Construction and Building Materials 182 (2018) 399–405

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Construction and Building Materials

journal homepage: www.elsevier .com/locate /conbui ldmat

Study on the preparation and properties of belite-ye’elimite-alite cement

https://doi.org/10.1016/j.conbuildmat.2018.06.1430950-0618/� 2018 Elsevier Ltd. All rights reserved.

⇑ Corresponding authors at: School of Materials Science and Engineering,University of Jinan, Jinan, Shandong 250022, China.

E-mail address: mse_chengxin@163.com (X. Cheng).

Xiaolei Lu a,b, Zhengmao Ye a,b,⇑, Shuxian Wang a, Peng Du a,b, Chuanhai Li a,b, Xin Cheng a,b,⇑a School of Materials Science and Engineering, University of Jinan, Jinan, Shandong 250022, Chinab Shandong Provincial Key Laboratory of Preparation and Measurement of Building Materials, Jinan, Shandong 250022, China

h i g h l i g h t s

� The characteristic diffraction peak of ye’elimite shifts to the left as forms calcium barium sulphoaluminate.� Ferrite phase promotes the dissolution of calcium barium sulphoaluminate at high temperature.� The trace element of barium is more tend to incorporate into other clinker phases than alite.� BYA cement can significantly improve the mechanical strength of BCSA cements.

a r t i c l e i n f o

Article history:Received 30 December 2017Received in revised form 11 June 2018Accepted 16 June 2018Available online 22 June 2018

Keywords:Belite-ye’elimite-alite cementPreparationProperties

a b s t r a c t

Belite-ye’elimite-alite (BYA) cement is a type of an environment-friendly binder with less CO2 emission inmanufacturing process and has the durative development of strength in hydration stage. In this paper,BYA clinkers were well prepared by adding barium oxide. A combination of X-ray diffraction (XRD),the Rietveld methodology, differential scanning calorimetry (DSC)-thermogravimetric (TG) analysis andscanning electron microscopy (SEM)-energy dispersive spectra analysis (EDS) was used to investigatethe composition and quantitation of clinker phase. Strength tests were also conducted to study themechanical properties in the hardened cement pastes. The results indicate that BYA clinker preparedat 1380 �C with 5 wt% of ferrite phase contained 25.6 wt% of ye’elimite coexisting with 9.3 wt% of alite.The characteristic diffraction peak of ye’elimite shifts to the left as barium replaces calcium in all the clin-ker specimens. In addition, the trace element of barium is more tend to incorporate into other clinkerphases than alite. Compressive strength of BYA cement increases by 20.4 MPa from 3 d to 28 d. It is ben-eficial for the improvement of the mechanical properties of BCSA cement at medium hydration ages.

� 2018 Elsevier Ltd. All rights reserved.

1. Introduction

Portland Cement (PC) is widely used as a construction material.However, the production of PC generates about 530 kg and 370 kgof carbon dioxide per ton (CO2/t) of clinker from calcining rawmaterials and burning fuel, respectively [1]. Faced with the issuesof energy scarcity and global warming, Portland cement industry isbeing confronted with extensive press coverage [2,3]. Hence, it iscompulsory and necessary for the cement industry to seek a kindof alternative cement to substitute for those traditional PC. Admit-tedly, much attention is currently being drawn to the developmentof modified special cement clinkers owing to low CO2 emission andlow energy consumption in the manufacturing process [4–6].

Calcium sulfoaluminate cements are considered to beenvironment-friendly materials because of low CO2 emission dur-ing its production process [7]. This kind of binders have much vari-able compositions, such as calcium sulfoaluminate cement (CSA),alite-calcium sulfoaluminate cement (ACSA) and belite-calciumsulfoaluminate cement (BCSA), and all of them contain ye’elimite,which features high early strength, small volume shrinkage duringhydration and corrosion resistance [8–10]. CSA and BCSA havebecome the subject of intense research because these binders havethe potential to substitute PC at a large scale. However, mechanicalstrength of mortar slowly increases owing to the low reactivity ofbelite at medium hydration ages (between 3 d and 28 d) [11]. Thecontent of alite is more than 50 wt% in ACSA clinkers, and can beresponsible for strengths at medium hydration ages. The issue con-cerning the coexistence of alite and ye’elimite minerals in the ACSAclinkers needs to be solved [12,13]. Many researchers investigatedthat adding minor CaF2 and other elements are the main way toachieve the coexistence of alite and ye’elimite in ACSA clinker

Table 1Theoretic mineralogical phase assemblage of clinkers (wt%).

