Next Article in Journal
Comparison of Laser Milling Performance against Difficult-To-Cut Alloys: Parametric Significance, Modeling and Optimization for Targeted Material Removal
Next Article in Special Issue
Effect of Graphene Oxide on the Crystallization of Calcium Carbonate by C3S Carbonation
Previous Article in Journal
Effect of Heat Treatment on Microstructures and Mechanical Properties of a Novel β-Solidifying TiAl Alloy
Previous Article in Special Issue
Revealing the Microstructure Evolution and Carbonation Hardening Mechanism of β-C2S Pastes by Backscattered Electron Images
 
 
Search for Articles:
Title / Keyword
Author / Affiliation / Email
Journal
Article Type
 
 
Advanced Search
 
Section
Special Issue
Volume
Issue
Number
Page
 
Journals
Materials
Volume 12
Issue 10
10.3390/ma12101673
materials-logo
Submit to this Journal Review for this Journal Propose a Special Issue
► Article Menu

Article Menu

share Share announcement Help format_quote Cite question_answer Discuss in SciProfiles thumb_up
...
Endorse textsms
...
Comment
first_page
settings
Order Article Reprints
Font Type:
Arial Georgia Verdana
Font Size:
Aa Aa Aa
Line Spacing:
Column Width:
Background:
Article

Effect of CaSO4 Incorporation on Pore Structure and Drying Shrinkage of Alkali-Activated Binders

by
Hyeongmin Son
,
Sol Moi Park
,
Joon Ho Seo
and
Haeng Ki Lee
*
Department of Civil and Environmental Engineering, Korea Advanced Institute of Science and Technology, 291 Daehak-ro, Yuseong-gu, Daejeon 34141, Korea
*
Author to whom correspondence should be addressed.
Materials 2019, 12(10), 1673; https://doi.org/10.3390/ma12101673
Submission received: 25 April 2019 / Revised: 15 May 2019 / Accepted: 17 May 2019 / Published: 23 May 2019
(This article belongs to the Special Issue Microstructures and Durability of Cement-Based Materials)
Browse Figures
Versions Notes

Abstract

:
This present study investigates the effects of CaSO4 incorporation on the pore structure and drying shrinkage of alkali-activated slag and fly ash. The slag and fly ash were activated at a 5:5 ratio by weighing with a sodium silicate. Thereafter, 0%, 5%, 10%, and 15% of CaSO4 were incorporated to investigate the changes in phase formation and internal pore structure. X-Ray Diffraction (XRD), thermogravimetry (TG)/derivative thermogravimetry (DTG), mercury intrusion porosimetry (MIP), nuclear magnetic resonance (NMR), and drying shrinkage tests were carried out to find the correlation between the pore structure and drying shrinkage of the specimens. The results showed that CaSO4 incorporation increased the formation of thenardite, and these phase changes affected the pore structure of the activated fly ash and slag. The increase in the CaSO4 content increased the pore distribution in the mesopore. As a result, the capillary tension and drying shrinkage decreased.

