incinerator bottom ash and ladle slag for geopolymers preparation
TRANSCRIPT
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Waste and Biomass Valorization ISSN 1877-2641 Waste Biomass ValorDOI 10.1007/s12649-014-9299-2
Incinerator Bottom Ash and Ladle Slag forGeopolymers Preparation
Isabella Lancellotti, Chiara Ponzoni,Maria Chiara Bignozzi, Luisa Barbieri &Cristina Leonelli
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ORIGINAL PAPER
Incinerator Bottom Ash and Ladle Slag for GeopolymersPreparation
Isabella Lancellotti • Chiara Ponzoni •
Maria Chiara Bignozzi • Luisa Barbieri •
Cristina Leonelli
Received: 25 July 2013 / Accepted: 18 February 2014
� Springer Science+Business Media Dordrecht 2014
Abstract Ladle slag (LS) and urban incineration bottom
ash (BA) are two types of non hazardous inorganic wastes
which do not contain significant amounts of pollutants such
as heavy metals and organics. Nowadays they are neces-
sarily disposed of with little attention placed for re-use or
recycling. Considering their chemical composition, rich in
silica and alumina with substantial levels of lime and iron
oxides, these residues can be suitable for generating new
alkali activated materials. A safe reuse of these residues in
high percentages (60–70 wt%) is presented in this study for
mortar production. The final room-temperature consoli-
dated materials, also known as geopolymers, have been
characterized in terms of thermogravimetric analysis,
morphology, porosity, and crystalline phases evolution.
When incinerator BA is used, the morphology of the
resulting geopolymer is very close to that of pure
metakaolinic pastes, whereas for LS based geopolymers
calcium presence promotes the formation of calcium–alu-
minate–silicate–hydrate phase. This investigation also
demonstrated that the content of reactive fraction of BA is
of primary importance to assess its possible use in alkaline
activation process.
Keywords Alkali activation � Geopolymers � Ladle slag �Incinerator bottom ash
Introduction
With the aim of transforming inorganic industrial waste to
valuable materials, two categories of aluminosilicates have
been here activated via alkali solutions and consolidated at
room temperature as cement-like materials. The first type
of waste is a residue of steel industry. Steel slag comes
from the ladle slag (LS) where the refining process of steel
produced by scrap melting in arc electric furnace or by the
conversion of iron to steel in a basic oxygen furnace (BOF)
occurs [1, 2]. In the steel making process, slags are used to
prevent oxidation of the steel through contact with air, to
limit heat losses through radiation and to remove impurities
from the molten steel [3]. Hence slag is an unavoidable by-
product of steelmaking process and its numerous functions
are very well known.
Ladle slag accounts for about 1/3 of the total amount of
slag usually produced in electric arc furnaces and its
European production can be estimated about 4 millions
t/year [4]. The amount of LS and, more in general, of steel
slag is going to increase in the near future as arc-electric
furnaces represent a more efficient and sustainable process
for steel production compared to blast furnaces [5]. Now-
adays LS is generally treated as non hazardous waste and
dumped in landfills and very few attempts are present to
evidence their commercial value when properly prepared
and processed [6]. Beside aluminosilicate, LS contains
calcium–silicate, magnesium–silicate and calcium–alumi-
nate compounds and minor amounts of other metallic
oxides, mainly iron. For its chemical composition LS was
investigated as cement constituent in mortar and concrete
preparation [2, 7] and geopolymer matrix for fiber rein-
forced composites materials [8].