Number Phase composition

Alite Ye’elimite Belite Ferrite

RA 15 23 42 20RB 15 23 47 15RC 15 23 52 10RD 15 23 57 5

400 X. Lu et al. / Construction and Building Materials 182 (2018) 399–405

[13,14]. Liu and Li [15,16] showed that ACSA clinker was producedat temperatures between 1250 and 1300 �C by adding CaF2 andMgO. Ma [17] reported that the mineral formation of C4A3$1 andC3S was achieved by adding CaF2 and CuO to the raw material.Pe’rez-Bravo [11] investigated that the addition of CaF2 and ZnO pro-moted the formation of higher amounts of alite in ACSA clinker.However, CaF2 have the negative effect on the refractory materialsin cement kiln and the environmental protection [18]. Besides, alite,as the primary mineralogical phase in this clinker, generates largeamounts of CO2 from limestone calcinations. Based on those disad-vantages, it is not an ideal solution to saving energy and reducingCO2 emission in cement industry.

Recently, Londono-Zuluaga [19] reported belite-alite-ye’elimite(BAY) cement, one of the promising cements, showed highermechanical strengths than BCSA cements at medium hydrationage. BAY clinkers were prepared with the mineralizer of CaF2 ineach raw material mixture. Some research also proved that bariumoxide (BaO) was employed to decrease the formation temperatureof clinker phases and make ye’elimite stable at higher temperature[20–22]. However, there have been a few studies on the prepara-tion of belite-ye’elimite-alite (BYA) clinker by adding BaO in rawmixes [23–25]. Hence, this research aims to synthesis of BYAcement, which can overcome the low mechanical strengths ofBCSA cements at intermediate ages. All the parameters involvedin the process (clinkering conditions, ferrite phase content, miner-alogical compositions and morphology of clinkers) and mechanicalproperties were studied.

Fig. 1. The phase composition of BCSA clinker calculated by QXRD.

2. Experimental

2.1. Raw materials and sample preparation

In order to investigate the effect of barium on the formation ofBYA clinkers and eliminate the interference of impurities,analytical-grade CaCO3, SiO2, Al(OH)3, Fe2O3, CaSO4�2H2O andBaCO3 together were used to prepare clinker minerals. The theo-retic phase composition of those four clinkers was showed inTable 1. BaO (4.0 wt% in the raw material dosage) was added toeach raw material mixture. The prepared raw meals were homog-enized in a ball mill bottle with agate balls for 4 h, and then thehomogenized raw meal was mixed with water, and pressed intoU 45 mm � 3 mm disk models under a pressure of 16 MPa. Afterthat, the meals were dried in an oven at 105 �C for 2 h to removethe retained water, and then the dried disks were sintered in aresistance furnace at different temperatures (1320 �C, 1350 �Cand 1380 �C, respectively) for 60 min. Subsequently, cement clink-ers were removed from the furnace immediately and cooledrapidly by a fan.

The BCSA clinker, with a theoretical mineralogical compositionof 60 wt% C2S, 30 wt% C4A3$ and 10 wt% C4AF, was obtained byheating at 1350 �C and holding for 30 min. Phase compositions ofthe BCSA clinker (as shown in Fig. 1) were calculated by QXRD withthe TOPAS 4.2 software. RD-1380 clinker specimen was scaled-upto 500 g. The raw meal, with the appropriate amounts of the start-ing materials, was also homogenized for 4 h through the ball mill,and then mixed with water and casted pressed into U 60 mm � 10mm disk models under a pressure of 16 MPa. After dried in an ovenat 105 �C for 2 h, the dried disks were sintered in the furnace at1380 �C for 60 min. Air blast was used to cool down the hot clinkerspecimens to room temperature. Those two kinds of clinkers weremixed with 4.9 wt% and 4.4 wt% anhydrite (chemical grade),respectively. Anhydrite dosage in two clinkers was calculated bythe Eq. (1) [26]. The clinker and anhydrite were ground together

