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Renewable Epoxy Thermosets from Fully Lignin-Derived Triphenols Shou Zhao, Xiangning Huang, Andrew Whelton, and Mahdi M. Abu-Omar ACS Sustainable Chem. Eng., Just Accepted Manuscript • DOI: 10.1021/ acssuschemeng.8b00443 • Publication Date (Web): 30 Apr 2018 Downloaded from http://pubs.acs.org on May 1, 2018
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ACS Sustainable Chemistry & Engineering
Renewable Epoxy Thermosets from Fully Lignin−Derived Triphenols
1
†
‡
Shou Zhao, Xiangning Huang, Andrew J. Whelton,
2 3
†
4
232, Santa Barbara, California 93106, United States
5
‡
6
Lafayette, Indiana 47907, United States
7
§
8
Indiana 47907, United States
9
ll
‡, §
and Mahdi M. Abu−Omar
†, ll,*
Department of Chemistry & Biochemistry, University of California, Santa Barbara, Building
Lyles School of Civil Engineering, 550 Stadium Mall Drive, Purdue University, West
Division of Environmental and Ecological Engineering, Purdue University, West Lafayette,
Department of Chemical Engineering, University of California, Santa Barbara, Engineering
10
II Building, Santa Barbara, California 93106, United States
11
*
12
ABSTRACT: A series of fully renewable triphenols (TPs) with various number of methoxy
13
group substituents (n = 0−6) were synthesized using lignin−derived phenols (guaiacol and
14
2,6−dimethoxyphenol)
15
syringaldehyde). The structural evolution from TPs to epoxy thermosets was followed by
16
nuclear magnetic resonance (NMR) and Fourier transform infrared (FTIR) spectroscopy.
17
Thermomechanical properties of the resulting epoxy thermosets were investigated by
18
dynamic mechanical analysis (DMA), tensile analysis (TA) and thermogravimetric analysis
19
(TGA). Increasing the content of methoxy groups decreased the glass transition
20
temperature (132 to 118 °C) and glassy modulus (2.6 to 2.2 GPa). Thermal stability of
21
high−methoxy−content thermosets was reduced due to electron−donating effects and
22
higher oxygen content. Conversions and isolated yields of TPs significantly decreased as
Corresponding author:
[email protected] and
aldehydes
(4−hydroxybenzaldehyde,
1
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vanillin
and
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23
the number of methoxy substituents increased, which markedly determined the feasibility of
24
TPs as precursors for polymers. This work widens the synthesis route of fully lignin−derived
25
polyphenols, yielding polymers with thermomechanical properties comparable to bisphenol
26
A (BPA) based materials. Evaluation of methoxy substitution provides insight for the
27
selection of lignin−derived monomers.
28
Keywords: Lignin, Epoxy thermoset, Methoxy, Renewable polymer, Thermomechanical
29
properties
30
INTRODUCTION
31
Epoxy thermosets have been extensively used as coatings, adhesives, electronic
32
materials and structural composites because of their excellent thermal and mechanical
33
properties. The most popular epoxy monomers are derived from bisphenol A (BPA), which
34
accounts for more than 90 % of epoxy cross−linked polymers. The suitability of BPA comes
35
from its aromatic structure, which confers good mechanical and thermal properties on the
36
resulting epoxy thermosets. However, as the development of renewable materials has
37
received increased attention, numerous biomass derived molecules have been investigated
38
to replace or supplement the petroleum−based BPA.2−23 Among these feedstocks, lignin is
39
the most promising candidate for making epoxy thermosets, since it is the sole
40
large−volume sustainable source composed of an aromatic skeleton.24, 25
41
1
Recent
catalytic
depolymerization techniques
can
convert lignin
to
various
42
value−added phenolic monomers including phenols and aldehydes.26−31 Lignin−derived
43
phenol monomers (LDPMs) have been extensively studied as BPA alternatives. Since
44
cross−linkable epoxy monomers require at least two epoxides per molecule, special efforts
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have been taken to increase the number of functional hydroxyl groups of LDPMs through (1)
46
conversion of other reactive groups like methoxy, double bond, or aldehyde to hydroxyl
47
groups,32−37 and (2) coupling repeated LDPMs using bridging reagents.38−48 Despite the
48
abundance of LDPMs and their coupling methods, lignin−derived aldehyde monomers
49
(LDAMs) are often neglected as renewable bridging reagents (akin to acetone in the
50
preparation of BPA). A few examples include the work of Foyer et al., in which a synthesis
51
route of formaldehyde−free resol resin based on vanillin was reported.
52
hydroxyl group of vanillin had to be protected prior to polymerization because the hydroxyl
53
of vanillin was deprotonated preferentially over phenols. Moreover, it is important to develop
54
building blocks that can yield polymer with tunable properties permitting wider applications.
55
For example, LDAMs can condense with phenols at the para and/or ortho position to yield
56
triphenols (TPs). The TP architecture improves the rigidity compared to conventional
57
bisphenolic systems, while adjusting the number of functional hydroxyl could tune the
58
cross−linking density and therefore mechanical properties of the resulting networks.
59
Furthermore, functionalizing the hydroxyl groups to epoxy, olefin, or cyanate ester results in
60
different types of materials.
49,50
However, the
51
61
Apart from the aromatic nature, lignin is characterized by methoxy substitution of its
62
aromatic rings. There are three types of monolignols (para−coumaryl alcohol, coniferyl
63
alcohol and sinapyl alcohol) existing in the lignin backbone, which form p−hydroxyphenyl
64
(H), guaiacyl (G) and syringyl (S), with varying number of methoxy groups.52,53 In our
65
previous studies, o−demethylation of methoxy groups has been proved as an efficient
66
method to convert lignin−derived phenols into cross−linkable epoxy prepolymer.