The second type of waste material, very close to LS in
terms of chemical composition and percentage of
I. Lancellotti (&) � C. Ponzoni � L. Barbieri � C. Leonelli
Department of Engineering ‘‘Enzo Ferrari’’, University
of Modena and Reggio Emilia, 41125 Modena, Italy
e-mail: [email protected]
M. C. Bignozzi
Department of Civil, Chemical, Environmental, and Materials
Engineering, University of Bologna, 40131 Bologna, Italy
123
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DOI 10.1007/s12649-014-9299-2
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amorphous phase and soluble salts, is bottom ash (BA)
deriving from urban waste incineration. At present the
incineration process represents an efficient alternative to
dumping and it is safely conducted till full oxidation of all
the combustible materials. Thermal treatment aims at a
volume reduction of waste; at the destruction, capture, and
concentration of hazardous substances; and evidently at the
recovery of energy [9]. One of the most important disad-
vantages of the incineration technology is the production of
significant amounts of solid residues: fly ashes (5 % of
initial weight of wastes) and bottom ashes (up to 30 % of
initial weight of waste) [10]. The BA, used in this paper, is
classified as non hazardous waste, differently from fly ash,
and it represents a residue with interesting chemical com-
position capable of matching with cement and ceramic
formulations requirements [11]. The similarities in terms of
physical characteristics and chemical composition between
granular construction materials and incinerator BA make
this residue virtually suitable for recycling as natural
aggregates replacement. In some countries, such as Japan,
German, Denmark and the Netherlands, incinerator BA is
used extensively in roads, aggregates, asphalt concrete, soil
amendment, soundproofing for walls, etc. The recycling
rate is typically 70–90 % and can be even up to 100 %
[12]. Notwithstanding this scenario, increasing regulatory
focus on leaching properties of bottom ashes has increased
the demand for dedicated techniques for upgrading of ashes
prior to utilization. Within the last decade, many efforts are
made for minimizing leaching of salts and heavy metals
such as Cu, Cr, As, Ni, Cd, and Pb in full-scale applica-
tions, especially using washing processes. No single pro-
cess has been found to ensure compliance with limit values
on leaching; however, extended curing as well as washing
could in most cases decrease leaching significantly.
Remaining problems were primarily associated with Cu, Cr
and sulfate leaching. [13]. In Italy only recently specific
plants for incinerator BA treatment are developing. In
particular these treatments consists of ageing, grinding and
Fe and Al separation by means of magnetic and eddy
current systems. The separated metals are about 8 % of the
total BA and are sent to recycling.
Thus both LSs and urban waste incineration ash repre-
sent a challenging problem of waste management due to
the presence of soluble salts and high aluminium-contain-
ing phases making their use not particularly appreciated in
cement industry. On the other hand their calcium content is
too high for completely substituting metakaolin (MK) in
structural geopolymer matrix [14, 15]. Nevertheless, both
wastes possess an important amount of vitreous fraction
making them promptly attacked by alkali solution. LSs
have already been activated with sodium silicate but a
complete investigation on the NaOH activation has never
been carried out previously by other authors [10]. Further,
only few papers [16] are present in literature, except our
work [17], which report an investigation about the use of
high amount of bottom ashes in geopolymer formulations.
On the basis of previous researches, this work aim at
demonstrating the possibility to use alkali activation for the
transformation of inorganic industrial and urban waste to
valuable materials. We report recent results in the micro-
structural, mineralogical, thermogravimetric and spectro-
scopic characterization of the newly proposed
formulations. These results represent a step forward in the
understanding the consolidation process of MK based
geopolymers with high content of LS or BA proposed for
the industry of building materials.
Materials and Methods
Ladle slag, incineration BA and MK’s chemical charac-
terization (X-ray fluorescence, Philips PW 2004), soluble
fraction in water (solid/liquid = 1/4, for 2 h) and loss of
ignition (LOI) (at 1,100 �C for 2 h) were performed and
reported in Table 1 [14, 17, 18].
Incineration BA was ground for 30 min in a ball mill
and sieved below 75 lm to reach grain size similar to that
of MK powder. LS was supplied as fine sand. The fraction
greater than 1 mm was sieved in order to obtain a grain size
distribution close to MK powder.