1 Notation: C = CaO, S = SiO2, A = Al2O3, F = Fe2O3, $ = SO3.

by the centrifugal ball mill until an average particle size (dv50)was close to 8 lm. The particle size distributions of the cementspecimens obtained by means of laser granulometry (the disper-sion liquid used during the test is ethanol) are given in Fig. 2.

W ¼ 0:13�M � Ac=S ð1Þwhere M is the anhydrite coefficient, namely, the ratio of theamount of SO3 provided by gypsum to the amount of SO3 neededfor the hydration of C4A3$ to form ettringite; Ac is the mass fractionof C4A3$ in the clinker; S is the mass fraction of SO3 in the anhydrite.

Cement pastes with a water to cement mass ratio of 0.5 wereprepared by mixing cement and water at 62 rpm in the mixer for2 min. After a 10 s interval, mixing was resumed for an additional2 min at 125 rpm. The fresh pastes were loaded into 20 mm � 20mm � 20 mm molds and vibrated at the time of casting to removeair bubbles. The molds were then covered with the plastic wrapand stored in a curing box with 98% relative humidity at 20 �C,

Fig. 2. Particle size distributions of two cement specimens.

X. Lu et al. / Construction and Building Materials 182 (2018) 399–405 401

and then removed from the molds. The demolded samples werecured in water at 20 �C for 3, 7 and 28 days.

2.2. Characterization

2.2.1. X-ray diffraction (XRD)All clinker specimens were ground into fine powder to perform

laboratory X-ray powder diffraction studies. The XRD patternswere collected on a Bruker AXS D8-Advance diffractometer withCu Ka radiation (k = 0.154 nm) generated at 40 kV and 40 mA atroom temperature. The powders were step scanned from 5� to70� with a step size and time per step of 0.02� and 0.5 s, respec-tively. Identification of clinker minerals was implemented by anal-ysis of Jade software. Rietveld refinement quantitative phaseanalysis was performed using TOPAS 4.2 software (with an accu-racy of about 1%). For all the diffraction patterns, the refined overallparameters included emission profile, background, instrument fac-tors and zero error [27]. The Rwp value of the profile refinementwas used to evaluate the quality of the fits in Rietveld refinementprocess. Generally, the result would be considered as reliable if theRwp value was less than 15% [28]. The crystal structure descrip-tions used for the main phases in clinkers are shown in Table 2.

2.2.2. Thermal analysisAn integrated thermal analyzer (Mettler, TGA/DSC, Switzerland)

was used to investigate the physical and chemical changes of therawmaterials during the heating. Before tests, rawmeals were vac-uum oven-dried at 105 �C for 2 h and then ground to fineness of lessthan 200 mesh, approximately 25 mg sample was added into theAl2O3 crucibles. The thermal analysis was performed from 25 �Cto 1400 �C at a heating rate of 10 �C/min under air atmosphere.

2.2.3. Morphology analysisA backscattered electron microscope was employed to examine

the clinker specimen for their morphology at microscopic scale.Those specimens used for the BSE examining need to be embeddedand polished for optimum performance [29], after polishing, it wascleaned by a clean polishing cloth. The final polished cross-sectionswere covered with carbon to provide a conductive surface for SEMimaging. Observation of mineral morphological feature, in particu-lar alite and ye’elimite minerals, was carried out on a scanningelectron microscope (SEM, Carl Zeiss Jena, EVO LS15, Germany),and equipped energy dispersive (EDS) spectroscopy was used todirectly analyze the elemental composition of the selected clinkerphases. The EDS analysis of each clinker mineral of more than 5points demonstrated the element mole ratio (The average value).

