1
5th International Seminar on Modern Polymeric Materials for Environmental
Applications, Krakow
Effects of chemical treatments on physical properties of flax fibres
J. Zhu1, J. Njuguna
1*, J. Pacacz
2, H. Abhyankar
1, K. Pielichowski
2, H. Zhu,
K. Immonen3 and A Nurmi
3.
1Centre of Automotive Technology, Canfield University, Canfield, UK
2 Cracow University of Technology, Cracow, Poland
3VTT Technical Research Centre of Finland, P.O. Box 1000,
FI-02044 VTT, Finland
Keywords: flax, chemical treatment, thermal degradation
Abstract
The hydrophobicity of flax fibres often leads to the poor fibre/hydrophobic matrix
adhesion. The flax fibres are amenable to modification so as to solve the problem.
Alkali, acetylation, silane treatment and enzymatic treatment were employed for
the flax fibre mats in author’s study. To understand how these treatments affect the
physical properties, infrared spectroscopy (FTIR) and thermal gravimetric analysis
(TGA) were conducted on flax fibres. It was found that all the treatments result in
the removal of pectin component within the primary cell wall due to the
disappearance of the characteristic peak at 1735 cm-1
. Comparing with the
untreated fibres, the onset degradation temperature of treated ones decreased,
however, the peak of the maximum decomposition rate shifted to high
temperatures, indicating a better thermal stability.
1 Introduction
Flax/tannin composites could potentially offer environmental benefits and desirable
characteristics aiming at reducing the environmental footprint of superlight electric
vehicles applications such as vehicle body panels, crash elements, side panels and
body trims [1]. The hydrophilic property of flax leads to the poor interfacial
adhesion with the nonpolar hydrophobic tannin matrix and difficulties in mixing. In
order to solve the above problems, adequate surface modifications, mainly
chemical treatments, have being investigated for many years. The hydroxyl groups
in flax fibres could be modified for hydrogen bonding with cellulose groups or to
introduce new moieties that form effective interlocks within the system.
* corresponding author. [email protected], Tel. +44 1234 754186,
Fax: +44 1234 752473 (J. Njuguna).
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Mercerization, acetylation, silane treatment, and other fibre pretreatments are
commonly used for flax composites as reported in the literature [2]. Alkali
treatment, also called mercerization, could possibly change chemical composition
of flax fibres due to the fact that cementing substances like lignin and
hemicellulose are removed during the mercerization process [3]. Alkali treatment
also produces fine cellulose fibres by transferring crystalline form cellulose I into
cellulose II [4]. Acetylation is a well-known esterification method originally
applied to wood cellulose to stabilize the cell walls against moisture, improving
dimensional stability and environmental degradation. The acetic anhydride reacts
with more reactive hydroxyl groups (OH) in lignin and hemicellulose, whereas the
hydroxyl groups of cellulose prevent the diffusion of reagent and result in low
extent of reaction [5]. Proper treatment of fibres with silane can increase the
interfacial adhesion to the target polymer matrices. Silane is hydrolyzed forming
reactive silanols and is then adsorbed and condensed on the fibre surface (sol-gel
process). The hydrogen bonds may be further converted into covalent bonds by
heating the treated fibres at a high temperature (see in Figure 1).
Figure 1. Grafting of silanols on flax fibre surface (redraw from Singha er al.[6]).
The fibre pretreatments are able to change not only the fibre/matrix interface but
also the thermal stability of flax fibres, greatly influencing the composite
manufacturing temperature and the associated thermal properties. Bledzki et al.[7]
reported that the degradation temperature of flax fibres increased from 319°C to
360°C after acetylation (34% acetylation). The existent of strong hydrogen bonding
between PLA matrix and flax fibres also leaded to the increase in the
decomposition temperature of composites [8]. In this paper, alkali, acetylation,
silane treatment and enzymatic treatment were to modify non-woven flax mats for
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preparing composite laminates. The chemical change of flax fibres from
pretreatments were indicated from Fourier transformation infrared spectroscopy
(FTIR) spectrums. The effects of fibre pretreatments on thermal properties of flax
fibres were investigated through thermal gravimetric analysis (TGA).
