Front. Phys.Frontiers in PhysicsFront. Phys.2296-424XFrontiers Media S.A.78230910.3389/fphy.2021.782309PhysicsBrief Research ReportInfluence of CaO Content on the Fly Ash–Lime System Hydrothermal Synthesis Reaction Under Autoclave CuringZhu et al.Fly Ash CementZhuChenhui1LouYilong2ShenXuemei3XuHesi1YangJie1*
School of Transportation and Civil Engineering, Nantong University, Nantong, China
Quzhou Water Resources and Soil and Water Conservation Management Center, Quzhou, China
Water Project Management of Nantong-Lvsi Canal, Nantong, China
Edited by:Qingxiang Meng, Hohai University, China
Reviewed by:Jie Zhu, Ningbo University, China
Shuiping Li, Yangzhou University, China
*Correspondence: Jie Yang, zch198916@qq.com
This article was submitted to Interdisciplinary Physics, a section of the journal Frontiers in Physics
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As a substitute for traditional Portland cement, the development and research of “low-temperature-synthesized fly ash cement” has been receiving extensive attention. This study explores the effects of calcium oxide content on the fly ash–lime system hydrothermal synthesis reaction under autoclave curing, focusing on the effects of CaO content on the strength of the cement paste. The changes in phase composition, microstructure, and morphology were characterized using X-ray diffraction and scanning electron microscopy (SEM) analysis. The results show that with an increase in the CaO content, the amounts of β-C2S and C12A7 in the gelling material also increase. However, when the CaO content is very high, the amounts of β-C2S and C12A7 in the gelling material no longer increase, and the strength is lost.
CaO contentlow-temperature-synthesized fly ash cementautoclave curingmicro-compositionmorphologyIntroduction
Cement is an indispensable building material in contemporary society. Its manufacturing process consumes a large amount of non-renewable resources as well as energy, which leads to greenhouse gas emissions [1–4]. Therefore, researchers have been extensively searching for an alternative gelling material.
High belite cement is one of the most researched alternatives. Three types of high belite cements have been studied, which includes: 1) belite-rich Portland cement [5–8]; 2) belite-rich sulfoaluminate cement or aluminoferrite cement as the main hydraulic minerals [9–17]; and 3) low-temperature-calcined active belite cement or low-temperature-synthesized fly ash cement [18–21]. Low-temperature-synthesized fly ash cement provides additional advantages of employing solid waste instead of clay as a resource. This decreases the consumption of limestone and allows sintering at low temperatures, which saves energy, and protects the environment. Therefore, it has good prospects for further development. Fly ash, lime, and a small number of admixture are smoothly mixed, and water is added until it molds. Subsequently, steam is cured at 100°C for 6–12 h to form calcium silicate hydrate and calcium aluminate. They are calcined at a proper temperature and heat is preserved until they quench. They are finely grounded and subsequently gypsum is added to finally produce cement.
This article prepared low-temperature-synthesized fly ash cement at different mixing ratios of CaO and Na2O. The effects of changing atmospheric pressures were observed during autoclave curing. Additionally, we observed the effects of calcium oxide content on the fly ash–lime system hydrothermal synthesis reaction under the autoclave curing. Particularly, this article focused on the effects of CaO content on the compressive strength of the prepared cement pastes. The changes in the phase composition, microstructure, and morphology were characterized using X-ray diffraction (XRD) and scanning electron microscopy (SEM) analyses.
Materials and Methods
The fly ash in the test was a gray powder. The specific surface area of the raw fly ash was 257.9 m2 kg−1, the specific surface area of ground fly ash was 436.2 m2 kg−1, and its chemical composition is as shown in Table 1. We analyzed pure lime i.e., CaO in the tests.
Chemical composition of fly ash.
Composition
CaO
SiO2
Al2O3
Fe2O3
MgO
SO3
Na2O
K2O
TiO2
LOI
Content (%)
2.26
49.21
29.46
4.36
0.80
0.18
0.39
1.21
1.21
10.08
The fly ash and lime were mixed smoothly at a certain percentage (the CaO content was 33, 38, 42%and 50%, respectively), and an appropriate amount of NaOH(1% measured by Na2O) was added. The sample was homogenized by adding water at a water:material ratio of 1:1. Subsequently, the prepared specimen was placed in an autoclave (at 160°C for 8 h), which was placed in a thermostat oil bath cauldron. The obtained autoclaved material was a synthetic material (precursor). It was calcined at 780°C in a high-temperature furnace and this temperature was maintained for 1.5 h. Subsequently, the material was quenched in air to obtain clinkers. The obtained clinkers were ground to a particle size of 0.08 mm using a mill, leaving a residue of 2% on the sieve. The ground clinkers were mixed with lime to obtain the gelling material.