2.2.4. Compressive strengthCompressive strength of hardened cement pastes (20 mm � 20

mm � 20 mm specimen) were measured by using the universaltesting machine (MTS, CMT 5504, 50 kN). The average value ofcompressive strength was calculated from three replicate speci-mens at designated age (1, 3, 7 and 28 days, respectively).

Table 2The structural details of the main phases in clinker.

Phase Reference ICSD code

o-C4A3$ Calos and Kennard (1995) 80361c-C4A3$ Saalfeld and Depmeier (1972) 9560C2S Tsurumi, Hirano, et al. (1994) 79553C3S Nishi and Takeuchi (1985) 64759C2A0.5F0.5 Colville and Geller (1971) 9197C3A Mondal and Jeffery (1975) 1841

3. Results and discussion

3.1. The phase analysis of cement clinkers

XRD was used to analyze the phase composition of clinker spec-imens. The clinkers burned at different temperature (1320 �C,1350 �C and 1380 �C, respectively) and amount of ferrite phaseare shown in Fig. 3. The clinker specimens burned at different tem-perature present the similar mineral compositions. Belite, ye’elim-ite, alite and brownmillerite are in all clinker specimens by analysisof Jade software. When the content of ferrite is 20 wt% (Fig. 3(a))and 15 wt% (Fig. 3(b)), the intensity of ye’elimite peak increaseswith the rise of sintering temperature. Moreover, the characteristicdiffraction peak of ye’elimite shifts to the left (from 23.66� to23.51�). This might be due to the fact that barium has larger ionicradius than calcium. Ba2+ replaces Ca2+ and forms calcium bariumsulphoaluminate in all the clinker specimens [30]. This result isconsistent with the observations of BSE-EDS in later part of thispaper. Calcium barium sulphoaluminate has higher hydrationactivity than that of ye’elimite. Consequently, it provides a favor-able condition for the early strength in hardened cement pastes.

The theoretic ferrite phase is C2F mineral, however, the actualcomposition of ferrite is C2A0.5F0.5 (brownmillerite, 2h = 12.16�,d = 7.27 Å) that presented in all the clinker specimens. It is proba-bly that C2F itself contains iron as Fe3+ in both tetrahedral and octa-hedral sites, and the latter is twice as numerous as the former. Alhas smaller ionic radius than Fe and preferentially enters tetrahe-dral sites [31], similarly, barium also went into brownmilleritesolid solution owing to the characteristic diffraction peak ofbrownmillerite shifts to the left (from 2h = 12.16� to 2h = 12.13�).The characteristic peak of alite (2h = 51.8�, d = 1.76 Å) is generallyweakened with the increasing burning temperatures. The resultillustrates that amounts of ferrite can promote the dissolution ofye’elimite solid solution at temperature higher than 1350 �C[32,33], which hinders the formation of alite [34,35].

XRD patterns of clinkers with 10 wt% and 5 wt% ferrite phaseare shown in Fig. 3(c) and (d), respectively. As showed in Fig. 3(c) and (d), the characteristic diffraction peak of brownmilleriteand ye’elimite both shift to the left, this suggests that barium canmerge into those two minerals. The dissolution of barium inbrownmillerite can decrease the formation temperature of liquidphase and improve the viscosity of liquid phase, and it provides afavorable condition for the formation of alite. It is also in agree-ment with the TG-DSC analysis. The characteristic peaks of alite(2h = 29.3�, d = 3.03 Å and 2h = 51.8�, d = 1.76 Å) were observed toincrease generally as the calcination temperature rises. In general,the intensity of diffractive peak is related to the content and crys-tallinity of phase [36]. Therefore, the diffraction peak of alite inclinker specimens is more visible with 5 wt% ferrite phase and itsactual content stays relatively high.

