impact of sodium sulfate solution on mechanical properties and structure of fly ash based...
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ORIGINAL ARTICLE
Impact of sodium sulfate solution on mechanical propertiesand structure of fly ash based geopolymers
Zvezdana Bascarevic • Miroslav Komljenovic •
Zoran Miladinovic • Violeta Nikolic •
Natasa Marjanovic • Rada Petrovic
Received: 23 August 2013 / Accepted: 29 April 2014
� RILEM 2014
Abstract In this paper, geopolymers based on two
different fly ash samples were exposed to sodium
sulfate (Na2SO4) solution (50 g/l) over a period of
365 days. It was found that sulfate solution attack
caused a small decrease in strength of geopolymer
mortars. Analysis of the Na2SO4 solutions by optical
emission spectroscopy indicated that exposing of the
geopolymer samples to the Na2SO4 solution had
caused leaching of one of the elements of the
aluminosilicate gel, silicon. Mineralogical analyses
of geopolymer samples did not show formation of any
new phases due to a reaction with sulfate ions.
Changes in aluminosilicate geopolymer gel due to
sulfate attack were investigated by electron micros-
copy and nuclear magnetic resonance. It was found
that treatment of geopolymer samples with the sulfate
solution caused breaking of –Si–O–Si– bonds in
aluminosilicate gel structure. Breaking of the –Si–
O–Si– bonds and leaching of Si were consequences of
the increase in the pH value of sulfate solution during
testing.
Keywords Geopolymer � Fly ash � Durability �Sulfate attack
1 Introduction
Alkali activated materials (AAM) are relatively new
group of binder materials. They are formed by the
reaction of different silicate materials with alkaline
solutions. Geopolymers are part of the group of AAM
generated by alkali activation of aluminosilicate
materials such as metakaolin or fly ash (FA). Geo-
polymers are characterized by highly cross-linked
three-dimensional aluminosilicate structure (geopoly-
mer gel), in which the negative charge of aluminum in
tetrahedral coordination is neutralized by alkali metal
ions [1, 2]. In order to widespread the uses of AAM as
alternative binder materials, these materials are
expected to meet all the requirements in terms of
quality and durability specified for Portland cement.
One of the durability requirements is resistance to
sulfate attack.
It is well known that sulfate ions from natural or
waste water may cause deterioration of building
elements based on hydrated Portland cement. During
the contact of hydrated Portland cement with sulfate
Z. Bascarevic (&) � M. Komljenovic �V. Nikolic � N. Marjanovic
Institute for Multidisciplinary Research, University of
Belgrade, Kneza Viseslava 1, 11030 Belgrade, Serbia
e-mail: [email protected]
Z. Miladinovic
Institute of General and Physical Chemistry, Studentski
trg 12-16, 11000 Belgrade, Serbia
R. Petrovic
Faculty of Technology and Metallurgy, University of
Belgrade, Karnegijeva 4, 11000 Belgrade, Serbia
Materials and Structures
DOI 10.1617/s11527-014-0325-4
solution, diffusion of sulfate ions into the structure of
the hardened cement occurs, followed by a reaction
with some of the phases present in the structure. The
main products of sulfate attack on hydrated Portland
cement structure are gypsum, ettringite, thaumasite or
mixtures of these phases [3]. The formation of these
phases can cause stress, strength loss, expansion and
finally deterioration of the material. Sulfate attack on
hydrated Portland cement is usually a slow process.
Occurrence and the extent of deterioration of hardened
Portland cement structure in contact with sulfate
solution depend on many factors: type of Portland
cement, water/binder ratio, pH of the sulfate solution,
concentration of sulfate ions, cation accompanying the
sulfate ions, temperature etc. [4–6]. Although there are
numerous investigations on the effects of sulfate
solutions on hydrated Portland cement structure [4], at
the moment, there is no standard method in Europe for
testing the resistance of cementitious materials to
sulfate attack [7].
Currently, there is also an ongoing work on
providing recommendations regarding appropriate test
methodologies for testing durability of AAM [8]. One
of the areas which will be given special attention is
sulfate attack on AAM. Previous investigations on
sulfate attack on AAM were carried out mainly in
sodium sulfate solutions in concentrations of 44–50 g/l
[9–15]. Several studies used also magnesium sulfate
(MgSO4) solution [13–16]. Other experimental con-
ditions, in terms of type of AAM samples (paste,
mortar or concrete), sample size, sulfate solution/
AAM samples ratio, duration of testing, testing
conditions (agitation and/or renewal of the sulfate
solution, the pH value of the solution) varied from one
study to another.
Most of the previous studies concluded that AAM
are quite resistant to sulfate attack, especially to the
attack of Na2SO4 solution [9, 11–13, 15]. In particular,
the investigations of the action of Na2SO4 solution on
aluminosilicate AAM, geopolymers, have shown that
this solution has little impact on the mechanical
properties of the material [2, 9, 11, 13]. However, in
several cases, it was observed that exposure to Na2SO4
solution had caused decrease or fluctuations in the
strength of the geopolymer samples [9, 14]. These
changes in the mechanical properties of the geopoly-
mer samples have been attributed to diffusion of alkali
metal ions from the geopolymer structure into the
sulfate solution [9, 14].
It is often stated that geopolymers are generally more
resistant to chemical corrosion than Portland cement [2].
Mineral (phase) composition and microstructure of
geopolymers differ significantly from the structure of
hydrated Portland cement, as well as degradation
processes of the materials [2, 11]. The main product of
geopolymerization reaction is alkali aluminosilicate gel,
which is responsible for good mechanical properties and
high chemical durability of geopolymers. However,
geopolymer gel is amorphous and X-ray structural
analysis (XRD) provides only limited information about
geopolymers‘ structure. Valuable pieces of information
about the structure and composition of the aluminosil-
icate geopolymer gel were obtained by infrared spec-
trometry (IR) and electron microscopy [17–19]. An
instrumental technique that has, over the last decade,
contributed substantially to the understanding of the
structure of geopolymer gel is nuclear magnetic reso-
nance (NMR) [20–22].