The gelling material was made into a cement paste, with a water–cement ratio of 0.5:1; it was poured into a 20 × 20 × 20 mm size model. This was placed undisturbed in wet air for 24 h and was later demolded. Subsequently, it was maintained in water at 20 ± 1°C. Additionally, the compressive strengths were tested at 3d, 7d, and 28d.
Results and AnalysisCement Paste Strengths
The results are presented in Table 2. The compressive strengths of the cement pastes at 3d, 7d, and 28d were maximum when the CaO content was 42%. This was because when CaO was present in excessive amount, the content of dissociative CaO in the gelling material also increased and produced Ca(OH)2 on hydration, which further influenced (increased) the compressive strength of cement pastes. When the content of CaO was low, the content of C2SH2 and C3AH6 in steam curing decreased, which further decreased the amount of β-C2S and C12A7. This deteriorated the quality of gelling materials.
Compressive strengths of the samples.
Specimens no
Component
Compressive strength/MPa
CaO (%)
Na2O (%)
3d
7d
28d
A
33
1
10.7
14.8
43.3
B
38
1
12.9
15.1
44.7
C
42
1
17.1
21.8
50.1
D
50
1
12.4
17.6
48.8
Micro-analysisXRD Analysis
This article conducted XRD analysis of the prepared specimens B and C (with CaO content 38 and 42%, respectively). Figure 1A shows the XRD atlas of the autoclaved material. In addition to the characteristic peaks of unreacted mullite and quartz, the XRD atlas exhibited the presence of C-S-H(I), C-A-H, C3ASH4, CH, and CaCO3 from the hydrothermal synthesis reaction and a small amount of reacted tobermorite in the autoclaved material. Figure 1B exhibits the XRD atlas of specimens B and C after calcination. In addition to the residual mullite and silica, the characteristic peaks of β-C2S, C12A7, CaCO3, and some melilite calcium aluminum (non-gelatinous) were observed. Figure 1C shows the XRD atlas of the two specimens (B and C) in hardened cement pastes (28d) obtained from their corresponding gelling materials. As the CaO content increased, the Ca(OH)2 content (in the hydration sample) and the gelling material also increased. The diffraction peaks of Ca(OH)2 and gelling material were acute, and the strength of the diffraction peak increased.
X-ray diffraction patterns of the two specimens (B and C): (A) autoclaved, (B) after calcination, and (C) hardened cement pastes.
From the XRD atlas, this article concluded that the CaO content, to some extent, influenced the phase composition and content of the autoclaved materials, calcined materials, and hardened cement pastes. With an increase in the content of CaO, the hydrothermal synthesis in the autoclaved material increased, which further increased the content of Ca(OH)2. Therefore, the amounts of gelling materials in the calcined materials increased. Additionally, the content of dissociative CaO increased. When it approached 50%, the increase in the gelling material was limited. The redundant unreacted CaO converted into dissociative CaO in the gelling material, which decreased the compressive strength.
Morphologies AnalysisMorphologies of Autoclaved Materials
Figures 2A,B shows the SEM analysis of the autoclaved materials of fly ash-lime system with different CaO contents after autoclaved curing at 160°C for 8 h. The material exhibited in Figures 2A,B contain 42 and 50% CaO respectively. When CaO doping was 42%, the hydrothermal reaction produced a large number of gelatinous C−S−H, other hydration products, some well-crystallized octagonal-shaped C3ASH4, and a small number of Ca(OH)2 crystals partially carbonized into CaCO3. Additionally, the surfaces of the particles exhibited a layer of hydration products with pores which overlapped each other. The well-crystallized tobermorite crystals formed using some gelatinous substances produced layered materials composed of single chain Si−O tetrahedral and polyhedral CaO. Figure 2 shows flaky or sheet like structures with their length varying from 4.5 to 11 μm. The fine particles of irregular mullite and quartz grains were wrapped with condensed matter and were not involved in the hydrothermal synthesis reactions. This micromorphology was consistent with the XRD results. From specimen B, it was observed that when the CaO content was 50%, the gelatinous material produced in the autoclaved material did not increase, whereas the crystalline state of Ca(OH)2 increased, and CaO did not participate in the reaction. CaO was present in the autoclaved materials, therefore the autoclaved material had greater amount of free CaO. Additionally, the aggregation of the particles was loose, the pores were large, and the whole structure was relatively loose. This indicated that the amount of CaO in the ingredients was not too high.
SEM patterns of different autoclave (A and B) and calcining (C and D) materials.
