414 cm−1 and 874 cm−1 [31] and a less intense band associated with portlandite OH groups (3645 cm−1), perhaps indicating its partial carbonation.
In another vein, Gismera et al. [32] contended that monocarboaluminate was present, attributing the signal at 3540 cm−1 to its OH groups. The wide signal with a small peak observed in this study may have been indicative of such a presence.

3.5. NMR Analysis

The 29Si NMR spectra for the 90-day blended cements containing 7% HcG/glass or HsT/glass at ratios of 2:1 or 1:2 are reproduced in Figure 5. Signals denoting the presence of the initial (anhydrous) Q0 units as well as the Q1 (-71ppm), Q2(1Al) (−81.5 ppm), and Q2 (−85 ppm) units found in the C-S-H gel [33] were present in all. The signal at −81.5ppm denoting Al uptake by the C-S-H gel was more intense in the 7% HsT (1:2) than in the 7% HcG (1:2) paste.
Table 10 compares the Qn content and mean chain length (MCL) values for the ternary pastes drawn from the deconvoluted 29Si NMR spectra with the data for OPC published in an earlier paper [27].
The lower intensity of the Q0 signals associated with the initial anhydrous phases in the ternary pastes than in OPC was a sign of higher reactivity in the former. All the blended pastes took Al up into their C-S-H gels, an effect more prominent in the materials prepared with (1:2) HcG/glass and (2:1) HsT/glass, which were also the gels with the longest chain lengths. Al uptake into C-S-H gel depends on the amount of dissolved Al, Ca, and Si, as well as on the pH of the porous solution [34,35]. The presence of alkaline ions such as Na may also favour Al uptake in the gel to balance the charge difference between Al and the Si it replaces [36], possibly associated with the higher Na content in the waste than in OPC. Al(IV), taken up into silicate tetrahedra bridging sites, prevails at low Ca/Si ratios, whereas high Ca/Si ratios (approximately above 1.2) result in larger fractions of Al(V) and Al(VI), species associated with the C-(A)-S-H structure [33].
The 27Al NMR spectra for the 7% blended cements reproduced in Figure 6 exhibit clearly distinguishable Al(VI) and Al(IV) signals. All the pastes generated two Al(VI) signals, one at 13.4ppm attributed to ettringite and the other at 8.7ppm to calcium monocarboaluminate hydrate [36].
In addition, the 27Al NMR spectrum for the paste bearing siliceous concrete waste (HsT) exhibited a signal at 56 ppm attributed to non-reactive tecto- and phyllo-silicates [16], whilst the signal at 68 ppm was associated with the Al(IV) found in silicate chain bridging sites [37].
Samples with limestone residue have higher Imonocar/Iett values, indicating that they contain a higher percentage of carbonate phases. In the case of samples with siliceous residue, however, the ratio is lower, indicating a higher ettringite content. In the study carried out on the OPC samples with a single residue (HcG or HsT), it was observed that if the residue was HcG, what was formed was aluminates or carboaluminates in addition to ettringite, but if the residue added was of a siliceous nature (HsT), only ettringite was formed. In these samples, in which glass is added in addition to the limestone or siliceous residue, what is observed is that the formation of aluminates or carboaluminates is favoured in both cases (Figure 7).

