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1 Copyright 2013 by ASME

MODELING POZZOLANIC SYSTEMS FOR SUBSURFACE CEMENTITIOUSSYSTEMS

Eduardus KoendersCOPPE-UFRJ / TU Delft

Rio de Janeiro, Brazil / Delft, The Netherlands

Camila Aparecida Abelha RochaCOPPE-UFRJ

Rio de Janeiro, Brazil

Neven UkrainczykTU Delft

Delft, The Netherlands

Romildo Dias Toledo FilhoCOPPE-UFRJ

Rio de Janeiro, Brazil

ABSTRACTThe secondary pozzolanic reaction mechanism has been

modeled explicitly in the Delft hydration model Hymostruc.

The model calculates the progress of the hydration process as a

function of the particle size distribution, the water cement ratio,

the temperature and the cement and pozzolanic chemistry. The

consumption of portlandite due to the activation of the

pozzolanic materials is shown in detail. The numerical results

are validated by an experimental testing plan on G-cement and

8% of silica fume and a water to cementitious ratio of 0.44. Thesimulated development of portlandite and degree of hydration

and the experimental results are in good agreement.

INTRODUCTIONThe interest in modeling the hydration process of

pozzolanic-based cementitious systems has gained an enormous

attention. Especially for the offshore industry, pozzolanic

systems, using green supplementary materials like sugarcane

bagasse, rice husk ash, fly ash or silica fume, this could add

both to the performance of the mechanical performance and to

the footprint of the sustainable solution. Blended cement

systems turned out to have a significant positive effect onreducing CO2 emissions. Replacing cementitious clinker by a

pozzolanic material leads directly to a reduction of the

cementitious clinker mass which, on its turn, leads to a

corresponding reduction of the CO2 production by the cement

industry. Nowadays, most blended cement systems in the

construction industry use Blast furnace slag as a pozzolanic

material. In The Netherlands, in general, slag replacements

exceed 65% and may increase to 80% of the cement content. In

Brazil, these numbers are a little lower, viz. 50% and is the

highest degree of replacement allowed. Optimizing these ratios

of blends can be very advantageous for the properties of the

internal hydration and the quality of the microstructure. An

advanced hydration model is needed to quantify these

properties. Therefore, in this paper the calculation principles o

the hydration model Hymostruc will be explained while also

accounting for the basic cementitious reactions and pozzolanic

reactions. The simulated results are compared with

experimental data received from lab tests on G-cement with

silica fume addition, at the LabEST laboratory of COPPEUFRJ.

HYDRATION MODELINGThe main vision behind the hydration modeling approach is that

the primary silicate reactions produce CH and that the

secondary reaction uses the SiO2 content of the pozzolans to

react and produce pozzolanic CSH. In this approach C3S and

C2S are the main silicate phases that produce most of the CH, a

necessary reaction product for the secondary pozzolanic

reaction to happen. Both the clinker phase and the pozzolanic

phase follow a certain particle size distribution (PSD) and are

taken into account in the modeling approach explicitlyAccording to the Rosin-Ramler equation, the grading of the

particles can be calculated per single fraction. From the

materials individual PSD and the water to cementitious ratio o

the cement paste, the particle structure of the blended paste can

be calculated. A 3D impression of the initial 3D microstructure

is provided in Fig 1 where the grey particles represent the

anhydrous cement grains and the purple particles represent the

pozzolanic grains.

Proceedings of the ASME 2013 32nd International Conference on Ocean, Offshore and Arctic Engineering

OMAE2013

June 9-14, 2013, Nantes, France

OMAE2013-10916

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Fig 1. Virtual 3D microstructure of cement and pozzolans

before reaction has commenced.

From this 3D particle structure, the inter-particle spacings and

the paste density can be calculated for each fraction

individually. Based on this, the geometrical structure of the

paste is available for simulation. In Hymostruc the hydration ofthe individual particles is modeled explicitly following both a

full 3D approach and a statistically-based cell concept [1]. A

cell is considered to be an elementary paste volume that

contains the volume of water and the volume of (blended)

cement grains up to a certain fraction. The cell density for three

different pozzolanic replacements is shown in Fig 2.