Three oxide ratios (CaO/SiO2; SiO2/Al2O3; Na2O/
Al2O3) are reported in Table 1 as they are indicators of
Table 1 Chemical composition and other physical data of LS and
BA added to MK
(wt%) Ladle slag Bottom ash Metakaolin
CaO/SiO2 3.32 0.35 _
SiO2/Al2O3 1.48 5.30 1.29
Na2O/Al2O3 _ 0.61 _
SiO2 16.4 49.45 53.6
Al2O3 11.1 9.33 41.7
CaO 54.5 17.49
MgO 4.0 2.88
Na2O Traces 5.70
K2O 0.04–0.2 1.41 2.5
Fe2O3 2.0–3.0 4.81 1.0
MnO 0.05–0.5 0.16 _
TiO2 0.04–0.2 0.81 0.5
Soluble fractiona 1.5 1.3 _
LOIb 9.81 4.77 _
Grain size \1 mm \75 lm \75 lm
a Determined as solubility in water (solid/liquid = 1/4) for 2 h for
five repeated treatmentsb Loss of Ignition at 1,100 �C, for 2 h
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good quality for structural building materials. In particular,
for LS a high CaO/SiO2 is observed according to its large
content ([50 %) of calcium oxide. On the contrary, a
higher SiO2/Al2O3 ratio is present for BA compared with
MK ratio (1.29), thus indicating that an extra alumina-rich
source should be used as precursor to reach geopolymer
formulations with high performances.
As previously reported [14], geopolymers made by
100 % of LS do not exhibit good mechanical properties
while the addition of MK as minor component for both the
slag has been optimized in two separate studies [13, 16]. It
was previously demonstrated that the minimum quantity of
30 wt% was suitable for both wastes. For LS based geo-
polymers the addition of 40 wt% of MK was also taken
into consideration. Different amount of NaOH (8 M, Carlo
Erba, Italy) and sodium silicate (SiO2/Na2O = 3, Ingessil,
Verona, Italy) solutions were added to the different mixes
as reported in Table 2. The investigated waste was alter-
natively mixed with MK and finally to the alkali solutions
with solid/liquid [g/g] ratio of 1.7 and 2.5 for LS and BA
based samples, respectively. A lower content of alkali
solutions was used for BA based samples comparing to LS
based geopolymers as BA is very rich of sodium oxide.
However, water addition was required to reach a good
workability when BA was used as precursor.
After 10 min mixing, geopolymers were cast in pris-
matic moulds with dimension of 3 cm 9 2 cm. Three
specimens for each mix were prepared.
In order to evaluate the reactive fraction of BA and
better tailor the formulation, an alkaline attack with NaOH
8 M was performed according to the test reported in lit-
erature [19]: 1 g of BA was placed in 100 ml of 8 M NaOH
solution and stirred constantly for 5 h in a flask bathed at
80 ± 2 �C. The analysis of liquid fraction after the test
performed by ICP-AES (Philips Varian, Liberty 200, using
k = 251,611 nm for Si and 396,152 nm for Al) shows the
amounts of Si and Al dissolved in an environment similar
to that of alkaline activation conditions. The dissolved
cations were determined to be: Si = 1.53 and
Al = 0.5 wt% for a ratio of Si/Al = 3.06. On this basis
new geopolymers were prepared and reformulated, here-
after indicated as MK30_BA70R, as reported in Table 2.
The reformulation was performed considering as starting Si
and Al content the amount dissolved in the alkaline
solution, i.e. the effective reactive fraction. This reformu-
lation, therefore, required a different dosage of NaOH and
Na-silicate as reported in Table 2.
Mineralogical and microstructural characterizations
were performed on both LS and BA based geopolymers
after curing for 24 h in sealed mould plus 30 days
unsealed. Curing procedure was carried out at room tem-
perature and relative humidity (R.H.) equal to 60–70 %.
Morphology studies were conducted on freshly fractured
samples by ESEM (ESEM, Quanta200, FEI, NL) equipped
with EDS in order to evidence phase distribution and
degree of reactivity of LS and BA in the geopolymeric
amorphous matrix. The mineralogical analysis of the two
geopolymers was carried out by a powder diffractometer
(PW3830, Philips, NL) with Ni-filtered Cu Ka radiation in
the 5–70 2h range on powdered samples (30 lm particle
size). Pore size distribution measurements were carried out
by a mercury intrusion porosimeter (MIP, Carlo Erba 2000,
Italy) equipped with a macropore unit (Model 120, Fison
Instruments, UK) on samples previously dried at 80 �C.
