Advances in Materials Science and Engineering

Advances in Materials Science and Engineering / 2017 / Article
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Alternative Cementitious Materials and Their Composites

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Research Article | Open Access

Volume 2017 |Article ID 8394834 | 9 pages | https://doi.org/10.1155/2017/8394834

The Role of Various Powders during the Hydration Process of Cement-Based Materials

Academic Editor: Prinya Chindaprasirt
Received19 Jun 2017
Accepted07 Aug 2017
Published11 Sep 2017

Abstract

The role of various powders including glass powder (GP), limestone powder (LP), and steel slag powder (SSP) during the hydration process of cement-based materials was investigated by using X-ray diffraction (XRD), thermogravimetric and differential thermal analysis (TG-DTA), scanning electron microscopy (SEM), and strength tests. GP has adverse impact on early strength, but the pozzolanic reaction at later stage enhances the strength development greatly. LP can significantly improve early strength. SSP has a good contribution to the early and later strength of the paste when its content is less than 15%. GP has little effect on the kind of hydration products but relatively large effects on the quantity. Calcium hydroxide (CH) content of GP paste decreases over curing age gradually, which is different from pure cement paste because its pozzolanic activity consumes more CH than that generated from the cement hydration. SSP and LP mainly play a role of filling effect at early stage. Nucleating effect of LP also promotes the early hydration of cement. The hydration of LP occurs at later stage and forms the calcium carboaluminate hydrates. The hydration of SSP is relatively slow, which generates CH at later stage and is effective in the strength development.

1. Introduction

Mineral admixture has become an indispensable component in concrete because it generally has some pozzolanic reactivity during the hydration process. Mineral admixture can replace cement and reduce cost of concrete; moreover, it can improve the workability of fresh concrete or some properties of hardened concrete. Therefore, the use of mineral admixture in concrete brings significant benefits.

Glass powder (GP) is ground waste glass which mainly comes from industrial waste glass (such as flat glass and glass fiber) and household waste glass (such as glass containers and light bulbs) [1]. GP has not been used as a cement replacement until recent years. It is amorphous and contains large quantities of silicon and calcium. Soda-lime glass is pozzolanic or even cementitious in theory when it is ground enough [1]. The use of GP in cementitious materials can effectively enhance the strength and inhibit the ASR reaction of the system [24]. GP was used to prepare reactive powder concrete (RPC) by replacing partial Portland cement to reduce the cost [5, 6]. It is found that using Portland cement, glass powder, silica fume, and water reducer can prepare high performance concrete with compressive strength up to 100 MPa. Concrete with GP has improved properties, that is, higher strength, lower dry shrinkage, and so on than those of the concrete with fly ash [3, 7]. However, the study on the action mechanism of GP in cement-based materials is still at the initial stage.

The main component of limestone powder (LP) is calcite (CaCO3), which is a cheap and easily available material. At present, LP is mainly used to replace partial fine aggregate or as mineral admixture in the concrete. As a mineral admixture, LP is observed to have hydration reactivity when it is ground to a certain degree of fineness and it needs to have a certain environment and enough hydration time [8]. LP reacts with aluminum phase in cement clinker to form calcium carboaluminate hydrates, which effectively accelerates the hydration and hardening process [9], and thus improves the properties of concrete [10, 11].

Steel slag powder (SSP) is the slag exhausted from converter, electric furnace, and refining furnace, whose main components are silicate and ferrite. In developed countries, the majority of SSP is used as aggregate in concrete [12]. China has studied the application of SSP as mineral admixture in recent thirty years. The studies have shown that SSP can be used as a kind of active cementitious material, but its activity is much lower than that of cement clinker.

Recently, little existing literatures focused on investigation of the hydration properties and process of the three various powders. As mineral admixtures, the hydration process and strength development of cement-based materials containing the three powders are relatively different. In this paper, GP, LP, and SSP will be used as mineral admixtures to study the role during the hydration process of cement-based materials.

2. Experimental

The ordinary Portland cement PO 42.5 (POC) complied with the Chinese standard GB175-2007 is used in this test. The chemical compositions of GP, LP, SSP, and POC determined by X-ray fluorescence (XRF) are listed in Table 1. The main compositions of GP are SiO2, Al2O3, and Na2O accounting for 55.75%, 10.64%, and 9.92%, respectively. LP contains high content of CaCO3, which mainly relied on raw limestone. The content of CaO, Fe2O3, and SiO2 in SSP is around 74%, because the source of steel slag is iron and steel materials, smelting slag material, eroded lining refractory, and the sediment carried by the solid material. SSP contains C2S, which can also be detected by XRD test.