Fig 2. Cell density for three different pozzolanic replacements.

Based on the cell concept, hydration products representing the

inner and outer C-S-H gel that is formed by each individual

fraction can be calculated. The outer expansion of the particles

is calculated according to the so-called particle expansion

mechanism (Fig 3) [1,2]. The expansion mechanism describes

the outer growth of a spherical central particle with diameterx,

while embedding the cement and

Fig 3. Schematic impression of expansion mechanism [3].

pozzolanic particles smaller than the central particle in the

expanding shell. The volumetric outer expansion of the

particles Vcou,ex,x,j and Vp

ou,ex,x,j with diameterx at time j and an

outer volume Vcou,x,j and Vp

ou,x,j can be calculated by means of a

geometrical leading to the following equations for cemen

(sup. c) and pozzolan (sup.p), respectively [1-3]:

)()()(1 ,,,;,;

,;, p

jx

c

jx

c

jxou

c

jxouc

jxexouff

vv

(1)

)()()(1 ,,,;,;

,;, p

jx

c

jx

p

jxou

p

jxoup

jxexouff

vv

(2)

where is the density of the shell surrounding a central particle

The factors f(c

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particles will hydrate faster than the bigger particles and show a

much rapid increase of the degree of hydration in comparison

with the coarser cement particles. However, in terms of mass,

the finer pozzolanic fractions contribute less, which also holds

for the development of the degree of hydration of the blended

system. In the model the degree of hydration of the blended

system s

is calculated according to:

p

jp

c

jcjs mmt )( (5)

where mc is the mass fraction of the cement and mp the mass

fraction of the pozzolan. The incremental evolution of the

degree of hydration of the cement is calculated from the four

Bogue phases, i.e. C3S, C2S, C3A and C4AF, individually and

based on their mass representation of the phases in the cement

clinker according to:

C3S:

3 3 3

3

3 3

, 1 , 1 ,

,

1 1

C S C S C S

x j x j x jC S

x j c cx xr r

(6)

C2S:

2 2 2

2

3 3

, 1 , 1 ,

, 1 1

C S C S C S

x j x j x jC S

x j c c

x xr r

(7)

C3A

3 3 3

3

3 3

, 1 , 1 ,

, 1 1

C A C A C A

x j x j x jC A

x j c c

x xr r

(8)

C4AF:

4 4 4

4

3 3

, 1 , 1 ,, 1 1

C AF C AF C AF

x j x j x jC AFx j c c

x xr r

(9)

Analogue to this, the evolution of the degree of hydration of the

pozzolanic particles can be calculated with a similar approach

Therefore, for a system with dominating pozzolanic SiO2

particles the degree of hydration p is calculated according to:

3

,1,

3

1,

,

222

2 11

p

x

SiO

jx

SiO

jx

p

x

SiO

jxSiO

jxrr

(10)

In these equations x is the actual depth of the water (reaction)

penetration front, x is the incremental increase of thepenetration front within a particular period of hydration time

and rc the radius of the clinker particle, and rp is the radius of a

pozzolanic particle. With these set of equations and with the

formulations of the chemical silicate reactions the amount of

phases consumed (C3S, C2S, C3A, C4AF, SiO2 and H2O), and

the amount of phases produced (C-S-H and CH) during

hydration of a blended system can be calculated as a function of

time and as a function of the degree of hydration.

Fig 4. Schematic representation for the shell (containing binder

particles = cement and pozzolan) surrounding a central cemen

particle (left) and a central pozzolan particle (right).