4. Discussion

The synergies in a blend of pozzolans present in (calcareous and siliceous) waste concrete fines with recycled CDW glass were analysed in depth in the study reported in this article.
Ettringite and portlandite were the hydrated phases identified in the reference OPC paste. Their content, along with the amounts of C-S-H gels, rose with reaction time.
Partially replacing OPC with 7% of the binary blend, either HcG/glass or HsT/glass at ratios of 2:1 or 1:2, had no qualitative effect on the mineralogical phases produced with cement hydration. Quantitative changes were nonetheless observed. In the pastes with the higher HcG/glass ratio (2:1), ettringite, portlandite, and amorphous phase formation was enhanced, whereas in the pastes containing siliceous concrete (HsT/glass) C-S-H gel formation was favoured. In both cases, higher glass contents (1:2) delayed hydration, with a concomitant decline in the relative amounts of reaction product.
Cement hydration yielded portlandite as the primary reaction product, although the type of CDW used conditioned the content of the mineral and its variation over time. Portlandite content was higher in the blends containing calcareous waste and glass than in OPC at all ages. Hydration was accelerated in the 28-day materials in particular due to the filler effect prompted by the waste [16]. At later ages (90 days), the presence of glass at whichever proportion (2:1 or 1:2) delayed hydration due to the decline in portlandite solubility as a result of the sodium in the medium [37,38], which neutralised the pozzolanic effect in the binary blends of CDW. The pastes with siliceous concrete were slightly more pozzolanic than the ones with calcareous waste at both ratios (Table 9).
Ettringite, in turn, is highly sensitive to the composition of the medium, depending primarily on the presence of sulfur, pH, and calcite content. This phase usually forms by non-uniform nucleation on C-S-H gel substrates in the presence of sulfur ions [39,40], whilst the presence of calcite in the medium, which prevents its conversion to monosulfoaluminate, favours stabilisation [41].
Here, due to the presence of calcite in the waste itself, a component absent from OPC, the ettringite precursor monocarboaluminate was observed to form in all the blended pastes. This is consistent with earlier research [42], according to which a higher content of this phase, ettringite, was found in pastes prepared with calcareous concrete waste.
The type of CDW used in the cement pastes modified C-S-H gel composition relative to the gel found in OPC paste. The presence of the waste favoured silicon uptake in the C-S-H gels, as attested to by the shift in the 29Si NMR signals, most prominently in the mixes containing HsT/glass where the Ca/Si and Al/Si ratios declined (Table 8). Al uptake into the C-S-H gel, observed in both the OPC and all the blended pastes analysed but especially in the material (2:1) HsT/glass, tended to lengthen the respective chains, which would explain the fibre-like structure visible in the SEM micrographs.

5. Conclusions

Adding calcareous or siliceous waste concrete/waste glass blends to cement pastes affects the proportion although not the nature of the mineralogical phases present in the hydration product. Pastes bearing calcareous concrete waste (HcG/glass ratio) enhance ettringite, portlandite, and amorphous phase formation, whereas the generation of C-S-H gels is favoured in pastes containing siliceous concrete (HsT/glass). In both cases, higher glass contents (1:2) delay hydration, with a concomitant decline in the relative amounts of reaction product. In the mixes bearing glass waste, the presence of calcite determines the formation of the ettringite precursor monocarboaluminate, which also acts as calcareous filler. The nature of the waste affects C-S-H gel composition, with a decline of approximately 36% to 44% in the Ca/Si and 50% to 76% in the Al/Si ratios.
Despite the scientific advances reported here, further research is needed to analyse the effect of such microstructural changes on ternary eco-cement mechanical strength and durability.

Author Contributions

Conceptualization, R.V.d.l.V.M., M.F. and R.G.G.; Data curation, L.F.C.; Formal analysis, M.F. and S.M.R.; Methodology, R.G.G.; Software, S.M.R.; Supervision, R.G.G.; Validation, R.V.d.l.V.M., L.F.C. and R.G.G.; Writing—original draft, R.V.d.l.V.M., M.F., S.M.R. and R.G.G.; Writing—review & editing, R.V.d.l.V.M., M.F. and R.G.G. All authors have read and agreed to the published version of the manuscript.

Funding

This research was conducted under a national project (grant number RTI2018-097074- B-C21 and C-22) funded by the Spanish Ministry of Science, Innovation, and Universities (MICIU), the Spanish National Research Agency (AEI), and the European Regional Development Fund (ERDF).

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Acknowledgments

The authors gratefully acknowledge the support received from the Spanish Construction and Demolition Waste Recycling Association (RCDA), the Spanish Institute of Cement and its Applications (IECA), and the Madrid Institute of Materials Science (ICMM-CSIC).

Conflicts of Interest

The authors declare no conflict of interest.