Based on these results, the clinker specimen (called hereafterRD-1380) burned at 1380 �C with 5 wt% ferrite was the mostpromising candidate to be scaled-up. The mineral content of RD-1380 specimen calculated by TOPAS 4.2 software is displayed inFig. 4. The diffraction peaks of belite, ye’elimite, brownmilleriteand alite were observed, and the results of Rietveld quantitativephase analysis of clinker specimens with 10 wt% and 5 wt% ferritecontent are presented in Table 3. All the refinements have Rwp val-ues below 8%, which suggests that the fitting result of phase com-positions are highly accurate. Although the phase assemblage ofRD-1380 specimen is somewhat different to their targeted phasecomposition, it has maximum percentages of both ye’elimite andalite. The percentages of ye’elimite and alite are 25.6 wt% and9.3 wt%, respectively (see Table 3), and it is beneficial for durativedevelopment of strength in cement.

Fig. 4. Rietveld refinements for the RD-1380 specimen.

(a) 20 wt% (b) 15 wt%

(c) 10 wt% (d) 5 wt%

Fig. 3. The XRD patterns of clinker specimens with different content of ferrite phase.

Table 3Phase compositions for BYA clinkers obtained from Rietveld method (wt%).

Phase RC-1320 RC-1350 RC-1380 RD-1320 RD-1350 RD-1380

Belite 54.8 53.6 50.4 56.5 56.2 55.5Ye’elimite (o+c) 24.5 26.8 26.3 21.3 24.8 25.6Brownmillerite 14.3 12.7 15.1 13.6 11.3 9.6Alite 6.4 6.9 8.2 8.6 7.7 9.3Rwp 7.19 5.32 6.49 7.83 5.60 7.57

402 X. Lu et al. / Construction and Building Materials 182 (2018) 399–405

3.2. Thermal analysis

The TG-DSC result of rawmixes are shown in Fig. 5. The thermalanalysis results are used to obtain the information on the decom-position and the formation of chemical compounds during burning.As showed in Fig. 5, the first endothermic peak located at approx-imately 285 �C is proven to be the decomposition of Al(OH)3

Fig. 5. TG-DSC curves of raw materials at different content of ferrite phase.

X. Lu et al. / Construction and Building Materials 182 (2018) 399–405 403

[19,37], the second peak between 650 �C and 820 �C is attributed tothe decomposition of CaCO3. The third peak at approximately1230 �C is ascribed to the formation of liquid phase, and the forthexothermic peak about 1275 �C is attributed to the formation reac-tion of alite mineral [38]. When RA specimens with 20 wt% ferritephase are sintered, it is probable that the fifth peak about 1350 �Cis the dissolution of ye’elimite solid solution which inhibits thecrystallization of alite, and this is consistent with previous resultsof XRD observations (see Fig. 3(a)).

3.3. SEM-EDS analysis

The morphological feature of clinker specimens with differentcontent of ferrite phase was tested by SEM in Fig. 6. The light greyfield corresponds to alite in which the distinct polygon ye’elimiteinclusions are identified as darker areas [11,39]. The size ofye’elimite is approximate to 4 lm and its outlines is also very clearin the clinker specimen from Fig. 6. The brightest phase spreadover the clinker specimens corresponds to ferrite. Compared toye’elimite grains in clinker specimen (called hereafter RA-1320)with 20 wt% ferrite content at the burning temperature 1320 �C(Fig. 6(a)), the RD-1380 specimen is smaller (Fig. 6(b)). The ele-ment ratios obtained by EDS measurements is shown in Table 4.

The EDS analysis of the RD-1380 specimen indicates that clinkerphases contain the trace element of barium. Ye’elimite containsmainly barium and iron as substituting elements. It has beenreported that Al3+ site in the sodalite framework is being substi-

Table 4Element ratios from EDS analyses for the RD-1380 specimen.