In previous research works, effects of Na2SO4
solution on geopolymers‘ structure were studied by
electron microscopy and infrared spectroscopy [9, 11,
14]. Electron microscopy of alkali-activated FA, after
being exposed to Na2SO4 solution for 365 days,
showed crystals of Na2SO4 salts in the pores of the
material [11]. This was attributed to the migration of
ions from the solution [11]. An earlier study showed
that, after the exposure of alkali-activated metakaolin
to the effects of various aggressive solutions (deion-
ized water, sea water, sulfuric acid, Na2SO4 solution),
no significant changes in the structure could be
detected by the IR analysis of the material [9].
However, based on infrared analysis of FA based
geopolymers, Bakharev concluded that sulfate attack
had caused an increase of a chain length of alumino-
silicate gel [14]. The same study showed that, when
sodium silicate was used as an alkaline activator,
exposure of the geopolymer samples to Na2SO4
solution resulted in increase of the Si/Al atomic ratio
in the aluminosilicate gel [14]. Nevertheless, although
the sulfate solution was analyzed by optical emission
spectroscopy, which confirmed the diffusion of alkali
ions from the geopolymer structure into the sulfate
solution, aluminum ions were not detected (or were
not analyzed), which would corroborate the results of
the infrared analysis [14].
On the other hand, it is well known that the extent of
the structural changes caused by sulfate attack on
building materials depends significantly on the quality
Materials and Structures
of the material [3–5, 7]. Chemical durability of
building materials is strongly affected by their
permeability, i.e. porosity [3]. It is recommended that
testing of the resistance of hydrated Portland cement to
sulfate attack should be performed on mortars
prepared with high water/cement ratio [7]. One recent
study on the effects of sulfate solutions on AAM
structure also showed that decreasing the water/binder
ratio increases the resistance to sulfate attack [15].
In our study, effects of the sulfate solution on
mechanical properties and structure of geopolymers were
studied on the geopolymer samples based on two
different alkali activated FA samples. The selection of
the FA samples was based on our previous research work,
which showed that, due to different reactivity of various
FA samples, geopolymer mortars with different mechan-
ical properties were obtained by alkali activation of the
FA samples [23, 24]. Different FA samples required
different amounts of water in order to obtain equal
workability of mortars [23, 24]. In this work, selection of
the two different FA samples for the synthesis of the
geopolymer samples enabled us to examine the impact of
the sulfate solution on geopolymers of different quality,
i.e. different initial strength and porosity.
The geopolymer samples were exposed to the effects
of the Na2SO4 solution (50 g/l) over a period of 365 days.
Any changes in the geopolymer gel due to sulfate attack
were studied using 29Si MAS NMR. Changes in the
sulfate solution were monitored by measuring the pH
values and testing the composition of the solution using
optical emission spectrometry. Formation of any new
phases in the structure, due to a reaction with sulfate ions,
was investigated by XRD of the material. Furthermore,
changes in the geopolymers‘ structure were examined by
scanning electron microscopy (SEM).
The aim of this work was to investigate the effects
of Na2SO4 solution on mechanical properties and
structure of FA based geopolymers and to determine
whether the exposure of the geopolymer samples to
the sulfate solution results in changes in the alumino-
silicate geopolymer gel.
2 Materials and methods
2.1 Materials
In this study, two FA samples from Serbian thermal
power plants (TPP) were used: FA Svilajnac TPP
‘‘Morava’’, Svilajnac and FA Kolubara, TPP ‘‘Kolu-
bara’’, Veliki Crljani. In order to increase the amount
of the more reactive FA particles, fractions of the FA
samples smaller than 63 lm were used [23].
Alkaline activator was sodium silicate with silicate
modulus (SiO2/Na2O mass ratio) of 3.04 (‘‘Galenika-
Magmasil’’, Serbia, 8.72 % Na2O, 26.5 % SiO2,
64.78 % H2O). Silicate modulus of the activating
solution was adjusted by adding 10 M solution of
NaOH (‘‘ZorkaPharm’’, Serbia, p.a. 98 %).
Sulfate solution was prepared using Na2SO4 of
99 % purity (Superlab, Serbia).
2.2 Preparation of geopolymer samples
Sodium silicate solution with modulus of 1.5 was used
as an activating solution. The activator solution/FA
ratio was the same for all the geopolymer samples with
10 % Na2O content with respect to the FA mass [23].
Geopolymer mortars were prepared by adding the
silicate solution to water and then mixing the solution
with FA and sand. Different amounts of water were
required in order to obtain equal workability of the
mortars based on the two FA samples (mortar flow
measured on a flow table was 125 ± 5 mm), so the
water/FA ratio was 0.56 for the mortars based on FA
Svilajnac, and 0.76 for the mortars based on FA
Kolubara (water in water/FA ratio was calculated as
water from sodium silicate solution ? water added for
consistency). Sand/FA ratio was 3/1. The molds with
three mortar prisms (40 9 40 9 160 mm) were
placed in plastic bags to avoid moisture loss during
curing. Geopolymer mortars were cured at 95 �C for
24 h. The curing temperature was selected after an
extensive optimization of the geopolymer synthesis
conditions for the FA samples used in this study.
Previously, curing of the geopolymer samples based
on FA Kolubara and FA Svilajnac was performed at
room temperature for 1 day followed by curing at
55 �C for 6 days [23] and at 55, 80 and 95 �C for 24 h
(unpublished data). It was found that the highest
compressive strengths of the geopolymer mortars were
achieved after curing of the samples at 95 �C for 24 h.
Geopolymer pastes were prepared by mixing the FA
with the alkaline activator solution in the same
proportion as in the preparation of the geopolymer
mortars. Water/FA ratio was 0.49 for the pastes
prepared with FA Svilajnac and 0.69 for the pastes
based on FA Kolubara. Dimensions of the paste
Materials and Structures
samples were 25 9 25 9 30 mm. Curing conditions
were the same as for the geopolymer mortars.