References

  1. Stafford, F.N.; Dias, A.C.; Arroja, L.; Labrincha, J.A.; Hotza, D. Life cycle assessment of the production of Portland cement: A Southern Europe case study. J. Clean. Prod. 2016, 126, 159–165. [Google Scholar] [CrossRef]
  2. European Standard EN 197-1; Cement-Part 1: Composition, Specifications and Conformity Criteria for Common Cements. CEN: Brussels, Belgium, 2011.
  3. Castro, M.I.; de Silva, J.H. Effect of nanosilica/MK ratio on the calcium aluminate silicate hydrate (CASH) formed in ternary cement pastes. J. Build. Engin. 2021, 38, 102220. [Google Scholar]
  4. Xu, G.; Shi, X. Characteristics and applications of fly ash a sustainable construction material: A state of art review. Resour. Conserv. Recycl. 2018, 136, 95–109. [Google Scholar] [CrossRef]
  5. Snelson, D.G.; Wild, S.; O’Farrell, M. Heat of hydration of Portland cement-MK-FA blendeds. Cem. Concr. Res. 2008, 38, 832–840. [Google Scholar] [CrossRef]
  6. Abdelmelek, N.; Lubloy, E. Flexural strength of silica, fly ash and metakaolin of hardened cement paste after exposure to elevated temperatures. J. Therm. Anal. Calor. 2022, 14, 7159–7169. [Google Scholar] [CrossRef]
  7. Vieira, J.P.B.; Correira, J.R.; de Brito, J. Post fire residual mechanical properties of concrete made with recycled concrete coarse aggregates. Cem. Concr. Res. 2011, 41, 533–541. [Google Scholar] [CrossRef]
  8. Medina, C.; Sánchez de Rojas, M.I.; Thomas, C.; Polanco, J.A.; Frías, M. Durability of recycled concrete made with recycled ceramic sanitary ware aggregate. Inter-indicator relationships. Constr. Build. Mater. 2016, 105, 480–486. [Google Scholar] [CrossRef]
  9. Dimitriou, G.; Savva, P.; Petrou, M. Enhancing mechanical and durability properties of recycled aggregate concrete. Constr. Build. Mater. 2018, 158, 228–235. [Google Scholar] [CrossRef]
  10. Infante, R.; Brazao, C.; Veiga, R.; de Brito, J.; Faria, P.; Bastos, D. CO2 sequestration by CDW aggregates and effect on mortars and concrete performance- An overview. Renew. Sustain. Energy Rev. 2021, 152, 111668. [Google Scholar] [CrossRef]
  11. Plaza, P.; Saéz del Bosque, I.F.; Frías, M.M.; Sánchez de Rojas, M.I.; Medina, C. Use of recycled coarse and fine aggregates in structural eco-concretes. Physical and mechanical properties and CO2 emissions. Constr. Build. Mater. 2021, 285, 122926. [Google Scholar] [CrossRef]
  12. Real Decreto 470/2021 Sobre el Código Estructural; Ministerio de la Presidencia, Relaciones de la Cortes y Memoria Democrática: Boletín Oficial del Estado n. 190: Madrid, Spain, 2021.
  13. ACI 130R-19: Report on the Role of Materials in Sustainable Concrete Construction; American Concrete Institute: Farmington Hills, MI, USA, 2019.
  14. Standard DIN 4226-101; Recycled Aggregates for Concrete in Accordance with DIN EN 12620-Part 101: Types and Regulated Dangerous Substances. German Institute for Standardization: Belin, Germany, 2017.
  15. Standard BS 8500-2; Concrete-Complementary British Standard to BS EN 206. Specification for Constituent Materials and Concrete (+A2:2019). Britihs Standards Institution: London, UK, 2015.