INTEGRATED PARTICLE KINETICSAs said, in Hymostruc the 3D microstructure is simulated using

the particle expansion mechanism (Fig. 3) where the particles

are modeled as expanding spheres following the kinetics of eq

(1). In this equation K0 is the basic rate of hydration of the

individual cement or pozzolan particles, F1 is the Arrheniusfunction and the i account for the state of water in the

microstructure during hydration. The last part in the equation

accounts for the change of the reaction process from phase

boundary to diffusion controlled and also accounts for the

temperature effect F2 on the morphological growth of the C-S-

H gel. The water penetration into an individual reacting particle

with time can, therefore, be described as with the following

equation called Basic Rate Equation (BRE):

1

22

,

2213210

1

1,)()(

jx

tr

j

jxFFFK

t(11)

where ,j+1 represents the penetration depth of the reaction

developed in the upcoming incremental time step tj+1, while

tr and x,j are the transition thickness and the thickness of the

product layer, respectively. Finally, accounts for the change

from phase boundary to a diffusion controlled reaction, and

are three empirical constants [2]. The first reduction factor

1 refers to the hydration of the embedded and stil

incompletely hydrated cement and/or pozzolanic particles

situated in the shell of either cement or pozzolanic particles

The still incomplete hydrated cement or pozzolanic particles

embedded in the shell of a central cement or pozzolanic particle

(Fig 4) may withdraw a certain amount of the water needed for

further hydration of the central cement or pozzolan particle

This means that the rate of hydration of the central cemen

and/or pozzolanic particles is affected by the embedded and

still incomplete hydrated cement and/or pozzolanic particles

which means that the kinetics of the particles is depending on

its particular position in the microstructure. It makes the rate of

hydration unique for each hydrating particle in the system. For

the cell concept as presented in this paper, this mechanism is

considered per fraction while for the fully 3D kernel this

Cement Pozzolan

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Fig 4. Effect of1 on the rate of reaction for different central

hydrating cement particlesx with diameters 20, 40 and 110 m

and embedded cement particles for a w/c ratio of 0.4.

mechanism is considered on an individual particle level. This

makes each particle a unique object. The reduction factor1 for

the central cement particle (Fig 4, left) can be described

according to the following formulation:

p

jxemp

c

jxemc

c

jx

c

jx

wmwmw

w

,;,;,

,

1

(12)

Where wcx,j, wcem;x,j and w

pem;x,j, are the incremental water

consumption of the central cement particle, by the embedded

cement particles and by the embedded pozzolanic particles,

respectively. Furthermore, mc and mp are the mass fractions of

the embedded cement and pozzolanic particles of all particles

with a diameter smaller than the central particle considered.

Fig 5. Schematic representation of the pore volume distribution

as a function of the pore diameter.

Fig 6. Effect of2 on the rate of reaction process versus the

degree of hydration for different water to cement ratios.

The second reduction factor2 refers to the water shortage in

the pore system and its associated effect on the partial emptying

of the pores and locally ceasing of the hydration process [1,2]When considering this concept in view of the addition of the

pozzolanic phase, the microstructural parameters that are

affected by the cement as well as the pozzolanic reaction are

both the volume of capillary waterVcap (bounded by hydration

and the actual pore volume Vpor (solidification of the

microstructure due to C-S-H production). The effect of the

water shortage in the pore system 2 can be calculated from the

free pore wall areaAwat, relative to the total pore wall area Aporor from the minimum pore 0 and maximum pore pordiameters

in the system and the diameter of those pores that are stil

completely filled with waterwataccording to:

,

,

0,

0,2

)()(

wat

po r

po r

wat

po r

wat

AA

(11)

The pore diameters in equation (11) change with progress of the

hydration process, which makes 2 also a function of the

degree of hydration . A pore model (Fig 5) can be used to

calculate these diameters during hydration and MIP

measurements can be conducted to validate this model.