Nine series of geopolymer mortar and paste sam-
ples were prepared based on both of the FA samples
(Table 1). The first samples were tested after curing at
95 �C for 24 h (starting samples). Eight series of
mortar and paste samples were prepared for testing
two groups of samples after four terms: 28, 90, 180 and
365 days. The first group was cured in the humid
chamber (temperature 20 ± 2 �C, humidity *98 %)
and will be hereinafter referred to as reference
samples. The second group of samples was exposed
to the Na2SO4 solution.
After the period of curing, (in the humid chamber or
in the Na2SO4 solution), in order to stop further
reaction, the paste samples were crushed and milled
(Netzsch Pulverisette) in isopropyl alcohol for 60 min.
After milling, the samples were washed with acetone,
dried at 50 �C for 60 min and packed in plastic bags.
Paste samples were prepared for scanning electron
microscopy (SEM) characterization by soaking the
fragments of the samples in isopropyl alcohol for 24 h
and drying at 50 �C for 60 min afterwards.
2.3 Experimental design
The Na2SO4 solution (50 g/l) was prepared by
dissolving of Na2SO4 in distilled water. Series of the
three geopolymer mortar prisms and the correspond-
ing paste sample were immersed in sealed plastic
containers with sulfate solution and kept at 20 ± 2 �C
for a period of up to 365 days. In order to ensure that
the entire sample surface was in contact with the
solution, geopolymer samples were placed on plastic
nettings (thickness 0.5 cm, hole size *3 cm). Solu-
tion/geopolymer mass ratio was 4/1. The sulfate
solutions were not renewed during the experiment,
thereby static testing conditions were established.
Instead, testing was performed for a longer period of
time (365 days), with high sulfate solution/geopoly-
mer samples ratio (4/1) and with high concentration of
the sulfate ions (50 g/l Na2SO4) in the solution.
2.4 Analytical methods
Chemical composition of the starting FA samples was
determined by energy dispersive X-ray fluorescence
spectrometer ED2000, Oxford instruments. The particle
size distribution (content of the particles smaller than
43 lm) was determined by sieving the FA samples
through the mesh. Compressive strength of the geo-
polymer mortars was tested according SRPS EN 196-1
[25] using Tony Technik (Toninorm) testing machine.
Nitrogen adsorption–desorption isotherms were
determined using a Micromeritics ASAP 2020 instru-
ment. Testing was performed on the powdered mortar
samples. The samples were crushed to pass through
100 lm sieve. Samples were degassed at 105 �C for
10 h under reduced pressure. The total pore volume
was given at p/p0 = 0.998. Specific surface areas of
the geopolymer samples were obtained by applying
the Brunauer–Emmett–Teller method.
The pH values of the Na2SO4 solutions before and after
the testing of the geopolymer samples were measured by
pH-meter (pH Testr30, Eutech Instruments).
The inductively coupled plasma optical emission
spectrometer (ICP-OES, SpectroGenesis EOP II,
Spectro Analytical Instruments GmbH, Kleve) was
used to determine the ion exchange between the
geopolymers and the Na2SO4 solutions. Prior to
analysis, Na2SO4 solutions were diluted with deion-
ized water in ratio 1:100. The concentration of each
element was calculated as the difference between the
concentration measured after curing the geopolymer
Table 1 Sample labels
Time (days) FA Svilajnac FA Kolubara
Humid chamber Sulfate solution Humid chamber Sulfate solution
0* G-Svil-0 G-Kol-0
28 G-Svil-Ref-28 G-Svil-S-28 G-Kol-Ref-28 G-Kol-S-28
90 G-Svil-Ref-90 G-Svil-S-90 G-Kol-Ref-90 G-Kol-S-90
180 G-Svil-Ref-180 G-Svil-S-180 G-Kol-Ref-180 G-Kol-S-180
365 G-Svil-Ref-365 G-Svil-S-365 G-Kol-Ref-365 G-Kol-S-365
* Samples cured for 24 h at 95 �C
Materials and Structures
samples in the Na2SO4 solution and the initial element
concentration in the same solution. Testing of the
sulfate solutions in which mortars based on FA
Kolubara were cured was performed in the same
terms as the compressive strength tests (28, 90, 180
and 365 days). The compositions of the Na2SO4
solutions in which FA Svilajnac geopolymers were
cured, except in these terms, were tested after 7 and
60 days, in order to further investigate the changes in
the initial period of curing.
XRD was performed by Philips PW 1710, with
CuKa X-rays operating at 30 mA and 40 kV, with
0.02� 2h steps, 0.5 s step-1 in 5–50� 2h range.
Morphological characterization of the geopolymer
samples was done by SEM (VEGA TS 5130 MM,
Tescan). Energy dispersive X-ray spectroscopy (EDS)
was performed by INCAPentaFET-x3 (OXFORD
Instruments). The samples were Au–Pd coated. Sam-
ples for EDS analysis were prepared by grinding and
polishing (MTI Corporation) of epoxy impregnated
samples. Grinding was done using SiC grinding papers
(300, 600, 1,200 and 2,000 grit, 3 min each) with
acetone as lubricant. Final polishing of the samples
was done using polishing cloths and diamond pastes
(0.5 lm and 0.25 lm, MTI Corp., 3 min each).29Si MAS NMR spectra were obtained at Larmor
frequency of 79.49 MHz using Bruker MSL 400
system, Apollo console upgraded (Tecmag). Single
pulse sequence was used for data acquisition with
pulse width of 4 ls, corresponding to p/2 flip angle.
Recycle time was typically 20 s, the number of scans
was 4,096 and the spectral width was 20,000 Hz for all
recorded spectra. Chemical shifts were externally
referenced to 2,2-dimethyl-2-silapentane-5-sulfonate
(DSS) standard. Gaussian peak deconvolution of the
obtained spectra was performed using DMFIT appli-
cation [26]. Prior to 29Si MAS NMR analysis, iron
content of the geopolymer samples was reduced by
exposing the samples to a strong magnetic field.