CompositionsSiO2Al2O3CaOFe2O3MgOSO3K2ONa2OP2O5loss

Cement21.252.9163.093.240.683.361.120.310.173.52
GP55.7510.646.600.281.010.270.549.920.0311.9
LP1.790.5654.690.350.400.030.0641.93
SSP14.113.5142.3917.456.600.500.130.221.638.72

40 mm 40 mm 40 mm paste specimens used in this paper were prepared by the paste mixer with water to binder ratio of 0.4. All the specimens were cured in normal environment with relative humidity (RH) higher than 90% and temperature of °C till the stipulated age of 3, 7, 28, and 90 days. The mixture ratios are shown in Table 2. The content of mineral mixtures in cementitious system is 15%, 30%, and 45% by mass. The samples containing 30% powders were used for microtest. The compressive strength of the pastes at different ages was tested by WAY-2000, a battery solution type compression testing machine. Specific test procedure is referred to GB/T17671-1999, Method of Testing Cement-Determination of Strength. The cores of broken pastes were collected to be soaked in anhydrous ethanol to stop the continued hydration for SEM tests. Before XRD and TG-DTA tests, the specimens were removed from the ethanol and quickly ground into powder in the agate mortar and dried in 60°C for 2 hours to avoid carbonization. The chemical compositions were measured by Axios advanced X-ray fluorescence instrument, in voltage range from 30 to 60 kV, current 50 to 100 mA. Morphology of the specimens was investigated by using a SEM (JSM-5610LV, Japan). The XRD was detected by X’Pert Pro, PANalytical of Netherland, with scanning speed of 6°/min. The TG-DTA experiments were measured on the Diamond TG/DTA analyzer, produced by Perkin Elmer Instruments Plant (Shanghai), in the temperature range from 0 to 900°C, using platinum crucibles with approximately 4 mg of sample, under dynamic N2 atmosphere (50 mL/min).


SamplesCementGPLPSSPWater

PC600000240

GP-155109000240
GP-3042018000240
GP-4533027000240

LP-155100900240
LP-3042001800240
LP-4533002700240

SSP-155100090240
SSP-3042000180240
SSP-4533000270240

3. Results and Discussion

3.1. Strength

Figures 13 present the compressive strength of the three groups. According to the results, GP reduces the early strength of the paste, and the strength reduction becomes more obvious with the increase of GP content, which indicates that GP has significant adverse effect on the strength of the composite cementitious materials. But, the later strength of the GP sample improves faster than that of the pure cement (PC) sample. The strength of PC paste at 90 days increases 4.9% higher than that at 28 days, while GP-15, GP-30, and GP-45, respectively, increase 33.7%, 48.3%, and 17.9%. The characteristics of the multiedges and smooth surface of the glass particles might reduce the early mechanical properties of the cementitious system. Furthermore, GP has no independent hydraulicity but has high pozzolanic activity. At the later stage, GP reacts with Ca(OH)2, the hydration product of cement, and generates calcium silicate hydrate (C-S-H) which makes the microstructure denser and improves strength.

Different from GP group, the strength of LP group at 3 and 7 days first increases and then decreases along with the increase of LP content. When the content is 15%, the paste strength increases obviously.

When the content increases to 30%, the paste strength decreases and is lower than that of PC sample. The strength at 28 and 90 days is all less than that of PC sample. Moreover, the more the LP content is, the more the strength decreases. The reason is that a proper content of LP provides the nucleation site [13] for cement hydration at early stage, which promotes early hydration of cement [14] and thus improves the strength; but at the later stage, the hydrates from the cementitious system containing LP are less than that of PC sample, resulting in lower strength [15].

The strength of SSP group increases along with the curing age. 15% SSP content has little reduction effect on the strength and the strength at 7 days even is higher than that of PC sample. When the content is 30% or higher than 30%, the strength decreases rapidly, which suggests that large amount of SSP is disadvantageous to the strength.