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25,32,43,51
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However, the presence of methoxy in polymers can alter the properties and should be
68
investigated. For example, methoxy substitution plays an important role in determining the
69
physiochemical properties of lignin. Lignin with high methoxy groups (e.g., hardwood lignin)
70
generally is less thermally stable and produces less char compared to the low methoxys
71
counterparts (e.g., softwood lignin) during lignin pyrolysis.54,55 Several experimental and
72
theoretical studies have shown that oxygen−carbon bond dissociation enthalpy was
73
substantially decreased when ortho or para methoxy substituent was situated on the
74
phenethyl of the dominant β−O−4 linkages.56−58 Inspired by these studies, we set out to
75
investigate the impact of methoxy substituents on the performance of lignin−derived
76
polymers. Hernandez et al. recently reported a bio−based epoxy resin using bis−guaiacol
77
(BG), which was synthesized from vanillyl alcohol and guaiacol.59 To investigate the impact
78
of methoxy groups, BG−based resin was compared to bisphenol F (BPF) based polymer.
79
The methoxy groups lower the glass transition temperature (Tg) and thermal stability of the
80
resulting resins. Harvey et al. reported similar results when making cyanate ester resins with
81
lignin−based bis−creosol, while the significant decrease in thermal stability was attributed to
82
the electron donating effect of methoxy.60 While these studies provided important
83
information on the impact of methoxy substitution, they focused on guaiacol (one methoxy
84
substituent) and ignored syringyl type substrates, which are abundant in hardwood lignin.
85
With the triphenol architecture used in this work, we are able to contrast triphenols with 0−6
86
methoxy substituents. Apart from the thermomechanical properties of thermosets, the
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feasibility and processability of thermoset precursors (e.g. bisphenol or triphenol) should
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also be considered. Effect of methoxy on properties of these precursors, including
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conversion, difficulty in isolation, yield and melting point needs to be discerned, especially
90
when methoxy substitution is high, 3−6 per molecule.
91
In the present work we report: 1) Synthesis of fully lignin−derived TPs. The synthesis of
92
TPs employs lignin−derived aromatic aldehydes as bridging reagents, which avoids
93
carcinogenic and highly volatile formaldehyde. 2) The impact of methoxy groups on
94
performance of TP−based thermosets. By controlling the starting LDAMs, i.e.,
95
4−hydroxybenzaldehyde (HBA), vanillin (VAN), syringaldehyde (SYA), and LDPMs, i.e.,
96
phenol (PhOH, it was used to compare with other methoxy−bearing phenols, even though it
97
has more petroleum nature), guaiacol (GUA) and 2,6−dimethoxyphenol (DMP), we
98
prepared TPs with 0 to 6 methoxy substituents. Selected TPs were converted to glycidyl
99
ethers and cured to explore their feasibility as precursors to make renewable epoxy resins
100
(Figure 1).
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EXPERIMENTAL SECTION
102
General.
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2,6−dimethoxyphenol, epichlorohydrin, tetrabutylammonium bromide, diethylenetriamine
104
(DETA), diglycidyl ether of bisphenol A (DGEBA) and 1,2,4,5−tetrachloro−3−nitrobenzene
105
were purchased from Aldrich Chemical Co. Ethanol (200 proof) was purchased from Decon
106
Labs, Inc. Sulfuric acid (98%) was obtained from Fisher Scientific. All chemicals were used
107
as received without further purification.
108
General Procedure for TPs (M0 to M6).
4−Hydroxybenzaldehyde,
vanillin,
syringaldehyde,
phenol,
guaiacol,
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4−Hydroxybenzaldehyde (2.44 g, 20 mmol) and phenol (7.52 g, 80 mmol) were
110
dissolved in 30 mL absolute ethanol. To this solution, 5.7 g of concentrated sulfuric acid,
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dissolved in 5 mL of absolute ethanol, were dropwise added while stirred. An ice bath was
112
used to control the temperature below 10 °C. After the addition of sulfuric acid, the
113
temperature was increased to 65 °C and the mixture was gently stirred for 2 days. Then,
114
100 mL of brine was poured into the mixture prior to the addition of 3 × 20 mL of ethyl
115
acetate to extract the product. The extract was dried with MgSO4 and concentrated using a
116
rotary evaporator. Purification of the product using silica gel chromatography (hexane/ethyl
117
acetate, 3:1 to 1:1) gave M0 as an orange solid (4.26 g, 69% isolated yield). H NMR
118
(acetone−d6, 400 MHz, Figure S1−A) δ: 6.91 (d, J = 8.4, 6H, c), 6.73 (d, J = 8.4, 6H, b), 5.30
119
(s, 1H, a).
120
54.26 (Ar3−CH). Anal. calc. for C19H16O3: C 78.06, H 5.52, O 16.42; found: C 77.47, H 5.30,
121
O 17.23. Other TPs (M1 to M6) were prepared using the same methods as M0. Their
122
structures are listed in Figure 2.
1
13
C NMR (acetone−d6, 400 MHz, Figure S1−B) δ: 155.4, 135.9, 130.0, 114.7,
123
M1, prepared from vanillin (3.04 g, 20 mmol) and phenol (7.52 g, 80 mmol), orange
124
solid (3.93 g, 61 % isolated yield). H NMR (acetone−d6, 400 MHz, Figure S2−A) δ: 6.93 (d,
125
J = 5.6, 4H, f), 6.74−6.71 (m, 6H, g+d+e), 6.51 (dd, J = 5.4, 1.2, 1H, c), 5.31 (s, 1H, a), 3.71
126
(s, 3H, b).
127
135.9, 130.0, 121.6, 114.8, 114.4, 112.7, 55.24 (−OCH3), 54.67 (Ar3−CH). Anal. calc. for
128
C20H18O4: C 74.52, H 5.63, O 19.85; found: C 74.23, H 5.44, O 20.33.
1
13
C NMR (acetone−d6, 400 MHz, Figure S2−B) δ: 155.5, 147.1, 144.7, 136.5,
129
M2, prepared from 4−hydroxybenzaldehyde (2.44 g, 20 mmol) and guaiacol (9.92 g, 80
130
mmol), orange solid (3.66 g, 52% isolated yield). 1H NMR (acetone−d6, 400 MHz, Figure
131
S3−A) δ: 6.93 (dd, J = 15.3, 8.5, 2H, d), 6.73 (t, J = 7.8, 6H, g+c+e), 6.53 (dd, J = 8.1, 1.7,
132
2H, f), 5.32 (s, 1H, a), 3.71 (s, 6H, b).