1. Introduction

A significant amount of CO2 is produced during cement production, which has substantially impacted global warming and air pollution [1]. Approximately 7% of the world’s CO2 emissions are due to Portland cement production. For example, 1 ton of CO2 is produced per ton of Portland cement [2]. As interest in the environment has increased, numerous studies have focused on developing binders that can replace cement [3,4,5,6]. Alkali-activated materials (AAM), such as blast furnace slag and fly ash, which can reduce carbon dioxide emissions, have recently been receiving attention as binders in place of conventional cement [7,8]. Slag and fly ash are currently used as representative binders that provide silicate (SiO2) and aluminate (Al2O3) as an aluminosilicate precursor instead of cement. Therefore, AAM is used for various fields such as transportation, industry, residential, mining, and well cementing [9,10], as well as for special purposes, such as radioactive waste disposal and toxic metal immobilization [11,12,13].
AAM is a composite synthesized by using inorganic material rich in silicate (SiO2) and aluminate (Al2O3) with an alkaline solution [14]. Numerous studies on the types of activators [15,16] and the types of binders [17,18,19,20,21,22] used in manufacturing AAM are currently in progress. MOH and M2O are frequently used as alkali activators, where M represents Na or K [15]. Slag and fly ash have been primarily used as the binders of AAM, and the reaction products have differed due to the chemical composition of both materials.
Calcium-rich slag-based AAM produces C-S-H gels with low Ca/Si ratios [23]. In contrast, the other products generated are hydrotalcite [24]. Slag-based AAM is structurally different compared to Portland cement, which mainly consists of SiQ1 and SiQ2 in a linear finite chain in the C-S-H gel. However, slag-based AAM has a long chain structure comprised of SiQ2 or SiQ2 (1Al) [23].
Fly ash, which has a high silica and aluminum content, can form an amorphous aluminosilicate gel as the primary product of the reaction [24]. This aluminosilicate gel has a three-dimensional network structure [25], which differs from a linear finite chain. In particular, the AAM that uses fly ash rich in silicon and aluminum shows a higher chemical resistance and thermal conductivity [26].
Recently, research on blended AAM with calcium-rich slag and fly ash that has high silicate and aluminum content has focused on utilizing these single binders [1,27]. It has been confirmed that a binder mixed with fly ash and slag has a high sulfuric acid resistance compared to only alkali activated slag due to the formation of more C-S-H gels and improvements in the distribution of the pore size [28,29]. When the two materials are mixed, the products of the reactions are complicated and differ from those produced when the fly ash and slag are used in isolation [23,26,30].
A significant number of studies have been conducted to improve the mechanical performance and control the setting time by incorporating an admixture into the AAM. Park et al. demonstrated that incorporating gypsum in the GGBFS activated by clinker-free CaO can lead to an ettringite formation that produces a positive effect on strength enhancement [31]. Although the addition of phosphoric acid in sodium silicate-based alkali-activated slag pastes has increased the setting time and decreased the initial compressive strength, the incorporation of gypsum increased the compressive strength and decreased the setting time [32]. In the case of fly ash with gypsum, a significant strength enhancement was observed in comparison with the strength of the unreacted fly ash after three months [33]. The formation of ettringite was observed as the incorporation of gypsum increased in high volume fly ash cement [34].
Aimin et al. showed that ettringite phase formation increased with an additional amount of gypsum in high volume fly ash cement [35]. Moreover, the addition of gypsum accelerated the geopolymerization of the bottom ash and activation of alumina leaching due to the presence of sulfate ions [36]. Neto et al. proved that incorporating sodium silicate and silica into a blast furnace slag (BFS) can result in additional ettringite formation as well as decreased shrinkage [37]. However, there is a lack of detailed studies on the pore structure when blended AAM is mixed with slag and fly ash that incorporate an admixture [38,39].
This study investigated the effect of CaSO4 incorporation on the pore structure and drying shrinkage of alkali-activated slag and fly ash (AASF). It also demonstrated the influence of anhydrite on AAFS when slag and fly ash were used as main binders with the alkaline activator. CaSO4 from 0 to 15% quantities in the weight ratio was incorporated into a slag/fly ash binder activated by a sodium silicate. X-ray diffraction (XRD), thermogravimetrics (TGs), and nuclear magnetic resonance (NMR) were used to characterize the hydration products. Mercury intrusion porosimetry (MIP) was conducted to examine the pore structure of the hardened alkali-activated slag/fly ash paste.

2. Materials and Methods

2.1. Materials and Specimens Preparation

The chemical compositions of the Class F fly ash and BFS used in the present study are shown in Table 1. The mortar specimens were fabricated with a 0.4:1:2 weight ratio of water:binder (fly ash and slag):fine aggregate. The fly ash and slag were actively mixed at a 5:5 ratio with 8% sodium silicate. A sodium silicate as an alkali-activator (SiO2 = 47.0%, Na2O = 50.0%, and bulk density = 1.2 g/cm3) of a powder type was used to synthesize the paste and mortar. The effect of incorporating CaSO4 on the pore structure of the AAFS was investigated by replacing a portion of the fly ash/slag with varying quantities of CaSO4 (0, 5, 10, and 15% relative to the weight of the binder). Table 2 shows the mixing proportions utilized in the present study.
The specimens underwent the following procedure. First, dry mixtures of fly ash/slag, sand, and CaSO4 were stirred to ensure homogeneity for five minutes. Water was then added to the mixture and stirred for an additional five minutes for homogeneous blending with the alkaline activator. Subsequently, the mixture was poured into a 50 × 50 × 50 mm3 mold for a compressive strength test and into a 30 × 30 × 600 mm3 mold for the dry shrinkage test. To determine the compressive strength and paste specimens, the mortar was sealed in a plastic wrap to prevent moisture from evaporating. The mortar was also cured at 20 °C. The specimens for the drying shrinkage test were installed one day after casting. The specimens for the drying shrinkage measurements were de-molded one day after casting and were cured at a room temperature of 20 °C and 50% relative humidity.