2 Material and methods
2.1 Materials
Non-woven flax fibre mats with different surface treatments.
Table 1. Investigated flax composites and flax mats.
Sample
type
Treatment
method
Detail
T None Yes
1 5% NaOH Mercerisation
2 NaOH+BTCA Acetylation
3 NaOH+APS Silane treatment
* BTCA- Butanetetracarboxylic acid, APS- Amiopropyltriethoxysilane, Laccase-Benzenediol, Doga-dodecyl gallate.
2.2 Characterisation
FTIR. FTIR spectroscopy was carried out with a shimadzu FTIR 8400S to
characterize all the sample to identify the chemical change of flax fibres. The scan
number is 64 per minute with the band range from 600 to 4000 cm-1
.
TGA. The thermal analysis of untreated and treated flax fibres, and tannin resins
were carried out by a TGA STA 449 instrument supplied by NEZSCH at Cracow
University of Poland. Around 20mmg of each specimen was heat from room
temperature to 600°C at the heating rate of 10°C/min. Air condition was applied
throughout the experiments.
3 Results and discussion
3.1 Effects of surface treatments on fibre chemical composition
To confirm and exam the efficiency of the selected treatment, the investigation of
the unmodified fibres is of importance for further comparison. Garside and Wyeth
[9] has introduced the use of Fourie transform infrared (FTIR) with attenuated total
reflectance (ATR) spectroscopy technique to identify and distinguish cellulosic
fibres (e.g. flax, hemp, jute etc.) as an alternative simply and highly reproducible
way to micro-spectroscopy. In terms of chemical compositions published in the
literature, the flax fibre mainly comprises polysaccharides including cellulose
(64.1%), hemicellulose (16.7%), pectin (1.8%) and lignin (2.0%), with minor
4
components such as bound water, waxes, and other inorganic materials. The fibrills
of cellulose in the crystalline form are deposited within the hemicellulose and
lignin acting as an amorphous phenolic polymer matrix. Based on the reference
data, the important characteristic band assignments for the investigated flax
fibres are summarised in
Table 1.
Table 1. Infrared band assignments for flax fibres.
Position/cm-
1
Assignment Belonged chemicals
3335 v (OH) free -
2850 v (CH2) symmetrical Organic compounds
1735 v (C=O) ester Pectin
1635 Adsorbed water All the chemicals
1595 v (C=C) aromatic Lignin
1505 v (C=C) aromatic Lignin
1155 v (C-C) ring breathing Largely from cellulose
1105 v (C-O-C) glycosidic Cellulose
Figure 2. FTIR spectrum of unmodified and treated flax fibres.
There is no big difference for the major chemical constituents between unmodified
and 5% NaOH mercerised flax fibres due to the similarity of the two spectrums as
shown in Figure 2. However, the peak around 1735 cm-1
standing for the existence
of pectin as mentioned before has disappeared in the FTIR spectra of flax fibres
modified with 5% NaOH. Apparently, the absence of this peak is attributed to the
removal of the pectin component within the primary cell wall. The peak at 1505
cm-1
was too weak to be observed by eye, indicating that the lignin was almost
0
700120017002200270032003700
Unmodified5% NaOH
Ab
sorb
ance
Wavenumber (cm-1)
5
removed after alkali treatment. As a result, the presence of absorbed water mainly
contributes to the peak shifting to 1582 cm-1
, a lower frequency compared to 1632
cm-1
for the IR spectra of unmodified flax fibres.
The most significant change in the FTIR spectra before and after NaOH-BTCA
treatment was observed in the range of 1500-1700cm-1
.The appearance of the peak
around 1730 cm-1
does not arise from the C=O bonds of pectin removed together
with other ingredients in the primary cell during the NaOH treatment but actually is
contributed from the ester bonds introduced by BTCA reacting with OH groups.