13
C NMR (acetone−d6, 400 MHz, Figure S3−B) δ:
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155.5, 147.1, 144.7, 136.4, 135.8, 130.0, 121.6, 114.7, 114.4, 112.7, 55.25 (−OCH3), 55.05
134
(Ar3−CH). Anal. calc. for C21H20O5: C, 71.58; H, 5.72; O, 22.70; found: C 71.47, H 6.33, O
135
20.20.
136
M2’, prepared from syringaldehyde (3.64 g, 20 mmol) and phenol (7.52 g, 80 mmol),
137
orange solid (4.51 g, 64% isolated yield). 1H NMR (acetone−d6, 400 MHz, Figure S4−A) δ:
138
6.94 (d, J = 8.5, 4H, d), 6.73 (d, J = 8.5, 4H, e), 6.38 (s, 2H, c), 5.32 (s, 1H, a), 3.71 (s, 6H,
139
b).
140
125.7, 110.4, 102.5, 51.34 (−OCH3), 50.68 (Ar3−CH). Anal. calc. for C21H20O5: C, 71.58; H,
141
5.72; O, 22.70; found: C 70.95, H 5.77, O 23.28.
13
C NMR (acetone−d6, 400 MHz, Figure S4−B) δ: 151.2, 143.2, 132.5, 131.4, 129.9,
142
M3, prepared from vanillin (3.04 g, 20 mmol) and guaiacol (9.92 g, 80 mmol), orange
143
solid (3.90 g, 51% isolated yield). 1H NMR (acetone−d6, 400 MHz, Figure S5−A) δ:
144
6.77−6.71 (m, 6H, c+e), 6.54 (m, J = 8.1, 1.7, 3H, d), 5.32 (s, 1H, a), 3.71 (s, 9H, b).
145
NMR (acetone−d6, 400 MHz, Figure S5−B) δ: 147.1, 144.7, 136.4, 121.6, 114.4, 112.7,
146
55.44 (Ar3−CH), 55.29 (−OCH3). Anal. calc. for C22H22O6: C, 69.10; H, 5.80; O, 25.10; found:
147
C 68.47, H 5.86, O 25.68.
13
C
148
M4, prepared from syringaldehyde (3.64 g, 20 mmol) and guaiacol (9.92 g, 80 mmol),
149
orange solid (3.79 g, 46% isolated yield). H NMR (acetone−d6, 400 MHz, Figure S6−A) δ:
150
6.78 – 6.69 (m, 4H, f+e), 6.56 (dd, J = 5.4, 1.1, 2H, g), 6.43 (s, 2H, d), 5.32 (s, 1H, a), 3.71 (s,
151
6H, b), 3.69 (s, 6H, c). C NMR (acetone−d6, 400 MHz, Figure S6−B) δ: 147.4, 146.9, 144.7,
152
136.2, 135.5, 121.6, 114.3, 112.7, 106.9, 55.76 (Ar3−CH), 55.67 (−OCH3), 55.28 (−OCH3).
153
Anal. calc. for C23H24O7: C, 66.98; H, 5.87; O, 27.15; found: C 66.69, H 6.53, O 26.78.
154
1
13
M4’,
prepared
from
4−hydroxybenzaldehyde
(2.44
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20
mmol)
and
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2,6−dimethoxyphenol (12.32 g, 80 mmol), orange solid (1.48 g, 18% isolated yield). 1H NMR
156
(acetone−d6, 400 MHz, Figure S7−A) δ: 6.95 (d, J = 8.4, 2H, d), 6.74 (d, J = 8.4, 2H, c), 6.43
157
(s, 4H, e), 5.32 (s, 1H, a), 3.71 (s, 12H, b). 13C NMR (acetone−d6, 400 MHz, Figure S7−B) δ:
158
151.2, 143.2, 131.3, 130.9, 129.9, 125.7, 110.4, 102.5, 51.38 (−OCH3 and Ar3−CH). Anal.
159
calc. for C23H24O7: C, 66.98; H, 5.87; O, 27.15; found: C 66.14, H 5.65, O 28.22.
160
M5, prepared from vanillin (3.04 g, 20 mmol) and 2,6−dimethoxyphenol (12.32 g, 80
161
mmol), orange solid (0.62 g, 7% isolated yield). H NMR (acetone−d6, 400 MHz, Figure
162
S8−A) δ: 6.77 (d, J = 1.2, 1H, d), 6.72 (dd, J = 5.3, 2.7, 1H, f), 6.57 (dd, J = 5.4, 1.2, 1H, e),
163
6.45 (s, 4H, g), 5.32 (s, 1H, a), 3.72 (s, 3H, b), 3.70 (s, 12H, c).
164
MHz, Figure S8−B) δ: 143.1, 131.7, 130.8, 129.9, 117.2, 110.0, 108.3, 102.5, 51.71
165
(−OCH3), 51.33 (−OCH3), 50.93 (Ar3−CH). Anal. calc. for C24H26O8: C, 65.15; H, 5.92; O,
166
28.93; found: C 68.30, H 6.47, O 25.23.
1
13
C NMR (acetone−d6, 400
167
M6, prepared from syringaldehyde (3.24 g, 20 mmol) and 2,6−dimethoxyphenol (12.32
168
g, 80 mmol), orange solid (0.47 g, 5% isolated yield). H NMR (acetone−d6, 400 MHz,
169
Figure S9−A) δ: 6.46 (s, 6H, c), 5.32 (s, 1H, a), 3.71 (s, 18H, b). 13C NMR (acetone−d6, 400
170
MHz, Figure S9−B) δ: 147.5, 135.1, 106.8, 56.40 (Ar3−CH), 55.72(−OCH3). Anal. calc. for
171
C25H28O9: C, 63.55; H, 5.97; O, 30.47; found: C 62.70, H 6.19, O 31.11.
172
General Procedure for Glycidyl Ethers of TPs (GEM0 to GEM6).