2.2. Test Methods

XRD, TG, MIP, and NMR analyses were conducted to investigate the effect of incorporating CaSO4 on the pore structure and phases of AAFS. The specimens for the analyses were immersed in acetone and dehydrated for 48 h to remove any capillary water. They were then subsequently crushed and made to pass through a 100-µm sieve.
The XRD analysis was conducted at a scan speed of 0.5 °/min using the Rigaku D/MAX-2500 (Rigaku, Tokyo, Japan) with Cu-Kα radiation and a scan range of 5° to 65°. The TG/DTG analysis was conducted using TGA/DSC1/1600LF (Columbus, OH, USA) in N2 gas heated at a rate of 10 °C/min.
MIP analysis was conducted using the ASTM D4284-07 method on an Autopore VI machine made by Micromeritics Instruments Corporation (Norcross, GA, USA). The contact angles and the surface tension of mercury were 130° and 485 dynes, respectively, for MIP analysis.
Solid-state 29Si MAS NMR spectral analysis was conducted at 79.51 MHz using an HX-CP MAS probe (Bluker, Billerica, MA, USA) and a 4-mm zirconia rotor with a Teflon spacer at a spinning speed of 11.0 kHz. A pulse width of 30° and 2.2 μs with a relaxation delay of 22 s was employed for the 29Si MAS NMR analysis. The chemical shifts were referenced to tetrakis (trimethylsiyl) silane at −135.5 ppm.
Solid-state 27Al MAS NMR spectra were collected at 156.3 MHz using an HX-CPMAS probe and a 2.5-mm outer diameter, as well as a low-Al background zirconia rotor at a spinning speed of 22.0 kHz. A pulse width of 30° and 1.8 μs with a relaxation delay of 2 s was employed. The chemical shifts were referenced to an external specimen of aqueous AlCl3 at 0 ppm for 27Al MAS NMR analysis.
The drying shrinkage was measured in accordance with ASTM 490 using a dial gauge. The first day’s measurements were taken hourly, the measurements for the rest of the first week were taken twice a day, and from the second week onwards, the measurements were taken once a day.

3. Experimental Results and Discussion

3.1. Shrinkage of Mortar Specimens

Drying shrinkage and mass change rates of specimens incorporating CaSO4 content are shown in Figure 1 and Figure 2, respectively. When 0% CaSO4 was incorporated, the highest drying shrinkage was observed in the paste, while G15 displayed the lowest drying shrinkage. The drying shrinkage difference between G10 and G15 was insignificant. In addition, the rate of growth of the drying shrinkage increased with a decrease in CaSO4 content. It was observed that the CaSO4 content affected the degree of shrinkage and the rate of shrinkage by changing the amount of water that evaporated. Therefore, a higher content of CaSO4 resulted in a lower mass loss due to a higher amount and faster water evaporation rate. This phenomenon is closely related to the pore size distribution [37]. This result means that the initial water evaporation occurs in the major capillary pores, and as the curing progresses, water evaporation in the intermediate micropores occurs [37]. The mass reduction of G15 by water evaporation was the largest, but the drying shrinkage in G15 was the smallest. It is reasonable that the rapid evaporation from the mesopore region has a greater effect than the evaporation from macropores [38].
The drying shrinkage rate from incorporating CaSO4 is shown in Figure 3. It can be observed that as the CaSO4 quantity increases, the ratio of drying shrinkage decreases. In addition, the highest peak drying shrinkage is delayed. The peak times at which the maximum drying shrinkages occur are 24, 45.6, 64.8, and 67 h. The results of drying shrinkage rates with different CaSO4 quantities show the existence of an initial shrinkage peak followed by a secondary peak. These peaks are closely related to the microstructure development and the hydration kinetics of each specimen [37]. The first peak is caused by the evaporation of free water after de-molding, whereas the second peak is related to the evaporation of water from the mesopores [37].

3.2. Effect of CaSO4 Incorporation on the Hydration Product of Paste Specimens

The results of XRD and DTG on the 7th and 28th days are shown in Figure 4 and Figure 5, respectively. The peaks of mullite and quartz were observed due to the presence of the unreacted fly ash. Previous studies have reported that when slag is used as a binder, ettringite is produced as a reaction of the sulfate [31]. Although the generation of ettringite was not significant in all the specimens, a peak of thenardite was observed, and its intensity increased with an increase in the CaSO4 content. The DTG results showed a primary peak between 50 to 100 °C and around 900 °C when the decomposition of the C-S-H gel and thenardite occurred [40,41,42]. The mass reduction in the C-S-H gel was less as the amount of CaSO4 incorporated was increased on the 7th day. Thenardite, which decomposes at around 900 °C, had a tendency to increase when the amount of CaSO4 incorporated was increased. The TG and DTG results showed a difference in the amount of C-S-H gel produced when the CaSO4 quantities were mixed. On the 7th day, as the CaSO4 content increased, the mass reduction between 100 and 200 °C also increased [43]. The results of the specimens’ TG and DTG on the 28th day show that the C-S-H gel formation decreased with an increase in the CaSO4 content.
A significant difference in the peak intensity of the anhydrite (CaSO4) was observed. Although the peak intensity of the G0’s anhydrite was insignificant, as the amount of CaSO4 increased, the peak intensity of the anhydrite was noticeable. The phase changes that interpreted the effect of CaSO4 on the pore structure and the drying shrinkage of the alkali-activated fly ash of the slag in the present study differ from those in the previous studies.
The 27Al MAS NMR results of each specimen on the 28th day showed the same results as the XRD in ettringite formation (Figure 6). The q2 and q3 peaks from 80 ppm to 60 ppm increased with an increase in CaSO4 incorporation. The resonance at 8 and 12 ppm denotes the presence of hydrotalcite and monosulfate, respectively. An increase in the incorporated CaSO4 quantity resulted in an increase in the peak near 10 ppm, where the peak indicates the presence of monosulfate. Therefore, an increase in the CaSO4 content can be consumed to form monosulfate and hydrotalcite with the addition of the Al gel in the C-S-H gel. The NMR did not show the formation of ettringite, and the greatest difference due to CaSO4 incorporation was confined to the formation of thenardite and anhydrite. The primary reason for no ettringite formation could be that any ettringite produced was transformed into mono sulfate due to an insufficient SO4 supply [44,45]. A further hypothesis can be made that ettringite was initially formed at an early stage and was then transformed into mono sulfate due to an inadequate SO4 supply [46,47]. The initially formed ettringite acted as a barrier that suppressed the hydration reaction of the binder. Consequently, the amount of unreacted slag increased with an increase in the amount of CaSO4 and the small amount of C-S-H gel produced.