3 Results and discussion
3.1 Properties of the starting FA and geopolymer
samples
Chemical composition of the starting FA samples and
content of fine FA particles (smaller than 43 lm) in the
samples are given in Table 2. Both FA samples were
class F [27]. Although a fraction of less reactive FA
particles in both of the starting FA samples was reduced
by sieving [23], FA Svilajnac still contained a signif-
icantly higher amount of fine particles (Table 2). Due to
different properties of the starting FA samples, geo-
polymer mortars with different properties were obtained
by alkali activation of the FA samples (Table 3).
After 24 h of curing, geopolymer mortars based on
FA Svilajnac showed about two times higher com-
pressive strength compared to FA Kolubara geopoly-
mers. Also, porosity of these mortar samples was
significantly lower than porosity of mortars based on
FA Kolubara (Table 3). Different porosity of the
mortar samples is partially a consequence of different
fine particles content in the FA samples (Table 2). Due
to the different particle size distribution of the FA
samples, in the preparation of the mortar samples,
different quantities of water had to be added in order to
provide equal workability. Except for the higher
water/FA ratio, lower compressive strength of the
FA Kolubara geopolymer was also a result of mineral
composition of the FA samples. Previous mineralog-
ical characterization of FA Kolubara showed that this
FA sample had high content of quartz, a crystalline
phase which remains un-reacted during the alkali
activation reaction [24].
Table 2 Chemical composition (wt%) and particle size dis-
tribution of the starting FA samples
Chemical composition FA sample
Svilajnac Kolubara
LOI at 1,000 �C 1.51 2.08
SiO2 49.89 55.51
Al2O3 21.66 21.59
Fe2O3 6.87 6.30
CaO 9.71 8.05
MgO 2.88 2.87
SO3 1.12 0.76
MnO – 0.20
P2O5 – 0.05
Na2O 0.63 0.55
K2O 1.21 0.94
Total 95.48 98.90
SiO2 ? Al2O3 ? Fe2O3* 78.42 83.40
Particle content \43 lm 52.65 29.85
* According to [27]: SiO2 ? Al2O3 ? Fe2O3 C 70 % for class
F FA
Materials and Structures
3.2 Effects of the Na2SO4 solution on mechanical
properties of the geopolymers
Changes in the compressive strength of the geopoly-
mer mortars during the testing are shown on Fig. 1.
The results are presented as relative strength (relative
to the starting compressive strength after 24 h at
95 �C, Table 3).
Strength of both groups of the reference geopoly-
mer mortars (based on FA Svilajnac and on FA
Kolubara) increased with time. After 365 days of
testing, compressive strengths of both groups of
samples were approximately 15 % higher than the
starting strengths (Fig. 1).
Compressive strength of the FA Svilajnac geopoly-
mer mortars exposed to the effects of the sulfate
solution showed only slight changes during the first
180 days of testing. A more significant reduction in
strength of these mortar samples was noticed after
365 days of testing (strength loss of about 12 %,
Fig. 1a). On the other hand, the strength of the FA
Kolubara mortars decreased already after the first
28 days of exposure to the Na2SO4 solution (by about
10 % compared to the strength of the starting samples,
Fig. 1b). After an initial decrease in strength, the
subsequent investigation showed there was a notice-
able strength increase of the FA Kolubara geopolymer
mortars, i.e. a structural recovery occurred.
Differences in strength changes of the geopolymer
mortars based on FA Svilajnac and FA Kolubara can
be explained by different porosity of the starting
mortar samples (Table 3). Due to the higher porosity
of the FA Kolubara mortars, ingress of the sulfate
solution into the geopolymer structure occurred more
rapidly. Characterization of the geopolymers‘ struc-
ture after the exposure to the Na2SO4 solution should
provide an explanation of the observed dependence of
the mortars strengths on the time of exposure.
3.3 Analyses of the Na2SO4 solution
The pH values of the starting sulfate solutions used in
this study were about 6 (Table 4). During the testing of
the geopolymer mortars, in contact with the samples,
pH values of the sulfate solution reached the value of
about 12 already after 28 days of testing. The observed
increase in pH of the sulfate solution is a result of
leaching of pore solution alkalis [9, 14, 28].
Table 3 Properties of the starting geopolymer samples
Geopolymer mortar Compressive strength,
24 h at 95 �C (MPa)
Specific surface area (m2/g) Porosity (cm3/g) Average pore
diameter (nm)
FA Svilajnac 43.1 ± 0.75 13.40 0.055 14.18
FA Kolubara 21.4 ± 0.49 27.58 0.160 22.05
Fig. 1 Strength of the geopolymer mortar samples: a FA Svilajnac geopolymers, b FA Kolubara geopolymers
Materials and Structures
By the ICP-OES analysis of the sulfate solutions
high and variable concentrations of S and Na were
detected. Generally, concentrations of S in the sulfate
solutions after the testing of the geopolymer samples
were lower than the initial S concentrations in the
solutions, while an increase in the concentration of Na
was observed (data not shown here). These results
were consistent with the findings of the previous
studies [9, 11, 14] and they indicated that diffusion of
sulfate ions in the geopolymers‘ structure and diffu-
sion of alkali metal ions from the structure into the
sulfate solution had occurred.