1
173
GEM0 was prepared by reaction of M0 (2.92 g, 10 mmol) and epichlorohydrin (30 g, 320
174
mmol). Tetrabutylammonium bromide (0.34 g, 1.1 mmol) was used as a phase transfer
175
catalyst. The mixture was heated at 85 °C for 3 h and followed by a dropwise addition of 6 g
176
of 20% w/w NaOH solution. The reaction was kept for another 1.5 h, and the mixture was
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washed with 15 mL acetone to precipitate the formed NaCl, filtrated to remove NaCl, dried
178
with Na2SO4 and concentrated with a rotary evaporator to yield GEM0 as a yellowish oil
179
(4.33 g, 94% isolated yield). 1H NMR (CDCl3, 600 MHz, Figure S10) δ: 6.91 (6H, f), 6.73 (6H,
180
e), 5.37 (1H, a), 4.15−3.91 (6H, b + b’), 3.32 (3H, c), 2.87−2.71 (6H, d + d’). Other glycidyl
181
ethers (GEM1 to GEM6) were prepared using the same method with 87−96% yields of
182
glycidylation. Epoxy equivalent weights (EEW) of obtained epoxy monomers were
183
determined to be 160−218 g/eq. using the HCl/acetone titration method.
61
184
GEM1, yellowish oil, 94 % isolated yield, EEW = 169 g/eq. 1H NMR (CDCl3, 600 MHz,
185
Figure S11) δ: 6.93 (4H, i), 6.8−6.71 (4H, j+h), 6.25 (1H, g), 6.51 (1H, f), 5.36 (1H, a),
186
4.17−3.91 (6H, b + b’), 3.71 (3H, e), 3.35 (3H, c), 2.88−2.71 (6H, d + d’).
187
GEM2, yellowish oil, 91 % isolated yield, EEW = 179 g/eq. 1H NMR (CDCl3, 600 MHz,
188
Figure S12) δ: 6.93 (2H, g), 6.73 (4H, i+f), 6.64 (2H, h), 6.53 (2H, j), 5.36 (1H, a), 4.18−3.91
189
(6H, b + b’), 3.73 (6H, e), 3.35 (3H, c), 2.86−2.71 (6H, d + d’). 1
190
GEM2’, yellowish oil, 96 % isolated yield, EEW = 181 g/eq. H NMR (CDCl3, 600 MHz,
191
Figure S13) δ: 6.94 (4H, g), 6.73 (4H, h), 6.38 (2H, c), 5.33 (1H, a), 4.18−3.97 (6H, b + b’),
192
3.73 (6H, e), 3.31 (3H, c), 2.86−2.61 (6H, d + d’). 1
193
GEM3, white solid, melting point 115 °C, 87 % isolated yield, EEW = 194 g/eq. H NMR
194
(CDCl3, 600 MHz, Figure S14) δ: 6.77 (3H, i) 6.71 (3H, g), 6.54 (3H, h), 5.34 (1H, a),
195
4.18−3.99 (6H, b + b’), 3.73 (9H, e), 3.36 (3H, c), 2.86−2.71 (6H, d + d’). 1
196
GEM4, yellowish oil, 89 % isolated yield, EEW = 199 g/eq. H NMR (CDCl3, 600 MHz,
197
Figure S15) δ: 6.78 (2H, j), 6.69 (2H, h), 6.56 (2H, i), 6.43 (2H, g), 5.33 (1H, a), 4.18−3.96
198
(6H, b + b’), 3.73 (9H, e), 3.69 (9H, f), 3.36 (3H, c), 2.87−2.61 (6H, d + d’).
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199
GEM4’, yellowish oil, 91 % isolated yield, EEW = 200 g/eq. 1H NMR (CDCl3, 600 MHz,
200
Figure S16) δ: 6.95 (2H, g), 6.74 (2H, f), 6.43 (4H, e), 5.33 (1H, a), 4.28−3.96 (6H, b + b’),
201
3.73 (12H, e), 3.32 (3H, c), 2.88−2.61 (6H, d + d’). 1
202
GEM5, yellowish oil, 89 % isolated yield, EEW = 210 g/eq. H NMR (CDCl3, 600 MHz,
203
Figure S17) δ: 6.85 (1H, g), 6.64 (1H, i), 6.58 (1H, h), 6.43 (4H, j), 5.31 (1H, a), 4.19−3.96
204
(6H, b + b’), 3.73 (3H, e), 3.66 (12H, f), 3.35 (3H, c), 2.87−2.61 (6H, d + d’). 1
205
GEM6, yellowish oil, 87 % isolated yield, EEW = 218 g/eq. H NMR (CDCl3, 600 MHz,
206
Figure S18) δ: 6.29 (6H, f), 5.31 (1H, a), 4.16−3.96 (6H, b + b’), 3.73 (18H, e), 3.36 (3H, c),
207
2.77−2.61 (6H, d + d’).
208
Formation of Epoxy Networks.
209
Four epoxy monomers (GEM0, GEM2, GEM2’ and GEM4) with 0−4 methoxy groups
210
were used to make epoxy networks. GEM6 was not used because of the low isolated yield of
211
M6 (5%), which makes it unreasonable for preparing renewable materials. The monomers
212
were respectively mixed with diethylenetriamine (DETA) with 1:1 molar ratio of epoxy vs.
213
−NH for curing. The mixtures were stirred for 10 min, degassed under vacuum to remove
214
entrapped air and poured into silicone molds for curing with the profile: 65 °C for 8 h, 90 °C
215
for 2 h and 120 °C for 2 h. Cured epoxy networks were expressed as ENM0, ENM2, ENM2’
216
and ENM4, respectively. Degree of cure were monitored using Fourier transform infrared
217
(FTIR). Conventional BPA−based epoxy network (ENBPA) was prepared from DGEBA and
218
DETA using the same method with TP−based materials.
219
Analysis Methods.
220
Chemical structure and conversion of TPs were followed using nuclear magnetic
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resonance (NMR) spectroscopy. NMR spectra were collected on an Agilent 400−MR DDR2
222
400 MHz spectrometer or a Varian Unity Inova 600 MHz spectrometer. Deuterated acetone
223
or chloroform were used as solvent. 1,2,4,5−Tetrachloro−3−nitrobenzene was used as the
224
NMR internal standard. FTIR analyses were conducted using a Thermo−Nicolet Nexus 470
225
FTIR Spectrometer equipped with an ultra−high−performance, versatile Attenuated Total
226
Reflectance (ATR) sampling accessory. The spectra were scanned over a wavenumber
227
range of 400−4000 cm
228
a capillary melting point apparatus (MEL−TEMP) with a heating rate of 5 °C/min.