3.3. Effect of CaSO4 Incorporation on Amorphous Gel of Paste Specimens

The 29Si NMR spectra of the CaSO4 that incorporated AAFS on the 28th day of curing are shown in Figure 7a–c, which represent the specimens’ incorporation of 0%, 5%, and 10% CaSO4, respectively. The spectra show that the predominant reaction product was C-A-S-H, which can be = attributable to the Q1, Q2(1Al), Q2, and Q3(1Al) sites with a significantly lower intensity of Q4(nAl) (n = 1, 2, 3, and 4) sites featured on the spectra. The summation of the relative areas corresponding to the C-A-S-H and N-A-S-H products of the G0 specimen was 35.61% and 32.54%, respectively. This indicates that the degree of reaction for the fly ash did not progress as much as that of the slag. However, the relative areas of both the C-A-S-H and N-A-S-H decreased with an increase in the CaSO4 content, thereby implying that the CaSO4 inhibits the reaction of AAFS. The summation of the reaction product (i.e., the entire relative area of C-A-S-H and N-A-S-H) for the G0 specimen was 69.08%, whereas that of the G5 and G10 specimens were 63.38% and 60.19%, respectively. This phenomenon is partially reflected by the TG/DTG results that indicate a reduction of C-A-S-H with an increase in the CaSO4 content.

3.4. The Correlation Between the Pore Structure and Drying Shrinkage of Paste Specimens

Figure 8 shows the pore size distribution results of each specimen with respect to the CaSO4 content on the 28th day as revealed by the MIP test. Their pore characteristics are tabulated in Table 3. The MIP peak intensities vary depending on the amount of CaSO4 mixed. The smaller the CaSO4 content, the more the pore distribution in the micropore was below 1.25 nm, whereas, as the CaSO4 content increased, the pore distribution was relatively prominent in the mesopore (1.25–25 nm). The increase in the CaSO4 content resulted in an increase in the peak in the macropore (25–5000 nm). The highest peak intensity was obtained when the amount of CaSO4 was 15%. Previous studies have found that the drying shrinkage is closely related to the volume of the mesopore [48]. A higher pore volume in the mesopore range is associated with a larger capillary tension by the water meniscus produced in the capillary pores of pastes, which is caused by a higher level of drying shrinkage [49]. The increase in the CaSO4 content causes a growth of the pores in the mesopore. Moreover, the decrease in the drying shrinkage is similar to the results of the previous studies [48].
The capillary pores are composed of the mesopore and micropore [50]. The micropore is composed of gel pores from the calcium aluminate silicate hydrate gel. Although an increase in the amount of CaSO4 resulted in the pores increasing in micro size, the pores in the mesopore decreased. When CaSO4 was not incorporated, the micropore that occupied the pores inside the C-S-H gel accounted for a significantly large part. However, the micropore size decreased with an increase in the CaSO4 content, as depicted by the TG/DTG results. Therefore, CaSO4 has an adverse effect on the formation of the C-S-H gel.
The changes in pores due to the incorporation of CaSO4 can affect the drying shrinkage of a hardened paste. A significant number of studies have been conducted on the correlation between the existing pore distribution and the drying shrinkage [51,52,53]. Also, the C-S-H gel and pore size distribution have a critical effect on the drying shrinkage [54]. Based on these results, it can be assumed that the incorporation of CaSO4 reduced the amount of C-S-H gel in AAM, resulting in a decrease in the micropores, which contributed to a higher drying shrinkage. A large pore size distribution in the mesopore resulted in larger capillary tension. Consequently, the drying shrinkage was reduced [55]. In addition, in the analysis of the 29Si NMR results, it was observed that the C-A-S-H gel and N-A-S-H gel reduced when CaSO4 was incorporated, which means the decrease of capillary tension resulting in drying shrinkage.