Samples for porosimetry were cut by diamond saw to
approximately 1 cm3, dried under vacuum and kept under a
P2O5 atmosphere in a vacuum dry box until testing.
Thermogravimetric characterizations of the geopoly-
mers were performed by means of TG/DTA equipment
(Netzsch 429, Germany) on 30 mg of powdered samples
with an heating rate of 20 �C/min up to 1,400 �C.
FT-IR spectra for samples containing incinerator BA were
recorded (Avatar 330 FT-IR Thermo Nicolet, USA); 32
scans between 2,000 and 650 cm-1 were averaged for each
spectrum at intervals of 1 cm-1. The FT-IR spectra have
been collected on geopolymers without (MK30_BA70) and
with the reformulation (MK30_BA70R), taking into account
the dissolved fraction of BA, in order to assess the differ-
ences in structure.
Results
The as-received BA presents a chemical composition
(Table 1) with insufficient Al content with respect to sili-
con (ratio Si/Al = 5.3 in Table 1), therefore the ash has
been admixed with MK to ensure the proper Si/Al ratio for
Table 2 Formulation of geopolymers referred to 100 g of solid and final Si/Al and Na/Al mass ratio
MK (g) LS (g) BA (g) NaOH 8 M (ml) Na silicate (ml) H2O (ml) Si/Al Na/Al
MK40-LS60 40 60 – 30 30 – 1.51 0.71
MK30_LS70 30 70 – 30 30 – 1.58 0.82
MK30_BA70 30 – 70 14 20 3 3.26 1.09
MK30_BA70R 30 – 70 10 24 3 2.06 1.24
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geopolymerization of structural materials. Many authors
found Si/Al ranging between 1.5 and 2.5 as most suitable
value for two parameters: material leachability [20], as a
consequence of high degree of 3D-polymerization in the
structure; and mechanical properties [21]. Furthermore,
both a soluble fraction, related to chlorides and sulphates,
and loss of ignition, imputable to inorganic and organic
carbon are present. These phases have also been confirmed
by XRD analysis (see below). In a previous paper [17], the
leaching of Ba, Zn, Pb, Cu, Cr and Ni was analysed to
evaluate the hazardousness of the BA. All the values were
below the regulation limits for disposing on landfill for not
dangerous wastes. For this reason geopolymers containing
this BA are not further subjected to leaching test.
SEM images of as-received LS and BA (Fig. 1a, c)
present the starting raw materials used for the preparation
of the specimens. Particles size distribution is particularly
wide in both the samples promising a good packing ability
of the two powders. LS presents irregularly shaped grains
(Fig. 1a) as well as more spherical particles according to
the high temperature environment in which they were
generated.
Fig. 1 SEM images of
untreated LS and BA (a) and
(c) and geopolymers
MK30_LS70 with
corresponding Si/Al and Si/Ca
ratios by EDS analysis (b),
MK30_BA70 cured for 30 days
(d), and MK30_BA70R cured
for 15 days with corresponding
Si/Al ratio by EDS analysis (e)
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Freshly fractured surfaces of geopolymers containing
70 wt% of LS or BA are reported in Fig. 1b, d, e,
respectively. In LS based geopolymer, un-reacted slag
particles are tightly connected to the matrix, however two
gel morphologies are clearly distinguished. The EDS ana-
lysis has highlighted the presence of two Ca–Na–alumi-
nosilicate (C–N–A–S–H) gels with different chemical
compositions: one gel is richer in Si, Al and Na and poorer
in Ca, compared to the other gel. In particular, calculating
the Si/Al and Si/Ca weight ratio, it has been determined
that the Si/Al ratio is quite similar for both gels (1.5 and
1.6), whereas the Si/Ca ratio changes from 0.6 to 1.3. These
findings agree with EDS analysis previously reported [14]
for alkali activated mixes containing larger content of MK.
Indeed, the dissolution of LS particles promotes the ion
exchange between sodium and calcium, leading to gel
richer in calcium with the increase of LS in the
formulation.