The last reduction factor 3 refers to the amount of water

available to accommodate the ions that develop during the

chemical reaction of cement and pozzolans (Fig 6). The

reduction of the amount of water in the hydrating paste is

considered to cause a shortage of water for the ions to move

through the microstructure and react to another phase. This socalled water shortage concept also causes a reduction of the

rate of hydration due to the consumption of water by cement

and pozzolans and can be calculated according to:

wbr

mwmwwbr pp

jpc

c

jc

3

(12)

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Fig 6. Effect of3 on the reaction process versus the degree of

hydration for different water to cement ratios.

where wbr is the water to binder ratio, mc and mp the mass

fractions of cement and pozzolans respectively. The factorswc

and wp refer to the water to cement ratio that at which either the

cement or the pozzolanic phase is completely hydrated if al

cementitious has hydrated (=1). For both cement and

pozzolan a factor 0.4 can be adopted.

With the basic rate equation as described in a simple form with

eq. (9), the formulations of the water dependency (1 to 3),

and the Arrhenius equation F1 for the temperature dependency

of the reactions, the integrated kinetics approach can be applied

to all particles that are part of the particle size distribution

including both the cement and pozzolanic particle fractions.

The calculation procedure should account for the incremental

increase of the hydration process and associated changes in the

microstructure, capillary water and the chemistry. Figure 7shows an schematic overview of the different calculation steps

that are considered in the calculation of the cement reactions.

To include the secondary pozzolanic reactions in the model,

both the cement chemistry and the secondary pozzolanic

reactions have to be described explicitly. For the cement

reactions the following reaction equations are considered [3]:

/C S ( ( / ) )H C SH ( ( / ))CHb C S xb C S x b C S (13)

where b = 2 or 3 represents reaction of C3S or C2S, respectively.

For the numerical calculations in this paper C/S = 1.8 and x = 4

is adopted. Reactions of aluminate-bearing clinker minerals are

represented by the following sequential chemical reaction

schemes:

3 2 6 3 32C A+3CsH +26H C As H (14)

3 6 3 32 4 12C A+0.5C As H +2H 1.5C AsH (15)

3 3 6C A+6H C AH (16)

4 2 6 3 32 3C AF+3CsH +30H C As H +CH+FH (17)

4 6 3 32 4 12 3C AF+0.5C As H +6H 1.5C AsH CH FH (18)

4 3 6 3C AF+10H C AH +CH+FH (19)

When all gypsum is consumed ettringite transforms to

monosulfate according to eqs. (15 and 18). After both gypsum

and ettringite are consumed, the remaining aluminates react

according to eqs. (16 and 19). For a dominating SiO2 secondary

pozzolanic reaction the following relation for the chemica

reaction holds:

xCH + S + (y-x)H CxSHy (20)

where the CH produced by the cement reaction reacts with the

SiO2 content of the pozzolan and water to a C-S-H gel. For

pozzolans with a high content of amorphous SiO2, this C-S-H

gel has about the same structure as the C-S-H gel formed by the

cement reactions.

Fig 7. Schematic representation of the cement reaction process.

For other compositions of pozzolans this may change. The

amorphous SiO2 content in pozzolans can change significantly

and depend on the type of material. Table 1 gives an overview

of the amorphous SiO2 content of pozzolans.

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Table 1: SiO2 content in pozzolans.

Pozzolan Content SiO2 [% m/m]

Slag 35-40

Silica fume 8498

Fly-ash 40-65

Sugarcane bagasse 42-49 coarse

34-43 fineRice husk ash >85%

The pozzolans that dominate in amorphous SiO2 is silica fume

and also rice husk ash shows a relatively high SiO2 content.

Later in this article the model will be validated by using silica

fume as a pozzolan.

EXPERIMENTSThe reference cement is composed only of the mixture of CEM

G cement, while the blend was produced with partial

replacement of Portland cement by 8 % mass of SF. The water

to cement ratio was 0.44. The curing of hydration was

conducted at a temperature of 20 C. In order to test the modelfor simulating the hydration of blended pozzolanic systems the

numerical results are compared with laboratory experiments by

means of the development of the amount of calcium hydroxide

CH. The amount of CH liberated during hydration is

determined by TGA TA Instruments SDT Q600, measuring the

mass loss near 430 C. From these experiments the CH data

liberated during plain paste and blended paste hydration after

different ages were obtained. The results are used for

preliminary testing of the numerical model for hydration

blended cement.