4. Concluding Remarks

The present study investigated the effect of CaSO4 incorporation on the phase and the internal voids of AAFS, as well as the effects on drying shrinkage. The CaSO4 was incorporated in weight ratios of 0%, 5%, 10%, and 15% in sodium silicate-activated fly ash/slag. The primary results of this study can be summarized as follows:
  • An increase in CaSO4 incorporation resulted in an increase in the unreacted slag, and hence, the amount of C-S-H gel decreased.
  • An increase in the CaSO4 content increased the number of voids distributed in the mesopore size, thereby decreasing the capillary tension and reducing the drying shrinkage.
  • The increase in the quantity of CaSO4 increased the formation of thenardite due to the combination of SO3 and Na ions. Consequently, it can be inferred that the number of SO3 ions needed for ettringite formation decreased.
  • The CaSO4 incorporation in AASF contributed to the increase in mesopore size, which may have caused a decrease in drying shrinkage by reducing the capillary tension.
This study shows that the incorporation of CaSO4 may have reduced the drying shrinkage by changing the pore structure of the alkali-activated fly ash/slag specimens. Future studies that investigate the effect of CaSO4 incorporation on the strength of AASF need to be carried out to determine the correlation between pore structure and mechanical properties.

Author Contributions

Conceptualization, H.M.S. and S.M.P.; methodology, H.M.S.; investigation, H.M.S. and S.M.P.; writing—original draft preparation, H.M.S., S.M.P. and J.H.S.; writing—review and editing, H.M.S.; supervision, H.K.L.; funding acquisition, H.K.L.

Funding

This study was supported by the National Research Foundation of Korea (NRF) grant funded by the Korea government (MSIT) (No. 2017R1A5A1014883) and (No. 2018R1A2A1A05076894).

Conflicts of Interest

No conflict of interest exits in the submission of this manuscript entitled “Effect of CaSO4 Incorporation on Pore Structure and Drying Shrinkage of Alkali-Activated Binders.” All the authors declare that they have no conflict of interest.