Comparing the two morphologies of BA and corre-
sponding geopolymer reported in Fig. 1c, d, it can be seen
that after 30 days curing the geopolymeric matrix appears
denser for the formation of gel, but particles of 30–50 lm
are still evident. This observation demonstrates that
incinerator ash is reactive in alkaline environment and can
be transformed in geopolymers, but the optimization of the
formulation can help to obtain complete reactivity. Fig-
ure 1e shows the microstructure of geopolymer containing
BA after reformulation cured for only 15 days, ash parti-
cles are still evident but a larger amount of geopolymeric
gel is formed, confirming that a Si/Al ratio near to 2 leads
to more extended reactivity. Furthermore, from EDS ana-
lysis it can be observed that the values of the Si/Al ratios
analysed in two areas are near to the theoretical value of
2.06 (reported in Table 2), confirming the high reactivity of
BA. For sake of comparison, in the sample before refor-
mulation the theoretical value of Si/Al, considering the
overall chemical composition only, was 3.26, but from
EDS analysis only an average value of 1.5 was found,
confirming the lower reactivity of the ash in this condition.
Moreover, higher amount of calcium (about 3 wt%) is
dissolved in the gel versus 1.3 wt% recorded for the initial
formulated geopolymers; with respect to the value
observed for LS the content of Ca in the gel remains lower.
Ladle slag exhibits a complex structure (Fig. 2) where
an amorphous matrix coexists with crystalline phases, such
as olivine (c-C2S Ca2SiO4 ICDD #180-941), gehlenite
(Ca2(Al(AlSi)O7) ICDD #174-1607), mayenite, syn
(Ca12Al14O33 ICDD #170-2144) and iron–magnesium–
calcium–silicate as previously described [14]. Traces of:
(1) periclase (MgO, ICDD #45-0946), from the ladle
refractory lining; (2) oldhamite (CaS, ICDD #38-1420),
from the desulfuration process; and (3), b-C2S (Ca2SiO4),
Ca(OH)2, calcium and magnesium carbonates have also
been identified [18]. The large extent of crystalline phases
makes difficult the quantitative determination of the
amorphous phases, as reported in the literature [18–22].
Nevertheless, LS are alkali activated by NaOH solution
when mixed with MK in proper amounts. Indeed, MK
brings reactive silica and alumina in the mix thus allowing
the geopolymerization process, which is very difficult
when only LS is used as its oxides are mainly in crystalline
form.
Figure 2 reports also MK30_LS70 XRD pattern, char-
acterized by an amorphous structure (broad diffraction
hump from 25� to 37� 2h) with peaks corresponding to
calcite, mayenite, cristobalite and periclase. Although dif-
ferent types of slag, reacting with water, are able to form
hydrate products similar to C–S–H [23, 24], LS exhibits
Fig. 2 XRD patterns of as-
received LS and geopolymer
MK30_LS70 after 30 days of
curing (O olivine, P periclase,
M mayenite, C calcite, Q quartz,
cr cristobalite, G gehlenite)
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binding property mainly in the presence of an alkaline
activator and LS reactivity increases with the decrease of
the particle size [25]. The chemical nature of thephases
formed in LS/MK geopolymers has been reported else-
where [14], but we can mention that it was demonstrated
from XRD patterns and EDS analysis that C–A–S–H and
3D aluminosilicate (N–A–S–H) network can coexists in
different extent. Ion exchange between sodium and calcium
also modifies the structure typical of metakaolinitic geo-
polymers. Recent studies carried out on synthetic sodium
aluminosilicate hydrate gel [26] show the existence of a
C–A–S–H gel more stable than N–A–S–H at high pH.
Figure 3a reports the XRD pattern of the MK, the as-
received BA and its corresponding geopolymer. The wide
amorphous hump of BA sample (more significant with
respect to LS) indicates its nature being both amorphous
and crystalline.
The crystalline phases present in the starting BA, aquartz (a-SiO2, JCPDF file 33-1161), calcite (CaCO3,
ICCD #5-586), anhydrite (CaSO4, ICCD #37-1496), gehl-
enite (Ca2Al(Al,Si)O7, ICCD #35-755) and plagioclase
((Na,Ca)(Si,Al)4O8), are still present in the consolidated
product (except for calcium sulfate, due to its solubility)
together with muscovite, present in MK.