DISCUSSION OF RESULTSAll thermogravimetric (TG) measurements showed a mass loss

at a low temperatures caused by the dehydration of CSH andaluminate phases [4], loss at around 400 oC due to the

dehydration of Ca(OH)2, a mass loss around 600 C attributed

to the decomposition of poorly-crystallized carbonated product.

An example of TG experimental data curve for PC hydration

after 28 days is given in Figure 8. In the TG the mass loss

around 400 oC was related to the stoichiometry of the Ca(OH)2

de-hydroxylation as obtained from TG analysis employing a

tangential approach [5]. The result was related relatively to the

mass of binder obtained after firing at 1000 oC. Figure 9 shows

the development of portlandite (CH) as a function of time. Two

data points series are plotted, corresponding to the reference

and blended paste (where cement was replaced by 8 mass % of

SF). For the hydration of reference cement paste the quantity ofCH produced increases continually with the hydration time. In

blended system, however, the CH quantity reaches a maximum

(at 7 days), which is still much lower than the quantity reached

by reference cement paste hydration, and begins to decrease

with further hydration (Fig. 9). These results are consistent with

the reaction of SF with CH (Eq. 20) produced by the hydration

of clinker (silicate phases, Eq. 1). Ca(OH)2 is consumed and

used for the formation of pozzolanic C-S-H.

Fig 8. An example of TG experimental data for PC hydration

after 28 days.

This chemical process affects, therefore, also the amount of C-

S-H formed as well as the microstructure development. In Fig 9

it can be also observed that at early ages, until 1 day o

hydration, the reference cement has a lower content of CH than

the blended one, while after 1 day the situation is reversed, the

reference cement has now a higher amount of CH than the

blended one. Until 1 day of hydration SF acts as an accelerator

(filler) only, while later the effect of pozzolanic reaction is

visible by a high CH consumption. The obtained results are in

accordance with literature. Dobson et al. [6] also found by the

NMR experiments

Fig 9. Comparison of hydration simulation against

experimental results for calcium hydroxide of reference and

blended paste hydration (water/binder ratio is 0.44 and the

replacement of silica fume is 8 %).

200 400 600 800 100080

85

90

95

100

CaCO3

TG,%

Temprature,oC

Ca(OH)2

0.01 0.1 1 10 100

0.00

0.05

0.10

0.15

0.20

Hydration time, days

CH,g/gbinder

Experimental:

Reference CemG

SF 8%

Simulation:

Reference CemG

SF 8%

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that the presence of SF particles greatly accelerates the

hydration of C3S during first 24 h. The fundamental

understanding of the acceleration of the clinker (PC) hydration

in the presence of the silica is still not yet clearly defined. The

causes may be attributed to the thickness and densification of

the shell of hydration products forming around the dissolving

clinker particles. The acceleration of early hydration of PC

could be ascribed to the fineness of the SF particles that would

provide preferential nucleation sites.

SIMULATIONSIn order to test the potential of the model to simulate the

hydration of blended pozzolanic systems the output results are

compared with the obtained experimental data. For modeling

purposes it was assumed that the cement has a mineralogical

composition of 60 mass % of alite (C3S), while hydration

reactions of other phases (C2S, C3A and C4AF) were neglected.

For modeling we used Rosin-Ramler distribution curve. The

reactive (amorphous) constituent of the SF is assumed to be 95

% of the SiO2 content. Each individual hydration reactionkinetics for C3S and SiO2 was modeled according to BRE (Eq.

