A type I ordinary Portland cement, ASTM C150 (C), a ground granulated blast-furnace slag (S) and white bottle glass (G) powder were used to prepare blended cement for this study. The chemical composition of C, obtained by X-ray fluorescence spectrometry, is reported in Table 1. The mineralogical composition of C, calculated by Bogue formulas, was C₃S: 60 %, C₂S: 16.4 %, C₃A: 3.8 %, C₄AF: 11.5%. The chemical composition of S and G are also given in Table 1 and determined by Inductively Coupled Plasma Atomic Emission Spectroscopy (ICP-AES) analysis. The mineralogical composition was identified by X-ray diffraction (XRD) and FTIR spectroscopy (FTIR). XRD analysis was performed using a Philips PW 3710 diffractometer operating with Cu Kα radiation at 40 kV and 20 mA and the FTIR spectra were performed on NICOLET Magna 550 using KBr technique.

The physical characteristics of all materials (density, absorption, specific surface, retained on sieve and particle size distribution d10, d50, and d90) also appear in Table 1. According to Table 1 and Figure 1, C has high density and particle size distribution with large volume of particles, bigger than the S and the G. Glass powder has the smallest ones. Having different particle size distribution favors packaging of mixtures, reducing empty spaces and increasing packing density (12). Management of these parameters is vital to obtain more resistant and more durable concretes.

XRD (Figure 2a) analysis of S and G shows absence of crystalline compounds. Only a diffuse band in 15-40º 2θ was observed assigned to amorphous silicate from G and another diffuse band centred at 2θ = 30º assigned to melillite, from S. Characterization of G and S through FTIR techniques can be seen in Figure 2b.

FTIR spectra of S show a broad band in 962 cm^-1 characteristic of asymmetric stretching vibration bands of Si-O in the silicate tetrahedrons, broadening and shifted to lower frequency, typical of IR spectra of glass phases (13). Vibration bands in 508 cm^-1 are assigned to deformation vibration of silicate O-Si-O and the other between 600-800 cm^-1 at asymmetric stretching vibration of Al-O bonds of AlO₄ (14). The bands near 1400 cm^-1 were assigned to CO₃^-2 group present by the partial carbonation of slag.

FTIR assignment of G is also performed on the basis of SiO₄^4- tetrahedron, which in this case has symmetry smaller than Td. The Si-O-Si stretch vibration, coupled with other vibrators of the structure, is between: 700-1200 cm^-1. The vibration of deformation O-Si-O is in the region 400-500 cm^-1 (15).

The reference slag blended cement was in proportion 30:70 (C:S) and then the S was replaced in 10 and 20% by mass with G. Table 2 shows the name given to each sample and its composition. Slag cement, hydrated in the presence of Na(OH) solution, was used as comparison in order to establish the alkaline activation capacity of the ground glass at early age.

The rate of heat evolution and the cumulative heat released during early hydration (first 48 hours) of different pastes (w/b = 0.5) were registered by isothermal conduction calorimetry at 20 ºC.

The workability of mortar was determined using the flow table test according to ASTM C1437 (16) as the diameters of spread mortar were measured along four lines and were expressed in percentage. Mortars were cast in 40 x 40 x 160 mm moulds and then compacted in two layers, covered with plastic sheet to prevent water loss and stored at 20 ± 2 °C. Standard siliceous sand and w/b= 0.50 were used. After 24 h, specimens were removed from the moulds and tightly covered with plastic sheets and stored until the test age was reached. From different blended cements, compressive strength was determined at 2, 7, 28 and 90 days. The reported results are the average of six compression tests.

The hydration of the pastes at 2, 7 and 28 days was analyzed by FTIR spectroscopy and the identification of hydration phases was carried out. Pozzolanic activity was determined by Frattini test according to the procedure described in EN196-5 at 2, 7 and 28 days (17). This test evaluates the pozzolanic activity of blended cements measuring their reaction with the Ca(OH)₂ released during cement hydration. The result is considered positive when the points are located below the calcium hydroxide solubility isotherm at 40 °C.

Figure 3 shows the heat release curves (mW/g) and the total heat (J/g) for C and blended cement pastes with addition of 10 and 20% powder glasses (CG10 and CG20). Table 3 shows information on singular points of the curves.

The rate of heat release declined and the intensity of the heat signal declined as the glass content grew. An increase in the dormant period and a delay in the occurrence of the second and third peaks in approximately 180 minutes were also observed.

As a consequence, the total heat released in the first 48 hours of hydration was lower and corresponded to 82 and 75% of the C heat (133.75 J/g) for the CG10 and CG20 blended cements, respectively.

Figure 4 shows the heat release curves (mW/g) and the total heat (J/g) for CSG0 and blended cement pastes with addition of 10 and 20% powder glasses (CSG10 and CSG20). Table 4 shows information on singular points of the curves.

Replacement of cement by 70% slag (CSG0) produced a general reduction of the heat release and extended the dormant period, generating a total heat equivalent to 35% of the reference C (133.75 J/g) at 48 hours of hydration. (Figure 4)

When the slag was replaced with 10 and 20% ground glass (CSG10 and CSG20), there were no significant differences in the dormant period compared to CSG0; but the intensity of the main peak increased (from 0.39 for CSG0 to 0.50 and 0.47mW/g for CGS10 and CGS20, respectively).