In addition to high concentrations of S and Na, the
results of ICP-OES analysis showed that exposing of
the geopolymer samples to the Na2SO4 solution had
caused leaching of one of the elements of the
aluminosilicate structure, silicon (Fig. 2). Leaching
of Si is probably less associated with an impact of the
sulfate ions than with the high pH of the sulfate
solution (Table 4). It is well known that the main
degradation mechanism of aluminosilicate glasses and
zeolites at high pH is hydrolysis of the siloxane bonds
(–Si–O–Si–) caused by a nucleophilic attack by OH-
at Si sites [29, 30]. Due to this phenomenon, treatment
with alkaline solutions is used for desilication of the
aluminosilicate structure of the zeolites with high Si/
Al atomic ratio [31–33]. One recent study showed that
exposure of alkali activated FA to highly alkaline
solution (14 M NaOH) resulted in a significant
leaching of Si [34]. Previous study on the effects of
alkaline solutions on geopolymers‘ structure and
properties found that treatment of fly ash based
geopolymers with solutions of up to pH 14 resulted
in a very small changes in the geopolymers‘ structure,
while in a more alkaline solution (pH[14) both silicon
and aluminum were leached [35]. However, the
authors noted that the investigated geopolymer sam-
ples had low silicate content in the activating solutions
(SiO2/Na2O ratios were 0.0, 0.2 and 0.79) and that the
geopolymer samples synthesized at a higher silicate
contents (SiO2/Na2O = 2.0) showed quite limited
resistance to immersion in alkaline solutions [35]. In
our work, sodium silicate with SiO2/Na2O ratio of 1.5
was used as the activator solution. High silicate
content in the activator solution is probably the reason
why leaching of Si was observed already in the
solution of the pH value of about 12 (Table 4). The
second element of the aluminosilicate structure,
aluminum, was not detected. The maximum concen-
trations of Si in the sulfate solutions (Fig. 2) were
detected in the same terms as the largest observed
decline in strength of the geopolymer mortars (Fig. 1).
These results suggest that Si was probably leached
from the aluminosilicate geopolymer gel.
3.4 Effects of the Na2SO4 solution on structure
of the geopolymers
3.4.1 XRD analysis
XRD analysis of the geopolymer samples after the
exposure to the Na2SO4 solution did not indicate
formation of any new phases formed due to a reaction
with sulfate ions (Fig. 3). Both the reference geopoly-
mer samples and the samples treated with the sulfate
solution contained only the phases originating from
the starting FA samples [24]: quartz, feldspar, anhy-
drite, hematite and mullite. The presence of calcite,
formed as a result of carbonation during curing, was
also detected. The intensity of calcite peaks increased
with the time of curing in the humid chamber. On the
Table 4 pH values of the Na2SO4 solutions
Time (days) Geopolymer samples
FA Svilajnac FA Kolubara
0 5.90 5.64
28 11.90 11.90
90 12.13 12.11
180 12.06 11.86
365 11.67 11.68
Fig. 2 Concentration of Si leached into the sulfate solution
Materials and Structures
other hand, while it seems that there was a decrease in
calcite peak intensity in the XRD patterns of the
G-Svil-S samples, no significant changes were
observed in the XRD patterns of the G-Kol-S samples.
Based on these results, it is difficult to draw a
conclusion on the role of calcite in sodium sulfate
attack on the FA based geopolymers. Previous studies
have shown that carbonation of Portland cement
concrete [36] and granulated blast furnace slag
concrete [37] prior to sulfate attack can increase their
sulfate resistance.
3.4.2 SEM and EDS analyses
By the SEM analysis of the geopolymer samples
Na2SO4 crystals (thenardite) were observed on the
fracture surface of the FA Kolubara geopolymer
samples after the exposure to the sulfate solution for
365 days (Fig. 4). The presence of Na2SO4 crystals is
probably associated with the migration of the sulfate
ions in the geopolymer structure, as noticed in the
previous study [11]. Thenardite crystals were
observed not only in the pores of the geopolymer
samples, but on the fracture surface of the sample as
well. The presence of the Na2SO4 crystals on the
surface of the sample suggests that the salt has
precipitated during the preparation of the sample for
the SEM analysis, since no washing of the samples
after the exposure to the sulfate solution has been
done. After the treatment with the Na2SO4 solution the
geopolymer samples were immediately crushed,
soaked in isopropyl alcohol and dried (Section 2.2).
Detailed EDS analysis of the polished geopolymer
samples confirmed the leaching of Na and Si from the
structure. The Si/Al and Na/Al atomic ratios of the
geopolymer samples treated with the Na2SO4 solution
were somewhat lower than the main atomic ratios of
the reference samples (Table 5).
3.4.3 NMR analysis
29Si MAS NMR spectra of the geopolymer samples
are shown in Fig. 5. Broad 29Si MAS NMR resonances
are typical for geopolymers [20, 38] and they indicate
poorly ordered aluminosilicate structure. A 29Si MAS
NMR spectra of FA based geopolymers consist of the
overlapping resonances attributed to silicon sites in
different silicate and aluminosilicate components
present in the material: aluminosilicate geopolymer
gel and un-reacted glassy and crystalline phases (e.g.
quartz, mullite) originating from the starting FA [21,
22, 24].
It is well known that the chemical shift at which
maximum peak intensity of the 29Si MAS NMR
spectrum occurs depends on the Si/Al atomic ratio of
the material [20, 39]. The 29Si MAS NMR spectra of
the starting FA Svilajnac geopolymer sample and the
reference samples after 28 and 365 days of curing
Fig. 3 XRD analyses of the starting geopolymer samples and the geopolymer samples after 28 and 365 days in the humid chamber and
in the Na2SO4 solution: a FA Svilajnac geopolymers and b FA Kolubara geopolymers
Materials and Structures
were centered at approximately -93 ppm (Fig. 5a).