−1
−1
with a resolution of 4 cm . The melting point was measured using
229
Crystal of M6 was obtained from slow evaporation of an ethyl acetate solution at room
230
temperature. The crystal was mounted on a cryo−loop and transferred to a Bruker Kappa
231
APEX II diffractometer. The APEX2 program was used to determine the unite cell
232
parameters and data collection (30 sec / frame, 0.5 deg. /frame Omega scan). The data was
233
collected at 100 K using Oxford nitrogen gas cryostream system. The raw frame data was
234
processed using SAINT program. The absorption correction was applied using program
235
SADABS. Subsequent calculations were carried out using SHELXTL program. The
236
structure was solved by direct methods and refined on F2 by full−matrix least−squares
237
techniques. Hydrogen atoms were located theoretically.
238
Differential scanning calorimetry (DSC Q−2000, TA Instruments) was conducted under
239
dry nitrogen atmosphere to monitor exothermic peak temperature. Samples of 5−10 mg
240
were placed in sealed aluminum pans for all DSC runs. Peak temperature and enthalpy
241
were obtained through heating the samples from 10 to 200 °C at a rate of 10 °C/min.
242
Dynamic mechanical properties were characterized using a DMA 2980 (TA
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Instruments). Rectangular specimens with dimensions of 30 mm length, 12.5 mm width and
244
2.5 mm thickness were measured in a single−cantilever mode. The measurements were
245
conducted from 35 to 180 °C at a heating rate of 3 °C/min and a frequency of 1 Hz. The
246
temperature at the maximum in the tan δ curve was taken as Tα (related to Tg).
247
Tensile testing was performed on dog−bone shaped specimens according to the ASTM
248
D638 standard, on a custom−built setup on a vertical TwinRail positioning table (Lintech, CA)
249
with a 100 N load cell. Crosshead speed was set to 0.5 mm/min.
250
Thermal stability studies were carried out on a Discovery Thermo−Gravimetric Analyzer
251
(TGA, TA Instruments) under a nitrogen flow of 40 mL/min. Samples (5−10 mg) were placed
252
in a platinum pan and scanned from 40 to 600 °C at a ramp rate of 20 °C/min.
253
RESULTS AND DISCUSSION.
254
Structure of TPs and Glycidyl Ethers.
255
Triphenylmethane architecture provides a convenient way to manipulate the number of
256
methoxy substituents by employing different starting aldehydes and phenols. To establish
257
the resulting structure, proton and carbon NMR spectra of M0 to M6 are provided in Figures
258
S1−S9 (trace amounts of triphenol isomers with aldehydes coupled at the ortho and/or meta
259
position of phenols are also included in these figures). The proton peak at ~ 5.3 ppm
260
corresponds to the triphenylmethyl group, which indicates successful condensation of the
261
aldehyde and phenol. The characteristic methoxy groups are observed at ~ 3.7 ppm, while
262
aromatic protons are found in the range of 6.3−6.9 ppm. For the carbon NMR, the
263
triphenylmethyl and methoxy groups are observed in the range 50.6−55.7 ppm. While the
264
para position of phenol is the main site for aldehyde coupling, it is noteworthy that certain
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amount of ortho or meta coupled byproducts are also observed in the proton spectra, with
266
molar ratio below 8 % of the product mixture. The dominant para−coupled products were
267
previously observed, which was related to their higher reactivity and less steric hindrance of
268
the para site.
269
are given in Figure S10−S18. Compared to TPs, new characteristic peaks are identified at
270
3.91−4.19 ppm (−CH2−, b and b’), 3.35 ppm (−CH−, c) and 2.61−2.87 ppm (−CH2− in epoxy
271
ring, d and d’), which are indicative of epoxy groups.
59
Proton NMR spectra of the corresponding glycidyl ethers (GEM0 to GEM6)
272
Because of the structural similarity of TPs, only one crystal structure (M6, prepared
273
from syringaldehyde and dimethoxyphenol) was obtained to confirm the structure and
274
determine the main coupling sites. Figure 3 reveals syringaldehyde couples exclusively at
275
the para sites of both dimethoxyphenol. Coupling at para sites provides TPs with stretched
276
orientation of hydroxyl groups (Figure 3). Together with its rigid architecture and high
277
number of hydroxyl groups (n= 3), TP−based polymers are supposed to exhibit satisfactory
278
mechanical properties.
279
Structure of TPs is further confirmed by IR spectra shown in Figures S19−S27. Starting
280
aldehydes (HBA, VAN and SYA) have an aldehyde peak around 1672 cm−1. After they are
281
condensed with phenols, the aldehyde group becomes triphenylmethyl group. This is
282
consistent with the IR spectra of TPs in which the aldehyde peak disappears (Figures
283
S19−S27, panels a). Other characteristic bands comprise 3058−3586 cm
284
and 1608, 1510 and 1437 cm−1 (aromatic C−C bond). When TPs are converted to glycidyl
285
ethers, the broad hydroxyl band diminishes significantly, while a new epoxy ring band at 912
286
cm
−1
−1
(O−H stretching),
emerges (Figures S19−S27, panels b). This is consistent with the NMR analysis
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287
confirming the presence of epoxide. This conclusion is further supported by the IR spectra
288
of the cured thermosets in Figures S19−S27, panels c. When epoxy monomers are cured
289
with DETA, epoxy groups are opened by amine while hydroxyl groups are created
290
concurrently. This process is reflected by the IR results, in which the epoxy band at 912
291
cm−1 disappears while the OH band around 3355 cm−1 increases. The absence of epoxy
292
bond is indicative of significant conversion of epoxy groups in our investigated networks.
293
Meanwhile, high reactivity of epoxy/DETA system is confirmed by two cycles of
294
heating−cooling using DSC analysis (Figure S28), as supported by the lack of an exotherm
295
on the second heating cycle. The high conversion of epoxy groups is mainly attributed to the
296
high reactivity of DETA. Meanwhile, at elevated temperature with the catalytic effect of
297
amine, the epoxy could also undergo ring−open polymerization.