The total heat release in the first 48 hours for CGS10 and CGS20 was the same and 45% of the total heat equivalent to C (133.75 J/g).

In Figure 5, the heat release velocity curves of blending cement with 70% replacement with S (CSG0) are shown. These samples were hydrated with NaOH solutions at different concentrations: 1, 3 and 5 % (CS-1, CS-3 and CS-5 respectively). Table 5 shows the singular points of hydration curves.

The maximum intensity peak increased between 1 and 3% NaOH and it decreased between 3 and 5% NaOH. Therefore, in the first 48 hours of hydration the sample with 3% NaOH generated the highest heat of hydration (52.35 J/g). This value was 9.5 % higher than that of blended cement (CSG0) hydrated with water and ~ 13.5 % lower than those with 10 and 20 % ground glass (CSG10 and CSG20) and with a considerable reduction of the dormant period, in agreement with the already reported results (18, 19).

For different mortars, the results of the flow test (in %) are shown in Table 6. Fluidity of mortars CG10 and CG20 was less than that of C. When incorporating 10 and 20% glass (CSG10 and CSG20) in slag cement, the percentage of slag was reduced and the effect tended to be reversed. The use of 3 % NaOH solution slightly reduced the fluidity compared to that of C, but it improved considerably with respect to CSG0.

Figure 6 shows the results of compressive strength of mortars in MPa. The compressive strength grew with age for all samples.

At 2 days, the compressive strength of CG10 and CG20 mortars was less than C, but these samples contained less cement than the reference sample. The compressive strength of CG10 and CG20 at 7 and 28 days reached or exceeded C at the same ages. The effect was moderated at 90 days.

At 2 days, CSG0, CSG10 and CSG20 mortars showed the effect of dilution on their compressive strength values. At 7 days, there was a considerable increase in the compressive strength overcoming the dilution; all mortars had a compressive strength greater than 70% of the pattern (C). At 28 days, although the CSG0 mortar reached 82.5% of the compressive strength of the pattern (C); CSG10 and CSG20 mortars reached 93% of the pattern. This means approximately 13% above CSG0 due to the joint action of slag and ground glass. Table 7 summarizes the previous information and shows the evolution of the compressive strength with the age of the samples studied, compared with the reference. At 90 days the same trend continued and compressive strength increased with the percentage of G.

The study of hydration and the identification of the phases formed were carried out by FTIR on pastes at different ages. The main vibrational bands identified for hydrated blended cements were: the wide bands located between 3450-3300 cm^-1, and 1640 cm^-1 corresponded to the stretching and bending vibrations respectively of the O-H bond in the water (6).The phases associated with hydrated calcium aluminates (which had bound water) could be analyzed in this area. Thus, in the samples with slag (with and without glass), these bands became wider as a consequence of the alumina of slag, since cement has a low C₃A content.

The peak in 3645 cm^-1 was attributed to the O-H bond of CH (20).The SiO₄ groups in the anhydrous materials (cement and slag) shifted to 996 cm^-1 with the hydration age in the pastes (ν3 Si-O bond) due to the formation of calcium silicate hydrate (C-S-H) and calcium aluminosilicate hydrate (C-A-S-H) (21). The advancement of hydration was related to with the shift and widening of these bands.

The band at 460 cm^-1 and the signal at 669 cm^-1 were attributed to ν2 and ν4 (Si-O-Si) bond vibrations, respectively. Another significant band was at 1420 cm^-1, attributed to ν3; CO₃^2- and the band detected in 872 and 713 cm^-1 were associated with ν2, CO₃^2- and ν4, CO₃^2-, respectively (22, 23). These vibrations were characteristic of calcite present as a minor component of cement and by pastes carbonation.

Figure 7 shows the infrared spectra of C, CG20, CSG0 and CSG20 at 2, 7 and 28 days of hydration. It can be seen that the silicate bands moved to a greater number of waves in all cases. The peak assigned to the CH (3645 cm^-1) appeared in the CG20 in the first ages and, as age increased, its intensity decreased. This peak is absent in CSG0 and CSG20 from the 2 days.

Figure 8 shows the pozzolanicity results of blended cements obtained by the standard Frattini test. The samples tested were CG10 CG20, CSG0, CSG10 and CSG20 at 2, 7 and 28 days.

For CG10 and CG20 at 2 days, there was stimulation by G because the values of (CaO] and [OH^-] resulted in the same order despite the increase in the percentage of replacement. At 7 and 28 days, the pozzolanic reaction occured due to the decrease in [CaO]. However, [OH^-] increased instead of decreasing with [CaO], by the alkalis release by G.

For CSG0, stimulation was observed at 2 days and pozzolanic activity at 7 and 28 days by simultaneously decreasing [CaO] and [OH^-]. For CSG10 and CSG20 samples, pozzolanic activity was observed at 2 days by decreasing [CaO] with the increase of the percentage of G replacement. However, [OH^-] increased slightly (much less than for samples CG10 and CG20) despite it had the same content of G. Alkaline activation of slag by ground glass in CSG10 and CSG20 could be observed by the significant decrease of [OH^-] compared with those released in CG10 and CG20.