Shifting of the maximum peak intensities of the 29Si
MAS NMR spectra of the geopolymer samples treated
with the Na2SO4 solution to higher frequencies (less
negative chemical shifts) indicated a decrease in the
Si/Al atomic ratio of these samples, i.e. confirmed
Fig. 4 SEM/EDS analysis of the G-Kol-S-365 sample
Table 5 EDS analysis of the geopolymer samples
Time (days) FA Svilajnac geopolymer samples FA Kolubara geopolymer samples
Reference samples Samples treated with
Na2SO4
Reference samples Samples treated with
Na2SO4
Si/Al Na/Al Si/Al Na/Al Si/Al Na/Al Si/Al Na/Al
1 2.86 (0.058)* 0.98 (0.043) 2.86 (0.058) 0.98 (0.043) 2.97 (0.011) 1.03 (0.017) 2.97 (0.011) 1.03 (0.017)
28 2.95 (0.034) 0.92 (0.003) 2.92 (0.039) 0.81 (0.015) 3.00 (0.053) 1.17 (0.034) 2.87 (0.033) 0.95 (0.015)
365 2.86 (0.051) 0.65 (0.008) 2.80 (0.041) 0.70 (0.012) 2.99 (0.042) 0.95 (0.027) 2.87 (0.021) 0.96 (0.018)
* Standard deviation
Fig. 5 29Si MAS NMR analysis of the starting geopolymer samples and the geopolymer samples after 28 and 365 days in the humid
chamber and in the Na2SO4 solution: a FA Svilajnac geopolymers and b FA Kolubara geopolymers
Materials and Structures
leaching of Si (Fig. 2). Results of the 29Si MAS NMR
analysis of the FA Svilajnac geopolymer samples
showed good correlation with the analyses of the
sulfate solution. The results of the ICP-OES analysis
showed that concentration of Si in the sulfate solutions
in which FA Svilajnac geopolymer samples were
cured increased with time (Fig. 2). Shifting of the
maximum peak intensities of the 29Si MAS NMR
spectra of the FA Svilajnac geopolymer samples
treated with the Na2SO4 solution from -92 ppm after
28 days to -90 ppm after 365 days in the solution
(Fig. 5a) confirmed that the Si/Al atomic ratio of these
samples decreased with the time of the treatment.
The maximum peak intensity of the G-Kol-0
sample 29Si MAS NMR spectrum was centered at
approximately -94 ppm (Fig. 5b). After curing of the
geopolymer samples in the humid chamber for
365 days, the maximum peak intensity of the 29Si
MAS NMR spectrum was shifted to approximately
-93 ppm (Fig. 5b). This was probably due to the
continuation of the alkali activation reaction, as
further dissolution of FA led to minor changes in the
composition of the aluminosilicate gel. A decrease in
the Si/Al atomic ratio of the samples treated with the
Na2SO4 solution was confirmed by shifting of the
maximum peak intensity of 29Si MAS NMR spectra to
less negative chemical shift. The 29Si MAS NMR
spectra of the G-Kol-S-28 and G-Kol-S-365 samples
were centered at approximately -92 ppm (Fig. 5b).
These results are consistent with the results of ICP-
OES analysis which showed that the concentration of
Si leached form the FA Kolubara geopolymers into the
sulfate solution changed only slightly after the first
28 days of investigation (Fig. 2).
It has become a common practice to quantify broad29Si MAS NMR spectra of geopolymers by means of
Gaussian deconvolution [20–22, 24, 40–42]. Decon-
volution of 29Si NMR spectra assuming constant line
widths for the Q4(mAl) peaks is commonly used for
zeolites and crystalline aluminosilicates [39], but
proved to be useful also for analyzing 29Si MAS
NMR spectra of alkali activated fly ash [21, 22, 24, 40–
42]. It is generally accepted that 29Si MAS NMR
spectra of geopolymers consist of all five Q4(mAl)
silicon species, with Q4(4Al), Q4(3Al), Q4(2Al),
Q4(1Al) and Q4(0Al) resonating at approximately
-84, -89, -93, -99 and -108 ppm, respectively
[20–22, 24, 38, 40–42]. The frequency of the individual
Q4(mAl) peaks varies depending on the Si/Al atomic
ratio of the material [39]. The peaks width is also
affected by changes in the Si/Al atomic ratio [20]: as the
Si/Al atomic ratio decreases, the peak width also
decreases. The 29Si MAS NMR spectra in this work
were deconvoluted using Gaussian line shapes, the same
number of peaks and constant line widths (Figs. 6, 7;
Tables 6, 7). The peak positions for each of the five
possible Q4(mAl) silicon species, ranging from 4 to 0 Al
neighbors, were adopted from the previous 29Si MAS
NMR studies of crystalline aluminosilicates [39] and
geopolymers [20–22, 24, 40–42]. The chemical shifts
and the peak widths were confined to those reported
previously [20–22, 40–42]. In addition to the Q4(mAl)
silicon peaks, in all the 29Si MAS NMR spectra in this
study a small resonances at approximately -78, -107.5
and -115 ppm were observed (Figs. 6, 7). A sharp
resonance at -107.5 ppm, indicating an ordered struc-
ture, can be attributed to quartz originating from the
starting FA [24, 39]. The small peak at -78 ppm is
usually ascribed to less condensed silicon species (Q1
and Q2) present in the material [21, 22, 39, 40]. The peak
at -115 pm is more difficult to identify and it can be
attributed to different silica polymorphs [41, 42] or to
Q4(0Al) units in the products of alkali activation
reaction [22].
Previous analysis of the 29Si MAS NMR spectra of
the reference FA Svilajnac geopolymer samples
showed that increase in compressive strength of the
reference geopolymer mortars was associated with a
small increase of peak areas of aluminum rich
components in the 29Si MAS NMR spectra,
Q4(mAl), m = 2, 3, 4 [24]. The results of the earlier29Si MAS NMR analyses of FA based geopolymer
samples showed that evolution of signals intensity of
individual Q4(mAl) components with reaction time
depends on the properties of the starting FA sample
[40], as well as on the composition of the activator
solution [21]. In our study, the activator solution with
high silicate content was used. It appears that contin-
uing of the alkali activation reaction of the investi-
gated FA Svilajnac geopolymer samples in the 29Si
MAS NMR spectra was manifested by an increase in
the fraction of aluminum rich components, Q4(mAl),
m = 2, 3, 4 (Table 6).