In order to analyze the activity of the three powders, the activity index [16] is used to reflect their activity. The calculation progress is as formulas (1) to (3). Here, is the relative strength of cement paste containing powders, is the strength of cement paste containing powders, and is the mass fraction of the cement. For the reference (PC sample), , its relative strength is . is the reference strength,

Although the cement content of the paste containing various powders decreases correspondingly compared to PC group, is higher than and is higher than in general because of the enhancement of hydration activity effect. And the difference between the two is relative strength of the hydration activity effect contribution, which is called relative strength of hydration activity (). The calculation is formula

Thus a relative index is obtained, which is the contribution rate of hydration activity (), which can be used to characterize the hydration activity contribution of the powders in the cement paste. The calculation formula is as follows, and the results are shown in Table 3:


Samples3 days7 days28 days90 days

GP-15−0.25−0.38−0.26−0.10
GP-30−0.31−0.30−0.360.04
GP-45−0.12−0.09−0.150.06

LP-150.260.25−0.060.01
LP-300.130.140.040.11
LP-450.08−0.13−0.200.12

SSP-150.140.250.040.14
SSP-300.100.14−0.080.16
SSP-45−0.10−0.01−0.190.07

The contribution rate of GP increases along with the curing time. The value of contribution rate developing from early negative to the late positive reveals that the pozzolanic reaction degree of GP at the later stage is significantly higher than that at the early stage. LP’s early contribution rate is high and decreases along with the curing time in general, which indicates that the early filling effect and accelerating effect obviously improve the strength of the paste, but the later hydration activity is low. SSP has better early filling effect and the later hydration activity works a long time; thus the SSP group has higher early and later contribution rate than GP group.

3.2. Hydration Products
3.2.1. XRD

Figures 47 display the hydration products of the pastes with different powders. The main crystal hydrates of GP samples are similar to those of PC paste, that is, Ca(OH)2 (CH), calcium aluminate hydrate (CAH), and unreacted clinker, because the main chemical compositions of GP and cement are similar. Compared with the PC sample, the CH of GP group decreases gradually along with curing time, because GP consumes some CH by pozzolanic reactivity at the later stage. GP has feeble pozzolanic reactivity at early stage, which mainly occurs at later stage. The pozzolanic reactivity of GP needs to be under certain excitation conditions, such as enough alkali, thermal, and physical conditions [17]. In this experiment, the pozzolanic reactivity of GP is excited by an alkaline environment produced by cement hydration.

Compared with GP group, Figure 6 displays that CH diffraction peak of LP group significantly reduces, while CaCO3 (CC) diffraction peak is greatly enhanced, which is main composition of LP. A small amount of calcium carboaluminate hydrates C3A-CaCO3-11H2O diffraction peak can be found at 90 days but hardly found at 28 days. It is probably because the cement contains a little C3A and LP reacts with C3A in cement to generate carboaluminate hydrates; thus it has a little strength contribution rate at later stage. The formation of calcium carboaluminate hydrates has been found in other researches, the generation time may be at 7 to 127 days, and the time is based on reaction activity of different LP [18].

Figure 7 displays XRD pattern of SSP, which shows that SSP contains C2S. Figure 8 displays the hydration products of SSP group at 28 days and 90 days. The main crystal hydration products are CH, the unhydrated clinker, and a small amount of CC. The CH content of SSP group gradually increases along with the curing time because SSP consumes no CH but C2S generates CH, and the cement hydration continues to produce CH, so the CH content will increase overall which proves that the later strength contribution rate of SSP can keep high over a long time.

3.2.2. TG-DTA

The TG-DTA curves of the pastes are shown in Figures 912. The characteristics of all TG-DTA curves are roughly the same. All the DTA curves have an obvious endothermic peak at 400 to 500°C where the samples mainly take off the coordinated water. The position of highest endothermic peak is about 470°C which is caused by the CH and C-S-H’s (mainly CH) dehydrated decomposition where the TG curves have a significant weight loss gradient which relates to the weight loss of CH [19].

Based on the endothermic peak and the weight loss rate of TG-DTA curves, the CH content can be calculated quantitatively. The dehydrated decomposition of CH will occur at 400 to 500°C which will result in a loss in quality and the content of CH can be calculated as formula (4). The CH content is shown in Figure 13.