298
Effect of Methoxy Substituents on Yields of TPs.
299
To study the conversion of TPs, aldehyde and phenol were reacted under the following
300
conditions: molar ratio of aldehyde: phenol = 1:4, aldehyde: H2SO4 = 1:3, absolute ethanol
301
was used as solvent and the mixture was stirred at 65 °C for 48 hours. Conversions were
302
calculated based on integrals of aldehyde and triphenylmethyl peaks in the proton spectra.
303
Table 1 lists the conversion of TPs prepared from different aldehydes and phenols.
304
Generally, conversions decrease with increased number of methoxy groups (from 83% for
305
M0 to 35% for M6). Comparisons between starting aldehydes and phenols reveal reactivity
306
of aldehydes (HBA > VAN > SYA) and phenols (PhOH > GUA > DMP) decreases with
307
increased number of methoxy substituents (Table 1). The negative effects of methoxy group
308
on conversion could be attributed to: 1) steric effect of methoxy, and 2) the electron donation
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of the hydroxyl and methoxy substituents increases the nucleophilicity of the ring system.
310
Due to resonance structures, the substituents favor the positions ortho and para to each
311
phenol or methoxy group. Increasing the number of substituents would therefore spread the
312
electron density over multiple sites.
313
Compared to conversion, methoxy groups have even greater impact on isolated yields.
314
For TPs (M0 to M4) that were prepared from aldehydes (HBA, VAN and SYA) and phenols
315
(PhOH and GUA), satisfactory isolated yields of 46−69% were achieved. However, when
316
2,6−dimethoxyphenol (DMP) was reacted with aldehydes, only 18%, 7% and 5% isolated
317
yields were obtained for M4’, M5 and M6, respectively. Low isolated yields of DMP−based
318
TPs could be attributed to: 1) low conversions of these TPs (35−49%), and/or 2) the steric
319
hindrance of the initially formed diphenyl intermediate. The reaction mixtures contain certain
320
amount of the diphenyl intermediate (proton NMR spectrum of the intermediate exhibits no
321
triphenylmethyl peak at 5.3 ppm). These undesired intermediates exhibit similar polarity with
322
TP products and impair the yields of flash column purification. The low yield of DMP−based
323
TPs makes them unsuitable for use in making renewable polymer materials.
324
Effect of Methoxy Substituents on Melting Point.
325
Melting points of TPs with various number of methoxys are listed in Table 2. The
326
highest melting point is found to be 241 °C (M0), while the lowest is 125 °C (M3). This
327
marked difference highlights the role of methoxy. Melting points of TPs from different
328
aldehydes follow the order: HBA > SYA > VAN, while phenols follow the order: PhOH >
329
DMP > GUA (Table 2). The lower melting points of TPs prepared from di−methoxy
330
substituents (SYA and DMP) than corresponding non−methoxy compounds (HBA and
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331
PhOH) could be explained by the electron donating effect of methoxy. Meanwhile,
332
methoxy−substituted phenols
333
intermolecular H−bonding would be decreased, which leads to lower melting point. As for
334
the mono−methoxy derivatives (VAN and GUA) that exhibit the lowest TP melting points,
335
influence of methoxy may be reflected by its impact on the symmetry of TP units. Symmetric
336
TPs like M0, M2’, M4’ and M6 exhibit melting points above 190 °C. By comparison, when
337
asymmetric units VAN and GUA (only one methoxy at ortho site) are incorporated, melting
338
points of TPs significantly decrease. Especially, M3 with three asymmetric guaiacol units
339
shows the lowest melting point (125 °C) among all TPs. Moreover, impact of unit symmetry
340
can be highlighted when TPs with the same number of methoxy groups are compared. For
341
example, melting point of M2’ (SYA−PhOH, 191 °C) is 27 °C higher than M2 (HBA−GUA,
342
164 °C), while M4’ (HBA−DMP, 204 °C) is 58 °C higher than M4 (SYA−GUA, 146 °C). The
343
impacts of methoxy on melting points could provide insight in the design of more
344
processable lignin−based thermosetting resins beyond epoxy networks.
345
Effect of Methoxy on Properties of TP−Based Epoxy Thermosets.
346
Differential Scanning Calorimetry (DSC) Analysis.
can
participate
in
intramolecular
H−bonding,
while
347
Effect of methoxy group on curing behavior is studied via DSC. Table 3 shows that
348
enthalpy (∆H) values of all curing systems fall in the range 91.5 to 96.4 kJ/ee, which is in
349
62 accordance with the typical value of 90−100 kJ/ee for epoxy/amine reactions. Table 3
350
demonstrates peak curing temperatures are not significantly different for all studied
351
monomers: GEM0 (81 °C), GEM2’ (80 °C), GEM2 (78 °C) and GEM4 (77 °C), which indicates
352
methoxy group has no impact on the epoxy/amine curing reaction. This could be attributed
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to the inert nature of methoxy, which cannot catalyze the epoxy/amine reaction.63 The
354
degree of curing was determined through two cycles of heating. As demonstrated in Figure
355
S28, all epoxy monomers are mostly cured as supported by the lack of an exotherm in the
356
second heating cycle.
357
Dynamic Mechanical Analysis (DMA) and Tensile Analysis (TA).