Guo et al. [27] found as newly phase formed in geo-
polymers containing waste materials containing calcium,
gismondine (CaAl2Si2O8. 4H2O, ICCD #20-452), corre-
sponding to calcium aluminum silicate hydrate. In the
sample investigated in this paper the presence of gismon-
dine is difficult to identify with certainty because all its
peaks overlap with the peaks of quartz. The formation of
gismondine could be due to the main reactivity of calcium
present in the amorphous fraction in the ash rather than
calcium in crystalline phases. The higher reactivity of
amorphous phase is evidenced in Fig. 3b where is reported
the comparison of XRD patterns of ash and ash treated in
NaOH. It appears evident the significant decrease of the
amorphous hump after the treatment with NaOH 8 M
confirming its higher reactivity in the geopolymers
environment.
Pore size distributions, reported in Fig. 4, were strongly
influenced by the waste based precursors used for geopo-
lymerization. Indeed, LS and BA geopolymers exhibit a
very different behavior: the former shows the lowest total
intruded volume with the most part of pore sizes in the
range of 0.010–0.10 lm, whereas the latter has large pores
and elevate intruded volume, thus indicating a large open
porosiy.
Pore size distributions were strongly influenced by feed
composition. For LS based geopolymers, by increasing the
content of LS, porosity curves move towards pores with
large dimensions. As LS promotes the formation of cal-
cium rich gel, it can be hypothesized that such a gel is
responsible for porosity increase. Indeed, both LS60-MK40
as well as LS70-MK30 exhibits two types of gel, as
reported [14].
Fig. 3 XRD patterns of a MK, BA and geopolymer MK30_BA70
after 30 days of curing and b of BA before and after treatment in
NaOH 8 M
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BA based geopolymers exhibit a different behavior as
function of the different amounts of sodium hydroxide and
sodium silicate solutions used in the mix. The absence of
C–A–S–H phase generates a more porous structure, which,
in its turn, is strictly influenced by the amount of Al and Na
available for geopolymerization process. In fact BA70-
MK30 presents a porosity mainly concentrated in the range
of 0.010–0.21 lm, whereas the reformulation of the alka-
line solutions in BA70-MK30R lead to a geopolymer with
a bimodal pores distributions in the range of 0.010–0.10
and 10–35 lm.
Figure 5 shows the differential thermogravimetric
(DTA/TG) curves of BA based samples. Both geopolymers
show mass loss as a function of temperature increase. An
average mass reduction of 12 %, occurred over the tem-
perature range of 100–1,400 �C, was recorded for geo-
polymers as observed by other authors [28, 29]. This loss is
significantly lower than that of pure MK geopolymer (30 %
mass reduction). The main weight loss is registered at
temperatures below 250 �C and it is imputable to water, the
exposure, in fact, to high temperatures leads to changes in
chemical structure and the dehydration of free and chem-
ically-bound water. As the external temperature increases,
moisture within the specimen rapidly migrates towards the
surface of the specimen and escape. The mass loss at about
250–600 �C is attributed to the removal of more tightly
bound water and probably also reflects the decomposition
of hydroxides formed in alkaline environment from the
soluble salts of metals. At 700 �C, weight decrease,
imputable to decomposition of calcium carbonate, is evi-
dent and is related to the presence of CaCO3 both in
incinerator ash as well as in geopolymers as confirmed by
XRD pattern showed in Fig. 3.
Samples MK30_BA70 and MK30_BA70R, before and
after reformulation, do not evidence significant differences
in the thermal properties. Small peaks in the range between
650 and 800 �C for the sample before reformulation shows
the higher presence of carbonates both residual from BA
and formed by the reaction with atmospheric carbon
dioxide. These results are confirmed by FT-IR spectros-
copy (see below).