  16. Frias, M.; Vigil de la Villa, R.; Martínez-Ramírez, S.; Fernández Carrasco, L.; Villar-Cociña, E.; García-Giménez, R. Multi-Technique Characterization of a Fine Fraction of CDW and Assessment of Reactivity in a CDW/Lime System. Minerals 2020, 10, 590. [Google Scholar] [CrossRef]
  17. Moreno, J.; Vegas, I.; Frías, M.; Vigil, R.; Guede, E. Laboratory-scale study and semi-industrial validation of viability of inorganic CDW fine fractions as SCMs in blended cements. Constr. Build. Mater. 2021, 271, 121823. [Google Scholar] [CrossRef]
  18. Caneda, L.; Monasterio, M.; Moreno, J.; Martínez, S.; García, R.; Frías, M. Behaviour and Properties of eco-cement pastes elaborated with recycled concrete powder from construction and demolition wastes. Materials 2021, 14, 1299. [Google Scholar] [CrossRef] [PubMed]
  19. Frías, M.; Martínez, S.; Vigil, R.; Fernández, L.; García, R. Reactivity in cement pastes bearing fine fraction concrete and glass from construction and demolition Waste: Microstructural analysis of viability. Cem. Concr. Res. 2021, 148, 106531. [Google Scholar] [CrossRef]
  20. Aprianti, E.; Shafigh, P.; Bahri, S.; Nodek, J. Supplementary cementitious materials origin from agricultural wastes-A review. Constr. Build. Mater. 2015, 74, 176–187. [Google Scholar] [CrossRef] [Green Version]
  21. Liu, G.; Florea, M.V.A.; Brouwers, H.J.H. The hydration and microstructure characteristics of cement pastes with high volume organic contaminated waste glass powder. Constr. Build. Mater. 2018, 187, 1177–1189. [Google Scholar] [CrossRef]
  22. Sanchez de Rojas, M.I.; Frías, M. The pozzolanic activity of different Materials, its influence on the hydration heat in mortars. Cem. Concr. Res. 1996, 26, 203–213. [Google Scholar] [CrossRef]
  23. Mohajerani, A.; Vajna, J.; Ho, T.; Cheung, H.; Kurmus, H.; Arulrajah, A.; Horpibulsuk, S. Practical recycling applications of crushed waste glass in construction materials: A review. Constr. Build. Mater. 2017, 156, 443–467. [Google Scholar] [CrossRef]
  24. Corinaldesi, V.; Gnappi, G.; Montenero, A. Reuse of ground waste glass as aggregate for mortars. Waste Manage 2005, 25, 197–201. [Google Scholar] [CrossRef]
  25. Wang, H.Y. A study of the effects of LCD glass sand on the properties of concrete. J. Waste Manage 2009, 29, 33541. [Google Scholar] [CrossRef]
  26. Aliabdo, A.S.A.; Elmoaty, A.; Aboshama, A.Y. Utilization of Waste glass powder in the production of cement and concrete. Constr. Build. Mater. 2016, 124, 866–877. [Google Scholar] [CrossRef]
  27. Vigil de la Villa, R.; Frías Rojas, M.; Martínez-Ramírez, S.; Fernández Carrasco, L.; Villar Cociña, E.; García Giménez, R. Reactivity of Binary Construction and Demolition Waste Mix as Supplementary Cementitious. Materials 2021, 14, 6481. [Google Scholar]
  28. Frías, M.; Martínez-Ramírez, S.; Vigil de la Villa, R.; García-Giménez, R.; Sánchez de Rojas, M.I. New scientific evidence of the effect of high temperatures and long curing times on MK-blended cements paste mineralogy. Cem. Concr. Res. 2022, 152, 106657. [Google Scholar] [CrossRef]
  29. Rodriguez-Carvajal, J. Recent advances in magnetic structure determination by neutron powder diffraction. Physica B 1993, 55, 192–199. [Google Scholar] [CrossRef]