358
Figure 4 and Table 4 show that Tα (α−relaxation temperature, related to Tg) of
359
thermosets decreases gradually with increased content of methoxy groups, i.e., ENM0
360
(132 °C) > ENM2’ (125 °C) > ENM2 (120 °C) > ENM4 (118 °C). Similar negative effect of
361
methoxy substitution on thermomechanical performance was reported for cyanate ester
362
resins.60 Even though some methoxys could form hydrogen bonds with hydroxyls that
363
improves the network constraint, reduced cross−link density on a mass/volume basis
364
caused by methoxy groups seems to play a more important role decreasing Tα. Storage
365
modulus (E’) curves of TP−based thermosets are displayed in Figure 4 and values given in
366
Table 4. Similar to Tα, increasing the content of methoxy reduces the storage modulus from
367
ENM0 to ENM4. It is noteworthy that glassy modulus (E30’, storage modulus at 30 °C) values
368
are in the range of 2.2 to 2.6 GPa. To compare the mechanical performance of TP−based
369
polymers
370
diethylenetriamine were cured using the same profiles with TP−based networks. The E30’
371
and Tα of DGEBA/DETA system (ENBPA) were measured to be 2.0 GPa and 103 °C (Figure
372
4 and Table 4), which is lower than our TP−based thermosets. Meanwhile, tensile properties
373
of TP and BPA−based thermosets are illustrated in Figure 5. TP−based thermosets exhibit
374
similar rigidity, i.e., max stress of 74.9 to 80.0 MPa and elongation at break of 2.55 to 2.68%,
with
BPA–based
materials,
diglycidyl
ether
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BPA
(DGEBA)
and
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375
while ENBPA is slightly more elastic with stress of 65.2 MPa and strain of 3.56%. These
376
results are attributed to the more rigid structure and higher functionality of TPs over BPA.
377
Moreover, TP−based epoxy networks possess marked mechanical performance that can
378
replace or supplement BPA−based analogues.
379
Thermogravimetric Analysis (TGA).
380
Figure 6 reveals a one−step degradation curve for all TP−based epoxy networks.
381
Figure 6 and Table 4 illustrate that the thermal stability of cured networks decreases with
382
increased content of methoxy (i.e., ENM0 > ENM2’ > ENM2 > ENM4). This is reflected from
383
the significant shift of onset degradation temperature (defined as Td5, temperature at 5%
384
weight loss) from ENM0 (257 °C) to ENM2’ (218 °C), ENM2 (206 °C) and ENM4 (184 °C),
385
respectively. The effect of methoxy substitution is attributed to its electron donation ability.60
386
Meanwhile, as methoxy groups increase, content of oxygen within the polymers increases,
387
which accelerates thermal decomposition. Moreover, the steric effect of methoxy might
388
decrease the degree of glycidylation, while formed side−products or impurities may lower
389
the thermal stability. Td30 (temperature at 30% weight loss) of cured samples reveal the
390
same trend with Td5, which confirms the effect of methoxy substitution. Besides, for M2 and
391
M2’ that have similar methoxy contents, they exhibit close values of Td5, Td30 and Ts (statistic
392
heat−resistant index temperature, calculated using equation 1). This further supports the
393
relationship between methoxy substituents number and thermal performance of the
394
resulting epoxy networks. As for the BPA−based network, it exhibits higher thermal stability
395
than TP−based thermosets as reflected by Td5 (305 °C), Td30 (371 °C) and Ts (169 °C). This
396
could be attributed to the triphenylmethane architecture of TP that is easily oxidized, as well
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as the electron donating effects of the methoxy groups. When the temperature reaches
398
330 °C, ENBPA exhibits a fast degradation behavior and only 8 wt % char was left when the
399
temperature reaches 600 °C. As for the TP−based networks, they start to exhibit higher
400
stability over ENBPA above 391 °C, with 17−23 wt % char formed at 600 °C.
Ts = 0.49[Td 5 + 0.6(Td 30 − Td 5 )]
401 402
(1)
CONCLUSIONS
403
Preparation of renewable TPs with 0−6 methoxy substituents is described. While the
404
rigid architecture and improved number of hydroxyl of the TP backbone afford epoxy
405
networks with marked properties, the dangling methoxy groups are found to have different
406
levels of impact on the resulting polymers. Because of its chemical inertness, the methoxy
407
group has no impact on the curing process (curing temperature and enthalpy). By
408
comparison, increasing methoxy content results in a decrease in thermomechanical
409
properties (Tα decreases from 132 to 118 °C, and glassy modulus decreases from 2.6 to 2.2
410
GPa). The greater impact of methoxy substitution is related to thermal performance, in
411
which onset degradation temperature decreases significantly from 257 °C for ENM0 (no
412
methoxy substituents) to 184 °C for ENM4 (four methoxy substituents). The greatest impact
413
is on the conversion and especially isolated yields of TPs, which determines the feasibility of
414
using these monomers in the manufacture of renewable polymers. Using harsher conditions
415
like increasing the reaction temperature with the aid of higher boiling solvents or microwave
416
irradiation may increase the yields, especially for TPs with higher content of methoxy. The
417
different impacts of methoxy substitution can guide the selection and/or modification (e.g.
418
deoxygenation) of lignin−derived monomers for making epoxy polymers with desirable
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419
properies. Decreased Tg and thermal stability as methoxy content increases may also
420
provide insight in the degradation of thermosets.
421
Supporting Information
422
Proton and carbon NMR, and FTIR spectra of all new compounds. DSC curing curves for
423
epoxy/amine systems to examine degree of cure. X−ray structure of M6.
424
ACKNOWLEDGMENTS
425
This research was supported by the Center for direct Conversion of Biomass to Biofuels
426
(C3Bio), an Energy Frontiers Research Center (EFRC) funded by the U.S. Department of
427
Energy, Office of Science, Office of Basic Energy Sciences under Award No. DE−SC000097,
428
National Science Foundation CBET−1624183, the University of California, Santa Barbara,
429
and the Mellichamp Academic Initiative in Sustainability. We acknowledge the use of the
430
MRL Shared Experimental Facilities, supported by the MRSEC Program of the National
431
Science Foundation under award NSF DMR 1121053; a member of the NSF−funded
432
Materials Research Facilities Network.
433
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Chemo−enzymatic synthesis and thermo−mechanical properties characterization. Ind.
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A. Structure property relationships of biobased n−alkyl bisferulate epoxy resins. Green
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Chem. 2016, 18 (18), DOI 10.1039/C6GC01308B.
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monomers: effect of cross−linking density. ACS Sustainable Chem. Eng. 2016, 4 (11), DOI
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(44) Wang, S.; Ma, S.; Xu, C.; Liu, Y.; Dai, J.; Wang, Z.; Liu, X.; Chen, J.; Shen, X.; Wei, J.
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Vanillin−derived high−performance flame retardant epoxy resins: facile synthesis and
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properties. Macromolecules 2017, 50 (5), DOI 10.1021/acs.macromol.7b00097.