References

  1. Lee, N.; Jang, J.; Lee, H. Shrinkage characteristics of alkali-activated fly ash/slag paste and mortar at early ages. Cem. Concr. Compos. 2014, 53, 239–248. [Google Scholar] [CrossRef]
  2. Mehta, K.P. Reducing the environmental impact of concrete. Concr. Int. 2001, 23, 61–66. [Google Scholar]
  3. Ortega, J.M.; Navarro, P.; Luis, J.; Albaladejo Ruiz, A.; Sánchez, I.; Climent, M.Á. Durability and compressive strength of blast furnace slag-based cement grout for special geotechnical applications. Mater. Constr. 2014, 64, 313. [Google Scholar] [CrossRef]
  4. Joshaghani, A.; Balapour, M.; Ramezanianpour, A.A. Effect of controlled environmental conditions on mechanical, microstructural and durability properties of cement mortar. Constr. Build. Mater. 2018, 164, 134–149. [Google Scholar] [CrossRef]
  5. Ortega, J.M.; Esteban, M.D.; Rodríguez, R.R.; Pastor, J.L.; Ibanco, F.J.; Sánchez, I.; Climent, M. Ángel Influence of Silica Fume Addition in the Long-Term Performance of Sustainable Cement Grouts for Micropiles Exposed to a Sulphate Aggressive Medium. Materials 2017, 10, 890. [Google Scholar] [CrossRef]
  6. Joshaghani, A.; Moeini, M.A.; Balapour, M. Evaluation of incorporating metakaolin to evaluate durability and mechanical properties of concrete. Adv. Concr. Constr. 2017, 5, 241–255. [Google Scholar]
  7. Bernal, S.A.; De Gutiérrez, R.M.; Pedraza, A.L.; Provis, J.L.; Rodríguez, E.D.; Delvasto, S. Effect of binder content on the performance of alkali-activated slag concretes. Cem. Concr. Res. 2011, 41, 1–8. [Google Scholar] [CrossRef]
  8. Yang, K.-H.; Song, J.-K.; Song, K.-I. Assessment of CO2 reduction of alkali-activated concrete. J. Clean. Prod. 2013, 39, 265–272. [Google Scholar] [CrossRef]
  9. Krivenko, P. Alkaline cements: Terminology, classification, aspects of durability. In Proceedings of the 10th Congress on the Chemistry of Cements, Göteborg, Sweden, 2–6 June 1997. [Google Scholar]
  10. Li, C.; Sun, H.; Li, L. A review: The comparison between alkali-activated slag (Si + Ca) and metakaolin (Si + Al) cements. Cem. Concr. Res. 2010, 40, 1341–1349. [Google Scholar] [CrossRef]
  11. Deja, J. Immobilization of Cr6+, Cd2+, Zn2+ and Pb2+ in alkali-activated slag binders. Cem. Concr. Res. 2002, 32, 1971–1979. [Google Scholar] [CrossRef]
  12. Cho, J.; Ioku, K.; Goto, S. Effect of PbII and CrVI ions on the hydration of slag alkaline cement and the immobilization of these heavy metal ions. Adv. Cem. Res. 1999, 11, 111–118. [Google Scholar] [CrossRef]
  13. Qian, G.; Sun, D.D.; Tay, J.H. Characterization of mercury-and zinc-doped alkali-activated slag matrix: Part I. Mercury. Cem. Concr. Res. 2003, 33, 1251–1256. [Google Scholar] [CrossRef]
  14. Provis, J.L.; Bernal, S.A. Geopolymers and Related Alkali-Activated Materials. Annu. Revu. Mater. Res. 2014, 44, 299–327. [Google Scholar] [CrossRef]
  15. Provis, J.L.; Van Deventer, J.S.J. Geopolymers: Structures, Processing, Properties and Industrial Applications; Elsevier: Cambridge, UK, 2009. [Google Scholar]
  16. Shi, C.; Roy, D.; Krivenko, P.V. Alkali-Activated Cements and Concretes; CRC press: Boca Raton, FL, USA, 2006. [Google Scholar]
  17. Komnitsas, K.; Zaharaki, D.; Perdikatsis, V. Geopolymerisation of low calcium ferronickel slags. J. Mater. Sci. 2007, 42, 3073–3082. [Google Scholar] [CrossRef]
  18. Guo, X.; Shi, H.; Dick, W. Use of Heat-Treated Water Treatment Residuals in Fly Ash-Based Geopolymers. J. Am. Ceram. Soc. 2010, 93, 272–278. [Google Scholar] [CrossRef]
  19. Longhi, M.A.; Rodríguez, E.D.; Bernal, S.A.; Provis, J.L.; Kirchheim, A.P. Valorisation of a kaolin mining waste for the production of geopolymers. J. Clean. Prod. 2016, 115, 265–272. [Google Scholar] [CrossRef]
  20. Dimas, D.D.; Giannopoulou, I.P.; Panias, D. Utilization of alumina red mud for synthesis of inorganic polymeric materials. Min. Process. Extr. Met. Rev. 2009, 30, 211–239. [Google Scholar] [CrossRef]
  21. Gong, C.; Yang, N. Effect of phosphate on the hydration of alkali-activated red mud–slag cementitious material. Cem. Concr. Res. 2000, 30, 1013–1016. [Google Scholar] [CrossRef]
  22. Kumar, A.; Kumar, S. Development of paving blocks from synergistic use of red mud and fly ash using geopolymerization. Constr. Build. Mater. 2013, 38, 865–871. [Google Scholar] [CrossRef]
  23. LeComte, I.; Henrist, C.; Liégeois, M.; Maseri, F.; Rulmont, A.; Cloots, R. (Micro)-structural comparison between geopolymers, alkali-activated slag cement and Portland cement. J. Eur. Ceram. Soc. 2006, 26, 3789–3797. [Google Scholar] [CrossRef]
  24. Davidovits, J. Synthesis of new high temperature geo-polymers for reinforced plastics/composites. SPE PACTEC 1979, 79, 151–154. [Google Scholar]
  25. Davidovits, J. Chemistry of geopolymeric systems, terminology. In Proceedings of the Géopolymère ’99, 2nd International Conference, Saint-Quentin, France, 30 June–2 July 1999; pp. 9–39. [Google Scholar]