  30. Young, R.A. The Rietveld Method; International Union of Crystallography: Chester, UK; Oxford University Press: Oxford, UK, 1995. [Google Scholar]
  31. Lin, W.; Zhou, F.; Luo, W.; You, L. Recycling the waste dolomite powder with excellent consolidation properties: Sample synthesis, mechanical evaluation, and consolidation mechanism analysis. Constr. Build. Mater. 2021, 290, 123198. [Google Scholar] [CrossRef]
  32. Gismera-Diez, S.; Manchobas-Pantoja, B.; Carmona-Quiroga, P.M.; Blanco-Varela, M.T. Effect of BaCO3 on C3A hydration. Cem. Concr. Res. 2015, 73, 70–78. [Google Scholar] [CrossRef] [Green Version]
  33. Yang, S.; Yan, Y.; Lothenbach, B.; Skibsted, J. Incorporation of Sodium and Aluminum in Cementitious Calcium-Alumino-Silicate-Hydrate C-(A)-S-H Phases Studied by 23Na, 27Al, and 29Si MAS NMR Spectroscopy. J. Phys. Chem. C 2021, 125, 27975–27995. [Google Scholar] [CrossRef]
  34. Pardal, X.; Pochard, I.; Nonat, A. Experimental Study of Si–Al Substitution in Calcium-Silicate-Hydrate (C-S-H) Prepared under Equilibrium Conditions. Cem. Concr. Res. 2009, 39, 637−643. [Google Scholar] [CrossRef]
  35. L’Hôpital, E.; Lothenbach, B.; Le Saout, G.; Kulik, D.; Scrivener, K. Incorporation of Aluminium in Calcium-Silicate-Hydrates. Cem. Concr. Res. 2015, 75, 91−103. [Google Scholar] [CrossRef]
  36. Skibsted, J.; Andersen, M.D. The Effect of Alkali Ions on the Incorporation of Aluminium in the Calcium Silicate Hydrate (C-S-H) Phase Resulting from Portland cement Hydration Studied by 29Si MAS NMR. J. Am. Ceram. Soc. 2013, 96, 651−656. [Google Scholar] [CrossRef]
  37. Dai, Z.; Tran, T.; Skibsted, J. Aluminum Incorporation in the C-S-H Phase of White Portland Cement−Metakaolin Blends Studied by 27Al and 29Si MAS NMR Spectroscopy. J. Am. Ceram. Soc. 2014, 97, 2662−2671. [Google Scholar] [CrossRef]
  38. Elaqra, H.; Rustom, R. Effect of using glass powder as cement replacement on rheological and mechanical properties of cement paste. Constr. Build. Mater. 2018, 179, 326–335. [Google Scholar] [CrossRef]
  39. Georgin, J.F.; Maach, N.; Pommay, J. Sulphate crystallization modelling and surface reactivity in solution. Constr. Build. Mater. 2017, 156, 266–276. [Google Scholar] [CrossRef]
  40. Danielik, V.; Fellner, P.; Králik, M.; Baďrová, B.; Gabčová, J.; Jurišová, J.; Foltinovič, T. Relation between the reactivity and surface area of gypsum. J. Mol. Liq. 2019, 283, 763–771. [Google Scholar] [CrossRef]
  41. Shi, C.; Zhang, G.; He, T.; Li, Y. Effects of superplasticizers on the stability and morphology of ettringita. Constr. Build. Mater. 2016, 112, 261–266. [Google Scholar] [CrossRef]
  42. Martin, L.H.J.; Winnefeld, F.; Müller, C.J.; Lothenbach, B. Contribution of limestone to the hydration of calcium sulfoaluminate cement. Cem. Concr. Comp. 2015, 62, 204–211. [Google Scholar] [CrossRef]
Materials 15 04661 g001 550
Figure 1. (Left) C-S-H gels, portlandite, and ettringite filling cracks. (Right) Detail of C-S-H gel fibres and portlandite formation on the gel.
Figure 1. (Left) C-S-H gels, portlandite, and ettringite filling cracks. (Right) Detail of C-S-H gel fibres and portlandite formation on the gel.