The peak (1635 cm-1
) representing the absorbed water in cellulosic crystalline
shifted towards the low-frequency side (1563 cm-1
) along with a new partially-
overlapped peak at 1540 cm-1
. The shift of the peak position is probably correlated
with the carboxylate carbonyl via NaOH treatment.
Efficiency of silane treatment, such as aminopropyl triethoxy siloxane (APS), is
reported higher higher for the alkaline treated fibre than for the untreated fibre
because more reactive site can be generated for silane reaction [6]. The combined
NaOH treatment in NaOH-APS type removed the waxy epidermal tissues, lignins,
adhesive pectins and hemicellulose. It can account for the disappearance of peaks
at 1735 cm-1
and 1505 cm-1
assigned to C=O in pectin and aromatic C=C in lignin,
respectively. In addition, the well-defined absorption band at around 690 cm-1
is
obtained due to the symmetric stretching of –Si-O-Si- structure on the APS treated
fibres derived. The increment of the peak intensity at 1000 cm-1
and 982 cm-1
is
possibly attributed to the presence of Si-O-C bonds derived from the silane
chemical treatment. .
3.2 Effects of surface treatments on fibre thermal degradation
TGA analysis was undertaken for untreated NaOH, NaOH-BTCA and NaOH-APS
treated flax fibres so as to investigate the effects of different treatments on thermal
degradation. For comparison purpose, the weight loss and decomposition rate as a
function of temperature are shown in Figure 3 (TG) and Figure 4 (DTG,
respectively. The quantitative information of TGA analysis results are summarised
in TG curves can to some extent reflect the difference and similarity of thermal
properties influenced by surface treatments. Origin, NaOH and NaOH-BTCA,
NaOH-APS flax fibres have the similar water content around 5.5% to 6%,
indicating no significant hydrophobic enhancement of flax fibres after
modifications due to the polar OH groups of cellulose and other polar introduced
ingredients. The onset of thermal degradation of these flax fibres was almost the
same, however the weight loss period after 350°C differed quite a lot. Obviously,
NaOH-BTCA exhibited the best thermal stability due to the slight weight loss
between 300-500°C. The residue content of 35% may be due to the improved
thermal stability or too much inorganic material in the selected fibres. The non-
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cellulose decomposition period of the NaOH only treated flax fibres was shifted to
a higher temperature of 500°C than unmodified and NaOH-APS types (410°C).
Table 2.
This decomposition profile of untreated flax fibres shows strong agreement of the
typical TGA-air of flax fibres found in the publications [10]. According to this TG
curves, it is obviously that some weight loss of around 5.47% occurred up to 200°C
due to the evaporation of absorbed water of flax fibres upon heating. Then the
biggest weight loss of 65.94% occurred in the approximate temperature range of
250°C to 380°C, followed by the second weight loss of 24.99%, which terminates
at 420°C. After that, a weight loss of 3.28% took place till 600°C and left the
residual content of 0.32wt%. The main decomposition temperature was obtained at
305°C, which is similar to the temperature of 319°C observed in literature [11].
The degradation kinetics of flax fibres is complicated due to their inhomogeneous
constituents, and can be better visualised by DTG curves. The first DTG peak is
broad and below 100°C as a result of water removal. The second DTG peak is
caused by cellulose degradation while the third DTG peak of around the 417°C is
largely attributed to the degradation of non-cellulose components. One thing worth
noting is that the cellulose degradation still continued after the first peak until
500°C since cellulose suffered different degradation reactions depending on
temperatures. Generally, in the temperature from 300°C to 500°C, cellulose is
firstly converted into active form to yield phenol, followed by the ring scission at
approximately 340°C to form anhydrosugars like levoglucosan with further
hydration, and the formation of polycyclic aromatic compounds (350°C), mainly
constituting the ash content in the 400°-500°C temperature range [12]. After the
third DTG peak, most of the decomposition products integrated into ash, and
further oxidised with temperature and left around 0.3% inorganic residue after
600°C.