  26. Bakharev, T. Durability of geopolymer materials in sodium and magnesium sulfate solutions. Cem. Concr. Res. 2005, 35, 1233–1246. [Google Scholar] [CrossRef]
  27. Lee., N.; Lee, H. Reactivity and reaction products of alkali-activated, fly ash/slag paste. Constr. Build. Mater. 2015, 81, 303–312. [Google Scholar] [CrossRef]
  28. Ramezanianpour, A.; Malhotra, V. Effect of curing on the compressive strength, resistance to chloride-ion penetration and porosity of concretes incorporating slag, fly ash or silica fume. Cem. Concr. Compos. 1995, 17, 125–133. [Google Scholar] [CrossRef]
  29. Leng, F.; Feng, N.; Lu, X. An experimental study on the properties of resistance to diffusion of chloride ions of fly ash and blast furnace slag concrete. Cem. Concr. Res. 2000, 30, 989–992. [Google Scholar] [CrossRef]
  30. Wang, X.Y.; Lee, H.S. Modeling the hydration of concrete incorporating fly ash or slag. Cem. Concr. Res. 2010, 40, 984–996. [Google Scholar] [CrossRef]
  31. Park, H.; Jeong, Y.; Jun, Y.; Jeong, J.-H.; Oh, J.E. Strength enhancement and pore-size refinement in clinker-free CaO-activated GGBFS systems through substitution with gypsum. Cem. Concr. Compos. 2016, 68, 57–65. [Google Scholar] [CrossRef]
  32. Chang, J.J.; Yeih, W.; Hung, C.C. Effects of gypsum and phosphoric acid on the properties of sodium silicate-based alkali-activated slag pastes. Cem. Concr. Compos. 2005, 27, 85–91. [Google Scholar] [CrossRef]
  33. Ghosh, A.; Subbarao, C. Microstructural Development in Fly Ash Modified with Lime and Gypsum. J. Mater. Civ. Eng. 2001, 13, 65–70. [Google Scholar] [CrossRef]
  34. Boonserm, K.; Sata, V.; Pimraksa, K.; Chindaprasirt, P. Improved geopolymerization of bottom ash by incorporating fly ash and using waste gypsum as additive. Cem. Concr. Compos. 2012, 34, 819–824. [Google Scholar] [CrossRef]
  35. Aimin, X.; Sarkar, S.L. Microstructural study of gypsum activated fly ash hydration in cement paste. Cem. Concr. Res. 1991, 21, 1137–1147. [Google Scholar] [CrossRef]
  36. Poon, C.; Kou, S.; Lam, L.; Lin, Z. Activation of fly ash/cement systems using calcium sulfate anhydrite (CaSO4). Cem. Concr. Res. 2001, 31, 873–881. [Google Scholar] [CrossRef]
  37. Neto, A.A.M.; Cincotto, M.A.; Repette, W. Drying and autogenous shrinkage of pastes and mortars with activated slag cement. Cem. Concr. Res. 2008, 38, 565–574. [Google Scholar] [CrossRef]
  38. Collins, F.; Sanjayan, J. Effect of pore size distribution on drying shrinking of alkali-activated slag concrete. Cem. Concr. Res. 2000, 30, 1401–1406. [Google Scholar] [CrossRef]
  39. Bernal, S.A.; Provis, J.L.; Walkley, B.; Nicolas, R.S.; Gehman, J.D.; Brice, D.G.; Kilcullen, A.R.; Duxson, P.; Van Deventer, J.S. Gel nanostructure in alkali-activated binders based on slag and fly ash, and effects of accelerated carbonation. Cem. Concr. Res. 2013, 53, 127–144. [Google Scholar] [CrossRef]
  40. Rodriguez-Navarro, C.; Ruiz-Agudo, E.; Luque, A.; Ortega-Huertas, M. Thermal decomposition of calcite: Mechanisms of formation and textural evolution of CaO nanocrystals. Am. Miner. 2009, 94, 578–593. [Google Scholar] [CrossRef]
  41. Wang, S.D.; Scrivener, K.L. Hydration products of alkali activated slag cement. Cem. Concr. Res. 1995, 25, 561–571. [Google Scholar] [CrossRef]
  42. Kim, M.S.; Jun, Y.; Lee, C.; Oh, J.E. Use of CaO as an activator for producing a price-competitive non-cement structural binder using ground granulated blast furnace slag. Cem. Concr. Res. 2013, 54, 208–214. [Google Scholar] [CrossRef]
  43. Ben Haha, M.; Le Saoût, G.; Winnefeld, F.; Lothenbach, B. Influence of activator type on hydration kinetics, hydrate assemblage and microstructural development of alkali activated blast-furnace slags. Cem. Concr. Res. 2011, 41, 301–310. [Google Scholar] [CrossRef]
  44. El-Didamony, H.; El-Sokkari, T.M.; KHALIL, K.; Heikal, M.; Ahmed, I.A. Hydration mechanisms of calcium sulphoaluminate C4A3S, C4AS phase and active belite β-C2S. Ceram. Silikaty 2012, 56, 389–395. [Google Scholar]
  45. Pelletier-Chaignat, L.; Winnefeld, F.; Lothenbach, B.; Le Saout, G.; Müller, C.J.; Famy, C. Influence of the calcium sulphate source on the hydration mechanism of Portland cement–calcium sulphoaluminate clinker–calcium sulphate binders. Cem. Concr. Compo. 2011, 33, 551–561. [Google Scholar] [CrossRef]
  46. Wang, X.; Pan, Z.; Shen, X.; Liu, W. Stability and decomposition mechanism of ettringite in presence of ammonium sulfate solution. Constr. Build. Mater. 2016, 124, 786–793. [Google Scholar] [CrossRef]
  47. Christensen, A.N.; Jensen, T.R.; Hanson, J.C. Formation of ettringite, Ca6Al2(SO4)3(OH)12·26H2O, AFt, and monosulfate, Ca4Al2O6(SO4)·14H2O, AFm-14, in hydrothermal hydration of Portland cement and of calcium aluminum oxide—calcium sulfate dihydrate mixtures studied by in situ synchrotron X-ray powder diffraction. J. Solid State Chem. 2004, 177, 1944–1951. [Google Scholar]