The differential thermogravimetric (DTA/TG) curves
for LS70-MK30 and LS60-MK40 (Fig. 6) show higher
weight loss than BA based geopolymers. As XRD and
porosity data suggest, the total weight loss is influenced by
the LS content in the feed: indeed increasing the LS
amount, the weight % loss moves from 15 % for LS60-
MK40 to 20 % for LS70-MK30. As previously described,
the main contribution to the weight loss (up to 650 �C) is
due to dehydration of free and chemically bonded water.
For these materials the dehydration of C–A–S–H phase
must also be taken into account together with the decom-
position of Ca(OH)2 occurring in the range of 350–450 �C
(this peak is particularly evident for LS70-MK30 geo-
polymer which is rich in Ca thanks to the high content of
LS). The weight loss detected between 700 and 750 �C is
due to calcium carbonate, present in traces in the starting
LS.
The comparison between geopolymers MK30_BA70
without and with reformulation is reported in FT-IR spectra
(Fig. 7). For both the samples a common feature is
observed:
• strong Si–O–T (T = Si, Al) asymmetrical stretching
peak at about 1,000 cm-1; by comparing this signal to
which of the mixture of raw materials (MK and BA)
before alkali activation (1,035 cm-1), reported in a
previous paper [17] appears evident the shift towards
lower values, implying a chemical change in the matrix,
indicating the degree of geopolymerization associated
to the inclusion of tetrahedrally-coordinated Al in the
Si–O–Si skeletal structure as observed also by other
Fig. 4 Pore size distributions of the investigated geopolymers
Fig. 5 DTA/TG curves of geopolymers MK30_BA70 before and
after reformulation
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authors [16, 30]. No signals near 900 cm-1, related to
Al(VI)–OH stretching vibrations, are visible, as
observed for examples by the authors in MK geopoly-
mers [31], notwithstanding traces of residual muscovite
are identified by XRD results in MK30_BA70. The
presence of Al(VI) signal could be related to low
geopolymerization degree in the samples.
• band at 1,460 cm-1, typical of carbonate species,
probably sodium carbonate, derived from the reaction
of free Na? ions with atmospheric carbon dioxide. In
sample with reformulation this band is less intense
probably due to the lower amount of Na2CO3 formed
by unreacted NaOH as consequence of the best
tailoring of mixture. This band was also observed by
the authors in MK geopolymers moulded and cured in
similar conditions (room temperature and polymeric
mould) [31].
• low intensity band at 875 cm-1, already attributed to
CaCO3 by other authors [32], therefore this signal can
be related to the presence of carbonates in geopolymer
as a consequence of their presence in BA.
Conclusions
The valorisation of LS and BA derived from the inciner-
ation of bottom ashes has been investigated via alkali
activation using a concentrated NaOH and sodium silicate/
water glass solutions.
The consolidated materials, aslo known as geopolymers,
contain high percentages (60 and 70 wt%) of LS and BA
derived from the incineration of urban wastes. Their mor-
phology is very close to that of pure metakaolinic pastes,
i.e. structural 3D geopolymers, although calcium presence
in the precursors tend to promote the formation of calcium–
aluminate–silicate–hydrate phase. There is a complex
evolution of the amorphous as well as the crystalline por-
tion of the wastes.
According to the literature [22], the presence of calcium
coming from LS and BA can promote an ion exchange
process with sodium, replacing it in the N–A–S–H gel and
consequently forming C–A–S–H. The structure of the C–
A–S–H gels has not been investigated in this paper, how-
ever it has been reported that the 3D structure typical of N–
A–S–H is usually preserved at these pH values [13].
This investigation has also demonstrated that the
determination of reactive fraction of BA is of primary
importance when assessing the possible use of this raw
material in the alkaline activation process. In particular, the
reactive Si/Al ratio is an important parameter to take into
account for a proper geopolymers formulation [18]. For
BA, significant differences have been observed in the Si/Al
ratios and microstructure with or without reformulation by
considering reactive Si/Al due to the presence of both
amorphous and crystalline fractions with a different degree
of reactivity.
Acknowledgments Authors are grateful to dr. Mirko Braga and dr.
Pasquale Pansini, from R.S.A. Laboratory, INGESSIL S.r.l., Monto-
rio (Verona, Italy) for supplying sodium silicate solutions.
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