Morphologies Analysis of Calcined Materials
Figures 2C,D shows the SEM analysis of the calcined fly ash–lime system with different CaO contents after hydrothermal synthesis and calcination at 780°C. The CaO content in Figures 2C,D was 42 and 50%. As observed from Figure 2C, before hydrothermal synthesis, C-S-H and C-A-H gels convert to β-C2S and C12A7, respectively under high temperature. The hydrothermally synthesized C−S−H was gelatinous; β-C2S also remained gelatinous but the β-C2S particles were finer than that of C−S−H. The better crystallized Ca(OH)2 in the autoclaved material decomposed into CaO and some substances such as irregular mullite, quartz particles, and CaCO3 did not participate in the reaction of hydrothermal synthesis. It was observed that the calcined materials had higher porosity, lower crystallinity, looser structure, and higher activity, owing to the high porosities of β-C2S and C12A7. Some materials exhibited a long square columnar cross-section, which was designated as the non-gelling calc alumina feldspar crystal (C2AS), produced by the decomposition of C3ASH4. This micromorphology was consistent with the XRD results. Figure 2D indicated that when the CaO content was increased to 50%, there was no increase in the content of β-C2S particles. The amount of most important cementitious minerals did not increase, and therefore the final strength did not improve. Additionally, the strength decreased owing to the existence of too much free CaO.
Morphologies Analysis of 28 d Hardened Pastes
Figures 3A,B exhibits the SEM analysis of the 28 d hardened cement pastes prepared using the fly ash–lime system with different CaO contents. The CaO doping in Figures 3A,B was 42 and 50%, respectively. Figure 3A shows that after curing for 28 days, when the CaO content in the original mixture was 42%, a large number of needle and flake hydration products were generated in the hardened cement slurry, including a well-crystallized flake or plate tobermorite composed of a single chain silica tetrahedron and CaO polyhedron. These were clustered with the generated Ca(OH)2 crystals and CaCO3, forming a network structure with a small number of pores. Almost all the C12A7 particles hydrated rapidly at 28d, while a small amount of small β-C2S particles present at the edge of the gel product were not hydrated. After adding gypsum, before molding, with the hydration at 28d, larger needles and sheet calcite crystals were observed, which mainly existed in some holes and seams. Owing to the decomposition of the hydrated garnet, some non-gelling calc alumina feldspar crystals (C2AS) were formed. The SEM analysis exhibited a long square columnar section, which was consistent with the results of XRD and exhibited a low 28d strength. Figure 3B, shows that on increasing the CaO doping to 50%, the CaO required for hydrothermal synthesis reached a saturation state, and the resulting hydrated calcium silicate and other gel products were flocculent. Compared with that of the CaO doping of 42%, the particles at CaO doping of 50% were loosely bound and resulted in a loose structure. Additionally at CaO doping of 50% there was more Ca(OH)2 crystallization, excess CaO, irregular mullite, quartz, and other particles occupying the holes and structural gaps. Therefore, when high amount of CaO (50%) was doped into the original ingredients, the pressure strength of the produced cement hardener did not show any change (neither increased nor decreased). This indicated that when the amount of CaO doping exceeded 42%, it had a negligible effect on the strength of the produced hardened cement slurry.
SEM patterns of different hardened cement pastes.
Conclusion
1) Under autoclaved conditions, the main gelatinizing active substance in the calcined material prepared by the hydrothermal synthesis of the fly ash–lime system was β-C2S and C12A7. With an increase in the CaO content, the amount of β-C2S and C12A7 in the final cementitious material increased correspondingly. When the content of CaO reached 50%, the amount of β-C2S and C12A7 did not change significantly. However, the existence of excessive free CaO led to a loose structure and loss of strength.
2) The results showed that the compressive strength of the paste reached a maximum at 3d, 7d, and 28d when the CaO content was 42%. When the CaO content was excessive, the content of free CaO in the cementitious material increased, and the Ca(OH)2 formed after hydration affected the strength of the paste. When the content of CaO was too low, the hydration products such as C2SH2 and C3AH6 in the steam feed were reduced, which further reduced the production of β-C2S and C12A7 after calcination, leading to a decrease in the final cementitious properties.
Data Availability Statement
The raw data supporting the conclusion of this article will be made available by the authors, without undue reservation.
Author Contributions
CZ, write YL, provide materials XS, macro analysis HX, collating test results JY, analysis result.
Funding
This research was funded by the Nantong University College Students' innovation and entrepreneurship training program (Grant No. 202110304115Y).
Conflict of Interest
The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.
Publisher’s Note
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