Clinker phases Stoichiometric ratio Element/at.%

Al Si

Belite C2S 2.09 15Ye’elimite C4A3$ 32.89 0.Alite C3S 1.46 11

Fig. 6. BSE image of clinker specimens with diff

Table 5Average atomic ratio obtained by EDS in RD-1380 specimen; n stands for the number of m

Atomic ratio n (Ca + Ba)/Si

Experimental EDS ratiosBelite 7 2.16Ye’elimite 5Alite 9 3.09

Theoretical stoichiometric ratiosC2S 2.0C4A3$ –C3S 3.0

tuted by Fe3+ [40,41]. The barium element can be also observedin belite solid solution, while it is not substituted by calcium ele-ment in alite as EDS analyses in Table 4. Table 5 includes theatomic ratios obtained by EDS and the corresponding values ofthe stoichiometric phases for the sake of comparison. Besides, dur-ing cooling, the barium element incorporated in the melt is crystal-lized, together with ferrite. The result is in accordance with theanalysis of XRD in front part of this paper.

3.4. Mechanical properties

The compressive strength of cement specimens at different cur-ing time is shown in Fig. 7. The compressive strength of BCSA pre-pared at w/c of 0.5 is also presented for the sake of comparison.BYA cement shows higher compressive strengths than BCSAcement paste at any hydration time, in spite of the lower amountof ye’elimite solid solution in BYA cements. The results indicatethat the strength of calcium barium sulphoaluminate is higherthan that of ye’elimite in early stage. After hydration for 3 d, thestrength of BCSA increases slowly, only by 4.5 MPa in the mediumstage, which indicates slowly hydration process. However, themost important result is that the compressive strength of RD-1380 specimen has a durative improvement, and the strengthincreases by 20.4 MPa from 3 d to 28 d, which may be attributeto the presence of alite in cement clinkers. The hydration of alitein the cement matrix results much more C-S-H gel which is verybeneficial to improve the density of the hardened cement pastes

S Ca Fe Ba

.41 3.46 31.89 0.42 1.3395 5.86 23.92 1.64 2.52.29 2.92 34.85 – –

erent ferrite phases ((a) 20 wt%, (b) 5 wt%).

easurements (points). Theoretical atomic ratios of clinker phases are also included.

(Ca + Ba)/Al (Ca + Ba)/S

0.80 4.50

– –0.67 4.0– –

Fig. 7. Compressive strengths of cement specimens with different hydration time.

404 X. Lu et al. / Construction and Building Materials 182 (2018) 399–405

and feature a higher strength. The result indicates prepared BYAcement can improve the mechanical strength of BCSA cements atmedium hydration ages.

4. Conclusions

The following conclusions can be obtained by this study on thepreparation and scale up of belite-ye’elimite-alite (BYA) clinker byadding barium element:

(1) The characteristic diffraction peak of ye’elimite shifts to theleft as barium replaces calcium and forms calcium bariumsulphoaluminate in all the clinker specimens. In addition,the results of Rietveld quantitative phase analysis showye’elimite and alite present in the phase assemblage inquantities of approximately 25.6 wt% and 9.3 wt%,respectively.

(2) When the content of ferrite phase is 20 wt%, the dissolutionof calcium barium sulphoaluminate is promoted with theincreasing burning temperatures. However, it is likely toprovide a unfavorable condition for the formation of alite.

(3) The distinct darker ye’elimite presents mainly as inclusionsinside the light grey alite and the brightest ferrite phase.The trace element of barium is more tend to incorporate intoother clinker phases than alite.

(4) BYA cement shows higher compressive strengths than BCSAat any hydration time. The most important result is that thestrength of BYA cement increases by 20.4 MPa from 3 d to28 d. It can significantly improve the mechanical strengthof BCSA cements at medium hydration ages.

Conflict of interest

We declare that we have no conflicts of interest to this work.

Acknowledgements

The authors are grateful for the financial support of the NationalKey Research and Development Program (2016YFB0303505), theNational Natural Science Foundation of China (Grant Nos.51272092 and 51772129), and the ‘‘111 Project” of InternationalCorporation on Advanced Cement-based Materials (No. D17001).

References

[1] J. Damtoft, J. Lukasik, D. Herfort, et al., Sustainable development and climatechange initiatives, Cem. Concr. Res. 38 (2008) 115–127.

[2] E. Benhelal, G. Zahedi, E. Shamsaei, et al., Global strategies and potentialsto curb CO2 emission in cement industry, J. Clean. Prod. 51 (2013)142–161.