Figure 13 indicates that the CH content of LP sample, in accordance with PC sample, increases gradually over curing time which is consistent with the CH diffraction peaks of XRD patterns. And it is the same as SSP sample because both cement and SSP can generate CH instead of the CH consumption resulting from the pozzolanic hydration which has been proven by the XRD patterns. Different from PC, LP, and SSP, the CH content of GP sample declines along with the curing time because GP consumes CH during the pozzolanic reaction, which has also been revealed in the XRD patterns. Along with the curing time, on the one hand, the cement generates CH; on the other hand, GP consumes some CH. In fact, the amount of CH changing along with curing time is determined by the relative content of cement and GP and their reaction speed.

3.2.3. SEM

SEM images of the pastes at 28 and 90 days are shown in Figures 1417. Figure 14(a) reveals that PC paste at 28 days has a large amount of fibrous C-S-H gel, some needle-shaped ettringite, and hexagonal CH crystals which forms a framework by staggering, overlapping to a network structure and connecting with the surrounding unhydrated cement particles. But, the microstructure of the paste at 28 days appears loose. Figure 14(b) displays that the cement hydration is more adequate over curing age, and various hydration products fill into the original loose pores and form dense microstructure. The more hydration products are produced over curing age, similar to the TG-DTA and XRD results.

Similar to the PC sample, a large number of fibrous C-S-H gel can also be observed in Figure 15(a), and sometimes it also presented strip or rod-like, tubular, foil-like sheet [20]. The microstructure of the paste containing GP becomes denser than that of PC sample; it is difficult to observe and identify the crystal phases. GP plays the role as the filler at the early stage. It can be found from Figure 15(b) that the paste has formed dense microstructure, and most of the hydration products are unable to identify from the morphology. GP consumes CH generated by cement hydration and forms C-S-H gel, which has been proven by XRD and TG-DTA tests. C-S-H gel connects with other hydrates and forms a denser entirety, which plays an important role in the improvement of strength and microstructure and illustrates why the strength contribution rate of GP becomes positive at the later stage.

Figure 16(a) displays that the hydration products of LP-cement paste at 28 days adhere to the surface of LP particles. The hydration products of C3S generate free Ca2+ which will produce hydration products along the surface of limestone particles; this is the so-called “crystal nucleus effect.” This effect can promote the early cement hydration and increase the early strength but hinder the development of later strength, which is consistent with the strength test. Figure 16(b) shows that the C-S-H gel presents II type network at 90 days. At the same time, LP particle surface has been eroded, which confirms that LP takes part in the later hydration reaction again.

Figure 17(a) shows that the microstructure is loose; thus the early hydration degree of SSP is very low at 28 days. It can be seen from Figure 17(b) that C-S-H gel has been basically filled in the pore system at 90 days. The surface of the SSP has been corroded seriously and covered by C-S-H gel which indicates that SSP reacts with cement at the later stage. CH crystals have been gradually surrounded by other hydration products and formed dense microstructure, which better explains why SSP has a relative high strength contribution rate over a long time.

4. Conclusions

(1) GP has negative effect on the early strength but a high strength development due to the pozzolanic reaction at later stage. LP can obviously improve the early strength, especially at 3 and 7 days; it mainly plays a role of filling effect and nucleating effect at the early stage and reactive effect at later stage. SSP has a high contribution to the early and later strength of the paste when its content is under 15%. The early filling effect and the later hydration of SSP improve the strength contribution rate over a long time.

(2) GP has little effect on the kind of hydration products, but relatively large effect on the quantity. CH content of PC sample increases gradually along with the curing age, while the GP group is contrary. The CH content produced by cement hydration gradually increases, which stimulates the pozzolanic activity of GP; GP consumes CH more than that cement hydration generates. And CH content of LP and SSP samples are similar to PC group which increases along with curing age. The LP hydration product calcium carboaluminate hydrates can be detected by XRD and also be confirmed by SEM. The active substances C2S of SSP generate CH at the later stage.

(3) GP, LP, and SSP mainly play the role of filling effects at the early stage, and the nucleating effect of LP promotes the early hydration of cement. The surface of GP, LP, and SSP has been eroded at 90 days indicating that they take part in hydration reaction at later stage, which is also proven by the strength tests.

Conflicts of Interest

The authors declare that they have no conflicts of interest.

Acknowledgments

This project is funded by the National Key R&D Program of China (2016YFC0401907) and Opening Funds of Guangxi Key Laboratory of New Energy and Building Energy Saving (15-J-22-4-001).

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Copyright © 2017 Shuhua Liu et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.


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