Deconvolution results of the 29Si MAS NMR
spectra of the FA Svilajnac geopolymer samples
treated with the Na2SO4 solution indicated a signifi-
cant decrease of peak areas of silicon rich components
in the 29Si MAS NMR spectra, Q4(mAl), m = 0, 1
Materials and Structures
(Table 6). Decrease in the fraction of the Q4(1Al) and
Q4(0Al) components was also observed in the 29Si
MAS NMR spectra of zeolites upon desilication
treatment [33]. The reduction of the signals intensity
of the silicon rich components in the 29Si MAS NMR
spectrum was attributed to the preferential leaching of
silicon which is not surrounded by aluminum in the
structure [32, 33]. Besides the observed decrease in
peak areas of the Q4(mAl), m = 0, 1 components, in29Si MAS NMR spectra of the FA Svilajnac geopoly-
mer samples treated with the Na2SO4 solution, an
increase in the fraction of less condensed silicon
species was observed (Q1 and Q2, Table 6). It seems
that breaking of –Si–O–Si– bonds and leaching of Si
had caused an increase in the fraction of silicon atoms
that are not involved in three-dimensional alumino-
silicate gel network, i.e. in Q4(mAl) structural units.
The observed decline in the strength of the
geopolymer samples in sulfate solution (Fig. 1)
resulted from the disruption in continuity of alumino-
silicate structure and the formation of structural
defects due to the leaching of Si.
Deconvolution of the 29Si MAS NMR spectra of the
reference FA Kolubara geopolymer samples showed a
more significant increase of peak areas of aluminum
rich components, Q4(mAl), m = 2, 3, 4 (Table 7),
compared to the deconvolution results of the FA
Svilajnac geopolymer 29Si MAS NMR spectra
(Table 6). Analysis of the deconvolution results of
the 29Si MAS NMR spectra of the FA Kolubara
geopolymer samples treated with the Na2SO4 solution
indicated a decrease in peak areas of the Q4(0Al)
components, as well as an increase in the fraction of
less condensed silicon species, Q1 and Q2, (Table 7).
The observed decrease in strength of the FA
Kolubara geopolymer mortars after 28 days of
Fig. 6 29Si MAS NMR
deconvoluted spectra of FA
Svilajnac geopolymers: a G-
Svil-0, b G-Svil-Ref-28,
c G-Svil-S-28, d G-Svil-
Ref-365, e G-Svil-S-365
Materials and Structures
exposure to the Na2SO4 solution was followed by a
structural recovery during further investigation
(Fig. 1). The increase in strength of the FA Kolubara
geopolymer samples is probably a result of continuing
of the alkali activation reaction in the sulfate solution.
Conditions to which the geopolymer samples were
subjected throughout the testing of the sulfate attack,
i.e. high concentration of Na in the solution and high
pH of the solution (Table 4) were favorable for
continuing the alkali activation reaction. The increase
in strength of the FA Kolubara geopolymer mortars in
the sulfate solution is consistent with the work of
Ismail et al., who investigated effects of sulfate
solutions on the structure of alkali activated fly ash/
slag mixture and suggested that geopolymer binder
continues to develop in the Na2SO4 solution [15]. A
similar phenomenon was observed during the expo-
sure of alkali activated slag to the effects of sulfate
solution, whereby an increase in strength of the
material in the Na2SO4 solution was attributed to the
continuing hydration [43]. However, no significant
differences could be observed by comparing the
deconvolution results of the 29Si MAS NMR spectra
of the G-Kol-S-28 and G-Kol-S-365 samples
(Table 7). As noted previously, 29Si MAS NMR
spectra of FA based geopolymers consist of the
overlapping resonances attributed to silicon sites in
aluminosilicate geopolymer gel and un-reacted FA.
Structural changes that occurred over extended expo-
sure of the FA Kolubara geopolymer samples to the
sulfate solution did not result in significant changes in29Si MAS NMR spectra of the geopolymer samples
(Figs. 5b and 7).
Nevertheless, the 29Si MAS NMR analysis of the
geopolymer samples provided useful information
regarding the degradation mechanism of geopolymer
gel in the sulfate solution. The 29Si MAS NMR
analysis of the geopolymer samples showed that,
Fig. 7 29Si MAS NMR
deconvoluted spectra of FA
Kolubara geopolymers: a G-
Kol-0, b G-Kol-Ref-28, c G-
Kol-S-28, d G-Kol-Ref-365,
e G-Kol-S-365
Materials and Structures
under the applied testing conditions, treatment of the
geopolymer samples with the Na2SO4 solution caused
breaking of –Si–O–Si– bonds and leaching of Si,
whereby breaking of –Si–O–Si– bonds occurred
preferentially in silicon rich components of the
aluminosilicate gel (Q4(0Al) and Q4(1Al) components
of the 29Si MAS NMR spectra, Tables 6 and 7).