Figure 3. TGA curves of investigated flax fibres.
0
50
100
0 100 200 300 400 500 600
UntreatedNaOH
7
Figure 4. DTG curves of investigated flax fibres.
TG curves can to some extent reflect the difference and similarity of thermal
properties influenced by surface treatments. Origin, NaOH and NaOH-BTCA,
NaOH-APS flax fibres have the similar water content around 5.5% to 6%,
indicating no significant hydrophobic enhancement of flax fibres after
modifications due to the polar OH groups of cellulose and other polar introduced
ingredients. The onset of thermal degradation of these flax fibres was almost the
same, however the weight loss period after 350°C differed quite a lot. Obviously,
NaOH-BTCA exhibited the best thermal stability due to the slight weight loss
between 300-500°C. The residue content of 35% may be due to the improved
thermal stability or too much inorganic material in the selected fibres. The non-
cellulose decomposition period of the NaOH only treated flax fibres was shifted to
a higher temperature of 500°C than unmodified and NaOH-APS types (410°C).
Table 2. Summary of TGA results for treated and untreated flax fibres.
Flax
type
Moisture
(wt%)
Main decomposition
temperature (°C)
DTG peaks (°C)
1st 2nd 3rd
Untreated 5.47 305.5 50.2 336.5 417.4
NaOH 5.88 250.3 59.6 293.0 528.1
NaOH-BTCA 5.83 258.5 78.2 301.5 451.3
NaOH-APS 6.49 261.8 48.3 299.9 421.4
Compared with TG curves, the effects on thermal stability were more clearly
obtained from DTG curves. The first DTG peak is associated with water
evaporation on heating. The higher peak temperature of NaOH-BTCA sample
around 80°C possibly indicates that BTCA treatment can lead to stronger hydrogen
bonding to water. The second peak related to cellulose degradation decreased from
336°C to the temperature range of 290-300°C for all the treated samples. This may
0
10
20
30
0 100 200 300 400 500 600
Untreated
NaOH
NaOH-BTCA
NaOH-APS
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correlate to the increase of amorphous cellulose which the degradation begined
with. Another noticeable change is the decrease of the maximum decomposition
rate at 1st peak. This is attributed to that pectin, and part of lignin and
hemicellulose on the flax fibre surface was removed, leading to an improvement of
thermal stability. Many researchers [12-14] have reported the positive influence of
alkali treatment on thermal degradation of natural fibres. NaOH-BTCA flax sample
shows a much smaller 2nd peak, indicating that BTCA significantly improves the
thermal stability of non-cellulose components attributable to 2nd peak. In addition,
the maximum decomposition temperature of the 2nd peak of pure NaOH treated
flax fibres was around 100°C bigger than that of untreated sample. The pure
mercerisation shows better effect than NaOH-BTCA and NaOH-APS to enhance
the thermal stability of non-cellulose constituents in flax fibres.
4 Conclusions
The effect of fibre treatments on chemical change and the associated thermal
properties of flax fibres were investigated through adequate characterizations and
analysis. It was proved that the pectin and lignin was removed during the NaOH
treatment due to the disappearance of their characteristic IR band at 1735 cm-1
and
1505 cm-1
, respectively. For other treated samples, the FTIR results also indicate
the presence of cross-linked BTCA (ester bond) and the introduced APS (Si-O-Si).
Due to the chemical composition change, the thermal properties of flax fibres
differed after treatments. All the treated samples displayed a much lower
decomposition rate at the initial degradation step. Additionally, NaOH-BTCA has
been found to offer the best improvement of thermal stability of the non-cellulose
part of flax fibres.
Acknowledgement
The authors are thankful the ECHOSELL (project no. 265838) and Cracow
University of Technology (project No. UMO-2011/01/M/ST8/06834) for the
financial and technical support for this research.
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