11) with a corresponding set of kinetic input parameters (Knucl.,

K0, tr, and 1). Kinetic parameters used for reference C3S and

blended hydration system employed for hydration simulation

are given in Table 2, whereas the input parameters for the

particle size distribution (PSD) for both cement and silica fume

are described in Table 3.The free outer growth of the particle

expansion can be calculated according to stoichiometry and

densities of components in the reaction equation. The

expansion factor for C3S reaction, in this first approach, was

considered to be c = 2.2, thus assuming both C-S-H and CH

reaction products to grow in the shell around the C3S particles.

Recently, in the 3D kernel, separate nucleation and growth of

CH particles in a free capillary pore space was implemented,

thus allowing a more realistic microstructural description as

regards to this issue, however with a high price on

computational efficiency. For the pozzolanic reaction the

expansion factor of p = 3.77 is used [7]. In the blended model

the volumetric expansion related to the C3S reaction is effected

by the pozzolanic reaction due to the consumption of CH, and

therefore the value 2.2 must be corrected in each time

increment in order to consider the interaction with the

pozzolanic reaction. Furthermore, it should be noted that the

particle size distribution of the cement and silica fume are

considered as independent phases.

Table 2: Reaction kinetic parameters

System Phase K0,

m/h

tr,

m

1

Reference C3S 0.09 6 2

Blended C3S 0.13 13 4

SF 0.002 1 4

Table 3: PSD input values for C3S and SF particle.

Phase n b Blaine,

m2 kg-1

Range,

m

Fraction

width,

m

Cem G 1.101 0.0267 320 1 - 90 1

SF 2.00 0.04 - 1 - 10 1

MODEL VALIDATIONThe modeling approach presented in this paper is a valuable

tool that can be employed to test hypothesis on fundamenta

mechanisms involved in pozzolanic hydraion systems. Here the

model was tested and validated against a limited amount of

experimental data. The validation of the multicomponen

kinetic model coupled with the evolving 3-D microstructure

incorporating pozzolanic fillers calls for a comparison of the

evolution of the component fractions (e.g. reactants and

hydration products) over time with the equivalent experimenta

data. For crystalline phases, quantitative X-ray diffraction

appears to be the most straightforward means for obtaining

phase quantification. This would be particularly useful for thePC minerals and crystaline hydration products such as CH

SEM/image analysis is also a useful technique for analyzing

real microstructures at various hydration ages

Thermogravimetric analysis provides data on the water released

at different temperatures, from which one can quantitatively

estimate the CH content of pozzolanic pastes. 29Si NMR [8] is

the only direct method for obtaining the reactivity o

amorphous silica. Combination of this techniques will be used

in future studies in order to validate and further improve the

pozzolanic modeling approach presented here. When

considering the development of the chemical phases the mass

of calcium hydroxide (CH) per gram of cement can be

calculated with the model and the results compared withexperimental data. Figure 9 shows the development of CH as a

function of time for both the reference and blended paste and

the results are compared with laboratory experiments. The

pozzolanic reaction between CH liberated by the C3S phases

and the secondary reaction with water and SiO2 phase turned

out to lead to a reduction of CH. Calcium hydroxide is

consumed and used for the formation of pozzolanic C-S-H

This chemical process affects, therefore, also the amount of C-

S-H formed in the microstructure. Good agreement with

experimental data could be reached for both systems. From the

simulated and experimental results it can also be observed that

for blended system the amount of CH in system reduces after 7

days of hydration. Justnes [8], Papadakis [9], and Yajun andCahyadi [10] show for different silica fume blended systems

that the CH content liberated after hydration may reach a

maximum and depending on the amount of replacement and

water binder ratio may even reduce to zero amounts indicating

the potential influence of pozzolanic reactions in paste. Our

simulation results indicated that for 25 % addition of SF the CH

reached the zero value after 65 days of hydration. Figure 10

shows the degree of hydration for both the plain paste and the

blended system. The results show the hydration of the clinker

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Fig 10. Simulation of a degree of hydration reactions of

reference and blended cement paste with 8 % silica fume (SF).