However, the observed degradation of the geopoly-
meric material was not a result of reaction with sulfate
ions, but rather a consequence of the high pH values of
Table 6 29Si MAS NMR spectral deconvolution of the FA Svilajnac geopolymer samples (Fig. 6)
Geopolymer sample Q1, Q2* Q4(4Al) Q4(3Al) Q4(2Al) Q4(1Al) Q4(0Al) quartz** Q4**
G-Svil-0 d (ppm) -77.8 -84.0 -88.9 -94.2 -99.8 -106.9 -107.6 -115.2
Width (ppm) 7.0 7.0 7.0 7.0 7.0 7.0 1.2 7.0
Area (%) 2.9 9.0 22.4 27.4 21.6 13.0 1.2 2.7
G-Svil-Ref-28 d (ppm) -77.8 -84.1 -88.8 -94.1 -99.9 -107.1 -107.8 -114.0
Width (ppm) 7.0 7.0 7.0 7.0 7.0 7.0 1.2 7.0
Area (%) 2.4 9.2 22.3 27.9 22.0 12.4 1.2 2.8
G-Svil-S-28 d (ppm) -75.5 -82.5 -88.2 -93.7 -99.3 -105.6 -107.5 -110.0
Width (ppm) 6.8 6.8 6.8 6.8 6.8 6.8 1.0 6.8
Area (%) 3.5 11.4 25.6 27.8 18.7 9.7 1.2 2.1
G-Svil-Ref-365 d (ppm) -77.2 -84.2 -89.3 -94.8 -100.7 -107.9 -107.7 -116.1
Width (ppm) 7.0 7.0 7.0 7.0 7.0 7.0 1.2 7.0
Area (%) 2.8 9.2 22.3 28.6 20.5 11.8 1.0 3.8
G-Svil-S-365 d (ppm) -74.7 -82.3 -87.7 -93.1 -98.4 -104.8 -107.7 -109.0
Width (ppm) 6.6 6.6 6.6 6.6 6.6 6.6 1.3 6.6
Area (%) 4.5 12.5 27.1 28.2 17.8 6.6 1.2 2.1
* Less condensed silicon species, Q1 and Q2 [21, 22, 39, 40]
** Quartz (-107.5 ppm) and other Q4 silicon units [22, 39, 41, 42]
Table 7 29Si MAS NMR spectral deconvolution of the FA Kolubara geopolymer samples (Fig. 7)
Geopolymer sample Q1,2* Q4(4Al) Q4(3Al) Q4(2Al) Q4(1Al) Q4(0Al) quartz** Q4**
G-Kol-0 d (ppm) -78.7 -84.0 -89.4 -95.0 -100.7 -107.3 -107.7 -114.0
Width (ppm) 7.0 7.0 7.0 7.0 7.0 7.0 1.5 7.0
Area (%) 1.8 9.1 23.1 28.6 18.7 12.0 1.5 5.2
G-Kol-Ref-28 d (ppm) -76.0 -83.3 -89.2 -94.6 -100.4 -107.4 -107.5 -114.6
Width (ppm) 7.0 7.0 7.0 7.0 7.0 7.0 1.3 7.0
Area (%) 2.3 10.5 23.3 27.4 18.7 12.2 1.9 3.8
G-Kol-S-28 d (ppm) -75.5 -83.3 -89.1 -94.5 -100.2 -107.2 -107.4 -115.1
Width (ppm) 6.8 6.8 6.8 6.8 6.8 6.8 1.0 6.8
Area (%) 3.2 12.2 24.8 27.7 18.2 10.6 1.4 2.0
G-Kol-Ref-365 d (ppm) -74.3 -82.4 -88.4 -93.7 -99.6 -106.9 -107.7 -114.5
Width (ppm) 6.9 6.9 6.9 6.9 6.9 6.9 1.4 6.9
Area (%) 2.4 12.3 23.7 28.2 19.7 10.1 1.6 2.0
G-Kol-S-365 d (ppm) -75.1 -82.9 -88.9 -94.3 -99.9 -107.2 -107.7 -115.5
Width (ppm) 6.8 6.8 6.8 6.8 6.8 6.8 1.6 6.8
Area (%) 3.0 11.8 25.9 27.7 18.1 10.1 1.4 2.0
* Less condensed silicon species, Q1 and Q2 [21, 22, 39, 40]
** Quartz (-107.5 ppm) and other Q4 silicon units [21, 39, 41, 42]
Materials and Structures
the sulfate solution (about 12, Table 4). High pH
values of the sulfate solution caused breaking of –Si–
O–Si– bonds and formation of structural defects,
which led to the observed strength decrease of the
geopolymer samples (Fig. 1). The obtained results
emphasize the importance of controlling pH value and
composition of the sulfate solution when testing
sulfate attack on geopolymers.
4 Conclusions
In this paper, the impact of the Na2SO4 solution (50 g/l)
on mechanical properties and structure of geopolymer
samples based on two different FA samples was
investigated over a period of 365 days.
It was found that the treatment with the sulfate
solution had caused a small decrease in strength of the
geopolymer samples (about 10 %). Decline in strength
of the less porous geopolymer samples was observed
only after 365 days of investigation. The strength of
the more porous geopolymer samples decreased after
the first 28 days of testing. The subsequent exposure to
the sulfate solution caused an increase in strength of
the more porous geopolymer samples, probably due to
continuing of the alkali activation reaction in the
sulfate solution.
Analysis of the sulfate solution showed that, in
addition to diffusion of sulfate ions in the geopolymer
structure and leaching of Na from the structure,
treatment of the geopolymer samples with the Na2SO4
solution caused leaching of Si. During the entire
testing period, the pH value of the sulfate solution was
about 12.
No new phases were detected due to a reaction of
the geopolymeric material with sulfate ions. Occur-
rence of Na2SO4 crystals on the fracture surface of the
geopolymer samples was attributed to migration of
sulfate ions in geopolymer structure.29Si MAS NMR analysis of the geopolymer sam-
ples showed that, in the applied testing conditions,
treatment of the geopolymer samples with Na2SO4
solution had caused breaking of –Si–O–Si– bonds and
decrease in Si/Al atomic ratio in the samples. Decon-
volution of the 29Si MAS NMR spectra indicated that
breaking of –Si–O–Si– bonds occurred preferentially
in silicon rich components of the structure, showed by
a decrease of Q4(mAl), m = 0, 1 components of the29Si MAS NMR spectra. It was concluded that the
leaching of Si was a consequence of the increase in the
pH value of sulfate solution during the sulfate attack
investigation.
Acknowledgments This work was carried out within the
Project TR34026 funded by the Ministry of Education, Science
and Technological Development, Republic of Serbia. Authors
are grateful to Dr. Aleksandra Rosic (Faculty of Mining and
Geology, Belgrade University) for XRD analyses, Ljiljana
Milicic (Institute for testing materials Serbia) for XRF analyses,
MSc Ivona Jankovic-Castvan (Faculty of Technology and
Metallurgy, Belgrade University) for porosity measurements
and Prof. Miroslav Nikolic (Plant and Soil Laboratory, Institute
for Multidisciplinary Research) for ICP-OES analysis.
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