[3] S. Ishak, H. Hashim, Low carbon measures for cement plant-a review. Carbonemission reduction: policies, technologies, monitoring, assessment andmodeling, J. Clean. Prod. 103 (2015) 260–274.

[4] S. Berriel, A. Favier, E. Domínguez, et al., Assessing the environmental andeconomic potential of Limestone Calcined Clay Cement in Cuba, J. Clean. Prod.124 (2016) 361–369.

[5] Y. Shen, J. Qian, Y. Huang, et al., Synthesis of belite sulfoaluminate-ternesitecements with phosphogypsum, Composites 63 (2015) 67–75.

[6] S. Wang, L. Lu, X. Cheng, Effects of slag and limestone powder on the hydrationand hardening process of alite-barium calcium sulphoaluminate cement,Constr. Build. Mater. 35 (2012) 227–231.

[7] E. Gartner, Industrially interesting approaches to ‘low-CO2’ cements, Cem.Concr. Res. 34 (2004) 1489–1498.

[8] H.F.W. Taylor, Cement Chemistry, Thomas Telford, London, U.K, 1990.[9] I. Janotka, L.È. Krajèi, Resistance to freezing and thawing of mortar specimens

made from sulphoaluminate-belite cement, Bull. Mater. Sci. 23 (2000)521–527.

[10] E. Álvarez-Ayuso, X. Querol, A. Tomás, Environmental impact of a coalcombustion-desulphurisation plant: abatement capacity of desulphurisationprocess and environmental characterisation of combustion byproducts,Chemosphere 65 (2006) 2009–2017.

[11] R. Pe’rez-Bravo, G. A’lvarez-Pinazo, Jose Compana, et al., Alite sulfoaluminateclinker: Rietveld mineralogical and SEM-EDX analysis, Adv. Cem. Res. 26(2013) 10–20.

[12] S. Ma, R. Snellings, X. Li, et al., Alite-ye’elimite cement: synthesis andmineralogical analysis, Cem. Concr. Res. 45 (2013) 15–20.

[13] N. Chitvoranund, S. Sinthupinyo, F. Winnefeld, et al., Synthesis andhydration of alite-calcium sulfoaluminate cement, Adv. Cem. Res. 29 (2017)101–111.

[14] J. Yang, W. Li, Z. Li, et al., Flame-Resistant Corrosion-Resistant CoatingCN102815951A, 2013.

[15] T.Y.F. Duvallet, Influence of Ferrite Phase in Alite-Calcium SulfoaluminateCements [PhD thesis], University of Kentucky, Lexington, KY, USA, 2014.

[16] X. Liu, Y. Li, N. Zhang, Influence of MgO on the formation of Ca3SiO5 and3CaO�3Al2O3�CaSO4 minerals in alite sulphoaluminate cement, Cem. Concr. Res.32 (2002) 1125–1129.

[17] X. Liu, Y. Li, Effect of MgO on the composition and properties of alite-sulphoaluminate cement, Cem. Concr. Res. 32 (2002) 1125–1129.

[18] S. Ma, X. Shen, X. Gong, et al., Influence of CuO on the formation andcoexistence of 3CaO�SiO2 and 3CaO�3Al2O3�CaSO4 minerals, Cem. Concr. Res.36 (2006) 1784–1787.

[19] D. Londono-Zuluaga, J.I. Tobon, M.A.G. Aranda, Clinkering and hydration ofbelite-alite-ye’elimite cement, Cem. Concr. Compos. 80 (2017) 333–341.

[20] A. Zezulová, T. Stanek, T. Opravil, The influence of barium sulphate and bariumcarbonate on the Portland cement, Procedia Eng. 151 (2016) 42–49.

[21] H. Ludwig, W. Zhang, Research review of cement clinker chemistry: Part A,Cem. Concr. Res. 78 (2015) 24–37.

[22] X. Cheng, J. Chang, L. Lu, et al., Study of Ba-bearing calcium sulphoaluminateminerals and cement, Cem. Concr. Res. 30 (2000) 77–81.