  48. Perera, D.; Uchida, O.; Vance, E.; Finnie, K. Influence of curing schedule on the integrity of geopolymers. J. Mater. Sci. 2007, 42, 3099–3106. [Google Scholar] [CrossRef]
  49. Cincotto, M.; Melo, A.; Repette, W. Effect of different activators type and dosages and relation to autogenous shrinkage of activated blast furnace slag cement. In Proceedings of the 11th International Congress on the Chemistry of Cement (ICCC), Durban, South Africa, 11–16 May 2003. [Google Scholar]
  50. Lubda, D.; Lindner, W.; Quaglia, M.; Hohenesche, C.D.F.V.; Unger, K.K. Comprehensive pore structure characterization of silica monoliths with controlled mesopore size and macropore size by nitrogen sorption, mercury porosimetry, transmission electron microscopy and inverse size exclusion chromatography. J. Chromatogr. A 2005, 1083, 14–22. [Google Scholar] [CrossRef] [PubMed]
  51. Güneyisi, E.; Gesoğlu, M.; Mermerdaş, K. Improving strength, drying shrinkage, and pore structure of concrete using metakaolin. Mater. Struct. 2008, 41, 937–949. [Google Scholar] [CrossRef]
  52. Aly, T.; Sanjayan, J.G. Effect of Pore-Size Distribution on Shrinkage of Concretes. J. Mater. Civ. Eng. 2010, 22, 525–532. [Google Scholar] [CrossRef]
  53. Shimomura, T.; Maekawa, K. Analysis of the drying shrinkage behaviour of concrete based on the micropore structure of concrete using a micromechanical model. Mag. Concr. Res. 1997, 49, 303–322. [Google Scholar] [CrossRef]
  54. Bazant, Z.P.; Wittmann, F.H. Creep and Shrinkage in Concrete Structures; John Wiley & Sons: Hoboken, NJ, USA, 1982. [Google Scholar]
  55. Palacios, M.; Puertas, F. Effect of shrinkage-reducing admixtures on the properties of alkali-activated slag mortars and pastes. Cem. Concr. Res. 2007, 37, 691–702. [Google Scholar] [CrossRef]
Materials 12 01673 g001 550
Figure 1. Drying shrinkage of the specimens.
Figure 1. Drying shrinkage of the specimens.
Materials 12 01673 g001
Materials 12 01673 g002 550
Figure 2. Mass change of the specimens.
Figure 2. Mass change of the specimens.
Materials 12 01673 g002
Materials 12 01673 g003 550
Figure 3. The ratio of drying shrinkage of the specimens.
Figure 3. The ratio of drying shrinkage of the specimens.
Materials 12 01673 g003
Materials 12 01673 g004 550
Figure 4. X-ray diffraction (XRD) patterns of the specimens on the (a) 7th day and (b) 28th day.
Figure 4. X-ray diffraction (XRD) patterns of the specimens on the (a) 7th day and (b) 28th day.
Materials 12 01673 g004
Materials 12 01673 g005 550
Figure 5. Thermogravimetric (TG)/DTG results on the (a) 7th day and (b) 28th day.
Figure 5. Thermogravimetric (TG)/DTG results on the (a) 7th day and (b) 28th day.
Materials 12 01673 g005
Materials 12 01673 g006 550
Figure 6. 27Al nuclear magnetic resonance (NMR) of the specimens on the 28th day.
Figure 6. 27Al nuclear magnetic resonance (NMR) of the specimens on the 28th day.
Materials 12 01673 g006
Materials 12 01673 g007 550
Figure 7. 29Si NMR of the specimens on the 28th day, (a) 0% CaSO4, (b) 5% CaSO4, (c) 10% CaSO4.
Figure 7. 29Si NMR of the specimens on the 28th day, (a) 0% CaSO4, (b) 5% CaSO4, (c) 10% CaSO4.
Materials 12 01673 g007
Materials 12 01673 g008 550
Figure 8. Pore size distribution on the 28th day.
Figure 8. Pore size distribution on the 28th day.
Materials 12 01673 g008
Table
Table 1. Chemical composition of fly ash and slag used in this study.
Table 1. Chemical composition of fly ash and slag used in this study.
(wt %)SiO2Al2O3Fe2O3CaOMgOP2O5TiO2K2OSO3LOI a
Fly ash50.021.010.04.81.31.51.51.41.02.71
Slag32.411.50.647.73.00.60.50.52.70.29
a Loss on ignition.
Table
Table 2. Mix composition of the specimens.
Table 2. Mix composition of the specimens.
Specimen CodeSlagFly AshGypsumWaterSandW/B a
G00.50.500.420.40
G50.4750.4750.050.420.40
G100.450.450.10.420.40
G150.4250.4250.150.420.40
a Water/binder ratio.
Table
Table 3. Pore characteristics on the 28th day.
Table 3. Pore characteristics on the 28th day.
Specimen CodePorosity (vol %)Total Pore Area (m2/g)Average Pore Diameter (nm)
G033.35103.7918.1
G533.7477.91911.9
G1038.1750.62020.4
G1543.0540.90829.7

Share and Cite

MDPI and ACS Style

Son, H.; Park, S.M.; Seo, J.H.; Lee, H.K. Effect of CaSO4 Incorporation on Pore Structure and Drying Shrinkage of Alkali-Activated Binders. Materials 2019, 12, 1673. https://doi.org/10.3390/ma12101673

AMA Style

Son H, Park SM, Seo JH, Lee HK. Effect of CaSO4 Incorporation on Pore Structure and Drying Shrinkage of Alkali-Activated Binders. Materials. 2019; 12(10):1673. https://doi.org/10.3390/ma12101673

Chicago/Turabian Style

Son, Hyeongmin, Sol Moi Park, Joon Ho Seo, and Haeng Ki Lee. 2019. "Effect of CaSO4 Incorporation on Pore Structure and Drying Shrinkage of Alkali-Activated Binders" Materials 12, no. 10: 1673. https://doi.org/10.3390/ma12101673

Note that from the first issue of 2016, this journal uses article numbers instead of page numbers. See further details here.

Article Metrics

Back to TopTop