Materials 15 04661 g001
Materials 15 04661 g002 550
Figure 2. (Left) Detail of (2:1) blend compaction. (Right) HcG/glass cement.
Figure 2. (Left) Detail of (2:1) blend compaction. (Right) HcG/glass cement.
Materials 15 04661 g002
Materials 15 04661 g003 550
Figure 3. TG/DTA curves at 28 and 90 days of treatment from ternary hydrated cement.
Figure 3. TG/DTA curves at 28 and 90 days of treatment from ternary hydrated cement.
Materials 15 04661 g003
Materials 15 04661 g004 550
Figure 4. IR spectra for 90 days of blended cements.
Figure 4. IR spectra for 90 days of blended cements.
Materials 15 04661 g004
Materials 15 04661 g005 550
Figure 5. 29Si NMR spectra for 90-day 7% HsT/glass and HcG/glass pastes.
Figure 5. 29Si NMR spectra for 90-day 7% HsT/glass and HcG/glass pastes.
Materials 15 04661 g005
Materials 15 04661 g006 550
Figure 6. 27Al NMR spectra for 90-day 7% HsT/glass pastes.
Figure 6. 27Al NMR spectra for 90-day 7% HsT/glass pastes.
Materials 15 04661 g006
Materials 15 04661 g007 550
Figure 7. Ratio of the intensities of the 27Al NMR signals for monocarboaluminate and ettringite (8/13.4).
Figure 7. Ratio of the intensities of the 27Al NMR signals for monocarboaluminate and ettringite (8/13.4).
Materials 15 04661 g007
Table
Table 1. Cement nomenclature.
Table 1. Cement nomenclature.
CementOPC (wt. %)HsT (wt. %)HcG (wt. %)Glass (wt. %)
OPC100000
7% HsT/G 1:2932.3304.67
7% HsT/G 2:1934.6702.33
7% HcG/G 1:29302.334.67
7% HcG/G 2:19304.672.33
Table
Table 2. FRX-determined chemical composition (%) of the cements studied (LOI = loss on ignition).
Table 2. FRX-determined chemical composition (%) of the cements studied (LOI = loss on ignition).
(%)OPC7% HsT/G 1:27% HsT/G 2:17% HcG/G 1:27% HcG/G 2:1
SiO214.2216.6915.2817.6317.16
Al2O32.892.802.842.943.13
CaO69.8166.5367.4765.8066.00
Fe2O33.703.513.513.543.57
MgO0.931.061.001.061.01
SO33.363.163.173.193.25
Na2O0.330.920.620.940.65
K2O0.760.730.740.800.87
P2O50.140.130.130.130.14
TiO20.200.190.190.200.20
LOI3.223.784.543.283.54
Table
Table 3. D10, D50, and D90 values (µm) for the cements studied.
Table 3. D10, D50, and D90 values (µm) for the cements studied.
OPC7% HsT/G 1:27% HsT/G 2:17% HcG/G 1:27% HcG/G 2:1
D102.072.041.941.971.95
D5011.411.410.911.110.9
D9034.834.833.934.634.2
Table
Table 4. Crystallography Open Database (COD) files used for Rietveld quantification.
Table 4. Crystallography Open Database (COD) files used for Rietveld quantification.
MineralFile Number
Alite992,000,105
Belite99,200,096
Calcite992,000,080
Al2Ca3O6992,000,100
Portlandite992,000,046
Ettringite992,000,085
C4ACH11992,000,037
Table
Table 5. Mineralogical composition of OPC paste (XRD–Rietveld).
Table 5. Mineralogical composition of OPC paste (XRD–Rietveld).
Phase (%)Initial2 Days28 Days90 Days
Alite522814traces
Belite2015105
C3A95tracestraces
C4AF65tracestraces
Calcite571411
Ettringiten.d.5810
Portlanditetraces172628
C4ACH11tracestraces58
A. matter 8182338
Total100100100100
RB12.314.510.69.7
χ27.98.37.67.5
n.d. = not detected; A. matter = amorphous matter; RB and χ2, agreement factors.
Table