phase C3S and the hydration of the pozzolanic phase SiO2. In

the model algorithm, these phases are independent meaning that

unique behavior of these phases is explicitly described which is

a true necessity for modeling pozzolanic hydration. The model

accounts for the effect of SF addition on the acceleration of PC

kinetics. The increase in the kinetics of PC hydration due to SF

addition was considered in this paper by increasing the C3S

kinetic parameter from 0.09 to 0.13. The proposed model is

flexible to simulate the simultaneous hydration reactions of a

multicomponent system. More experimental data on kinetics of

PC and SF reactions are needed in order to draw further

conclusions. Figure 11 depicts the evolution of the simulated

avarage Ca/Si molar ratio of the overall C-S-H hydrationproduct with hydration time. The Ca/Si molar ratio starts to

decrease when the pozzolanic reaction is activated at

Fig 11. Simulated avaraged Ca/Si molar ratio of the overall C-

S-H hydration product.

about 9 h, because of the precipitation of C1.1SH (20) while PC

precipitates C1.8SH (13). Moreover, the model is capable o

simulating the further decrease in Ca/Si ratio that could happen

when there is not a sufficient amount of CH available in the

system.

CONCLUSIONThe pozzolanic model described in this paper shows the

potential to use growing spheres numerical simulation models

to simulate pozzolanic reactions in blended cement systems

The model is implemented in the simulation model Hymostruc

and integrated in the 3D kernel. The simulated results show

good agreement with obtained experimental data, achieved

from TGA laboratory experiments for CH liberation during

hydration of blended paste systems as measured in the LabEST

laboratorium in at COPPE-FRJ in Rio de Janeiro. Further

testing of the multi-component hydration kinetics mode

incorporating other types of reactive pozzolanic fillers requires

a comparison of the simultaneous evolution of the reactants and

associated hydration products, and more systematicexperimental data.

ACKNOWLEDGMENTSThis work was financially supported by the COPPE-UFRJ

M&E at TU Delft, and the Marie Curie Actions EU grant FP7-

PEOPLE-2010-IEF-272653-DICEM

REFERENCES[1] Breugel, K. van, 1991, Simulation of Volume Changes in

Hardening Cement-Based Materials, PhD, TUDelft.

[2] Koenders E.A.B., 2006, Stereology-based Modelling o

Blended Cement Microstructures, Internal report nr

25.5-06-09, TU Delft, The Netherlands.

[3] Ukrainczyk N. Koenders, E.A.B. and Breugel, K. van

2012, Multicomponent Modelling of Portland Cemen

Hydration Reactions, IICCRRR confe, Cape Town, SA.

[4] R.V.S. Ramachandran: Applications of Differentia

thermal analysis in Cement Chemistry, Chemica

Publishing Company NY (1969).

[5] B.K. Marsh, R.L. Day, (1988). Cement and Concrete

Research 18(2) 301-310.

[6] C.M. Dobson, D.G.C. Goberdhan, J.D.F. Ramsay, S.A

Rodger: J. Mat. Sci. Vol. 23 (1988) p. 4108-4114.

[7] Lothenbach, B., Scrivener, K., Hooton R.D.

"Supplementary cementitious materials", Cem Concr Res

41(12) (2011) 1244-1256.

[8] Justnes H. (2002). Condensed silica fume as a cemenextender. In: Bensted, J., Barnes, P. (Eds.), Structure and

Performance of Cements 2nd ed. , pp. 399-408.

[9] Papadakis, V. G. (1999). Experimental investigation and

theoretical modeling of silica fume activity in concrete

Cement and Concrete Research 29 7986.

[10] Yajun, J. and Cahyadi, J. H. (2004). Simulation of silica

fume blended cement hydration , M and S 37, 397-404.

0.01 0.1 1 10 100

0.0

0.2

0.4

0.6

0.8

1.0

Degreeofre

action


Reference:

C3S

Blended:

SF

C3S

0.01 0.1 1 10 100

1.60

1.65

1.70

1.75

1.80


AvaragedCa/SimolarratioofCSH

2013_OMAE2013-10916

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