[23] X. Guo, L. Lu, S. Wang, et al., Influence of barium oxide on the compositionand performance of alite-rich Portland cement, Adv. Cem. Res. 24 (2012)139–144.

[24] J. Zhang, C. Gong, S. Wang, et al., Effect of strontium oxide on the formationmechanism of dicalcium silicate with barium oxide and sulfur trioxide, Adv.Cem. Res. 27 (2015) 381–387.

[25] J. Li, Study on High Belite-Sulphoaluminate Cement [PhD thesis], WuhanUniversity of Technology, Wuhan, China, 2013.

[26] Y. Wang, M. Su, L. Zhang, Sulphoaluminate Cement, Beijing University ofTechnology Press, Beijing, China, 1999.

[27] K. Morsli, Á.G. De La Torre, S. Stöber, et al., Quantitative phase analysis oflaboratory active belite clinkers by synchrotron powder diffraction, J. Am.Ceram. Soc. 90 (2007) 3205–3212.

[28] E. Jansen, W. Schäfer, G. Will, R values in analysis of powder diffraction datausing Rietveld refinement, J. Appl. Crystallogr. 27 (1994) 492–496.

[29] P. Stutzman, J. Clifton, Sample preparation for scanning electron microscopy,in: L. Jany, A. Nisperos (Eds.), Proceedings of the Twenty-First InternationalConference on Cement Microscopy, Las Vegas, 1999, pp. 10–22.

[30] X. Cheng, J. Chang, L. Lu, et al., Study on the hydration of Ba-bearing calciumsulphoaluminate in the presence of gypsum, Cem. Concr. Res. 34 (2004) 2009–2013.

[31] P. Hewlett, Lea’s Chemistry of Cement and Concrete, fourth ed., ElsevierScience & Technology Books, Amsterdam, Netherlands, 2004.

[32] M.C.G. Juenger, F. Winnefeld, J.L. Provis, et al., Advances in alternativecementitious binders, Cem. Concr. Res. 41 (2011) 1232–1243.

[33] D. Shang, M. Wang, F. Wang, et al., Incorporation mechanism of titanium inPortland cement clinker and its effects on hydration properties, Constr. Build.Mater. 146 (2017) 344–349.

[34] S. Uda, E. Asakura, M. Nagashima, Influence of SO3 on the phaserelationship in the system CaO-SiO2-Al2O3-Fe2O3, J. Am. Ceram. Soc. 81(1998) 725–729.

[35] X. Li, W. Xu, S. Wang, et al., Effect of SO3 and MgO on Portland cement clinker:formation of clinker phases and alite polymorphism, Constr. Build. Mater. 58(2014) 182–192.

X. Lu et al. / Construction and Building Materials 182 (2018) 399–405 405

[36] R. Snellings, M. De Schepper, K. De Buysser, et al., Clinkering reactions duringfiring of recyclable concrete, J. Am. Ceram. Soc. 95 (2012) 1741–1749.

[37] J. Strunge, D. Knoefel, I. Dreizler, Effect of alkalies and sulfur on the propertiesof cement Part I. Effect of the sulfur trioxide content on cement properties,Zement-Kalk-Gips Ed. B 38 (1985) 150–158.

[38] X. Li, Study on Mineral Composition, Alite Structure and Correspondingproperties For Sulfur Bearing Portland Cement Clinker [PhD thesis], NanjingTech-University, Nanjing, China, 2014.

[39] L. Lu, J. Chang, X. Cheng, et al., Study on a cementing system taking alite-calcium barium sulphoaluminate as main minerals, J. Mater. Sci. 40 (2005)4035–4438.

[40] A. Cuesta, Á.G. De La Torre, E. Losilla, et al., Pseudocubic crystal structure andphase transition in doped ye’elimite, Cryst. Growth Des. 14 (2014) 5158–5163.

[41] C. Hargis, J. Moon, B. Lothenbach, et al., Calcium sulfoaluminate sodalite(Ca4Al6O12SO4) crystal structure evaluation and bulk modulus determination,J. Am. Ceram. Soc. 97 (2014) 892–898.

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