Table 6. Mineralogical composition of 7 % HcG/glass paste.
Table 6. Mineralogical composition of 7 % HcG/glass paste.
Phase (%)(1:2) 2d(2:1) 2d(1:2) 28d(2:1) 28d(1:2) 90d(2:1) 90d
Alite67n.d.n.d.n.d.n.d.
Belite55n.d.n.d.n.d.n.d.
C3Atracestracesn.d.n.d.n.d.n.d.
C4AFn.d.n.d.n.d.n.d.n.d.n.d.
Calcite252326162514
Portlandite233427383039
Ettringite101115231723
C4ACH11tracestracestracestracestracestraces
A. matter312032232824
Total100100100100100100
RB16.812.215.813.719.816.3
χ25.77.17.96.88.38.5
n.d. = not detected; A. matter = amorphous matter; RB and χ2, agreement factors.
Table
Table 7. Mineralogical composition of 7% Hst/glass paste.
Table 7. Mineralogical composition of 7% Hst/glass paste.
Phases (%)(1:2) 2d(2:1) 2d(1:2) 28d(2:1) 28d(1:2) 90d(2:1) 90d
Alite75n.d.n.d.n.d.n.d.
Belite5tracesn.d.n.d.n.d.n.d.
C3Atracestracesn.d.n.d.n.d.n.d.
C4AFn.d.n.d.n.d.n.d.n.d.n.d.
Calcite383839363033
Portlandite91115171924
Ettringitetraces557510
C4ACH11n.d.n.d.n.d.traces57
A. matter414141404126
Total100100100100100100
RB19.615.417.819.318.921.3
χ27.78..76.48.66.89.7
n.d. = not detected; A. matter = amorphous matter; RB and χ2, agreement factors.
Table
Table 8. 90-day OPC and C-S-H gel ratios.
Table 8. 90-day OPC and C-S-H gel ratios.
OPC7% HcG/Glass (2:1)7% HsT/Glass (2:1)
Al2O3/SiO20.460.230.11
CaO/SiO23.682.372.06
Table
Table 9. Mass loss (%) by temperature range and relative Ca(OH)2 content (%) in the pastes studied.
Table 9. Mass loss (%) by temperature range and relative Ca(OH)2 content (%) in the pastes studied.
%50/400 °C (H2O)400/550 °C (H2O)550/750 °C (CO2)Rel. Ca(OH)2
OPC 28d16.255.052.660
OPC 90d18.405.092.340
7% HcG 1-2 28d14.505.012.70+6.7
7% HcG 1-2 90d18.655.032.75+6.3
7% HcG 2-1 28d14.315.063.24+5.7
7% HcG 2-1 90d17.904.943.13+4.4
7% HsT 1-2 28d14.234.912.71+4.6
7% HsT 1-2 90d17.215.052.17+6.6
7% HsT 2-1 28d14.144.862.93+3.5
7% HsT 2-1 90d18.054.922.47+4.0
Table
Table 10. 90-day Qn signal deconvolution and MCL compared with OPC.
Table 10. 90-day Qn signal deconvolution and MCL compared with OPC.
OPCHcG (1:2)HcG (2:1)HsT (1:2)HsT (2:1)
Q015.208.204.405.105.20
Q147.6032.3039.3039.0037.10
Q2 (1Al)1.7021.1017.2019.0022.90
Q235.5038.4039.1036.9034.90
MCL3.566.345.315.355.73
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Vigil de la Villa Mencía, R.; Frías, M.; Ramírez, S.M.; Carrasco, L.F.; Giménez, R.G. Concrete/Glass Construction and Demolition Waste (CDW) Synergies in Ternary Eco-Cement-Paste Mineralogy. Materials 2022, 15, 4661. https://doi.org/10.3390/ma15134661

AMA Style

Vigil de la Villa Mencía R, Frías M, Ramírez SM, Carrasco LF, Giménez RG. Concrete/Glass Construction and Demolition Waste (CDW) Synergies in Ternary Eco-Cement-Paste Mineralogy. Materials. 2022; 15(13):4661. https://doi.org/10.3390/ma15134661

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Vigil de la Villa Mencía, Raquel, Moises Frías, Sagrario Martínez Ramírez, Lucía Fernandez Carrasco, and Rosario García Giménez. 2022. "Concrete/Glass Construction and Demolition Waste (CDW) Synergies in Ternary Eco-Cement-Paste Mineralogy" Materials 15, no. 13: 4661. https://doi.org/10.3390/ma15134661

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