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(45) Hitce, J.; Crutizat, M.; Bourdon, C.; Vivès, A.; Marat, X.; Dalko−Csiba, M.
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Flash−metathesis for the coupling of sustainable (poly) hydroxyl β−methylstyrenes from
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essential oils. Green Chem. 2015, 17 (7), DOI 10.1039/C5GC00759C.
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(46) Shibata, M.; Tetramoto, N.; Imada, A.; Neda, M.; Sugimoto, S. Bio−based
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thermosets
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wheat
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bran
and
beetroot
pulp:
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thermosetting bismaleimide resins using eugenol, bieugenol and eugenol novolac. React.
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Funct. Polym. 2013, 73 (8), DOI 10.1016/j.reactfunctpolym.2013.05.002.
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epoxy: shape memory, repairing, and recyclability. Macromolecules 2017, 50 (21), DOI
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(48) Wan, J.; Zhao, J.; Gan, B.; Li, C.; Molina−Aldareguia, J.; Zhao, Y.; Pan, Y. T.; Wang, D.
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Y. Ultrastiff biobased epoxy resin with high Tg and low permittivity: from synthesis to
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(49) Foyer, G.; Chanfi, B. H.; Boutevin, B.; Caillol, S.; David, G. New method for the
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synthesis of formaldehyde−free phenolic resins from lignin−based aldehyde precursors. Eur.
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Polym. J. 2016, 74, DOI 10.1016/j.eurpolymj.2015.11.036.
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(50) Foyer, G.; Chanfi, B. H.; Virieux, D.; David, G.; Caillol, S. Aromatic dialdehyde
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precursors from lignin derivatives for the synthesis of formaldehyde−free and high char yield
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phenolic resins. Eur. Polym. J. 2016, 77, DOI 10.1016/j.eurpolymj.2016.02.018.
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polyphenols. Macromolecules 2017, 50 (9), DOI 10.1021/acs.macromol.7b00064.
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polymeric materials: review and perspective. Chem. Rev. 2015, 116 (4), DOI
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Synthesis and characterization of bio−based epoxy resins derived from vanillyl alcohol.
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(60) Harvey, B. G.; Guenthner, A. J.; Lai, W. W.; Meylemans, H. A.; Davis, M. C.; Cambrea,
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617
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phosphorus−containing polyol synthesized from cardanol. RSC Adv., 2015, 5, DOI
619
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620
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621
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622
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623
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624
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625
modified montmorillonite on the reaction mechanism of epoxy/amine cure. J. Phys. Chem. B
626
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reaction
and
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development.
627 628 629 630 631 632 633 634 635 636 637 638
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2014,
7,
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639 640 641 642 643 644
Figures and Tables
645 646
Figure 1. Synthesis route of epoxy networks from lignin−derived aldehydes and phenols.
647
648
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649
650
Figure 2. List of TPs with different number of methoxy groups. TPs are abbreviated as Mn,
651
while n indicates the number of methoxy groups. The starting aldehyde and phenol for each
652
TP are also listed in parentheses.
653
654
655
656
657
658
659
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660 661
Figure 3. Crystal structure of M6. Crystal was collected from the slow evaporation of an
662
ethyl acetate solution at room temperature.
663
664
665
666
667
668
669
670
671
672
673
674
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675 676
Figure 4. DMA curve of epoxy networks derived from TPs with different number of methoxy
677
groups. Temperature at the maximum in tan δ curve is taken as Tα (related to Tg).
678
679
680
681
682
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683
684
Figure 5. Tensile tests of epoxy networks derived from TPs with different number of
685
methoxy groups.
686
687
688
689
690
691
692
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693 694
Figure 6. Thermogravimetric analysis thermograms of epoxy networks derived from TPs
695
with different number of methoxy groups.
696 697 698 699 700 701 702 703 704 705 706 707 708 709 35
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710
Table 1. Conversion (%) of TPs Prepared from Lignin−Derived Aldehydes and Phenols with
711
Different Number of Methoxy Groups
a
Aldehyde Phenol
HBA
VAN
SYA
(0)
(1)
(2)
PhOH (0) b
83 c
72
64
GUA (1)
81
68
64
DMP (2)
49
42
35
712
a
713
for 2 days. Absolute ethanol is used as solvent. b Numbers (in parentheses) next to starting
714
aldehydes or phenols indicate the number of methoxy groups situated on these reagents.
715
Numbers in the table means conversion (%) of TPs prepared from different aldehydes and
716
phenols. For example, 83% is the conversion of TP synthesized from HBA and PhOH.
Reaction conditions: molar ratio of aldehyde: phenol = 1:4, aldehyde: H2SO4 = 1:3, 65 °C
717 718 719 720 721 722 723 724 725 726 727 728
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c
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729
Table 2. Melting Point (°C) of TPs with Different Number of Methoxy Groups a Aldehyde Phenol PhOH (0)
b
HBA
VAN
SYA
(0)
(1)
(2)
188
191
241
c
GUA (1)
164
125
146
DMP (2)
204
133
190
730
a
731
a heating rate of 5 °C/min. Numbers (in parentheses) next to starting aldehydes or phenols
732
indicate the number of methoxy groups situated on these reagents. c Numbers in the table
733
mean melting points (°C) of TPs prepared from corresponding aldehydes and phenols. For
734
example, 241 °C is the melting point of TP synthesized from HBA and PhOH.
Melting points were measured using a capillary melting point apparatus (MEL−TEMP) with b
735 736 737 738 739 740 741 742 743 744 745 746 747
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748
Table 3. DSC Curing Data for Epoxy/DETA Systems Exhibiting Onset Curing Temperature
749
(Ti), Peak Curing Temperature (Tp) and Enthalpy of Reaction (∆H).
750 751 752
753
Ti
Tp
∆H
Theoretic
Measured
(°C)
(°C)
(kJ/ee)
EEW (g/eq.)
EEW (g/eq.)
GEM0
47
81
96
154
160
GEM2
43
78
94
174
179
GEM2’
45
80
95
174
181
GEM4
44
77
92
194
199
sample
754
755
756
757
758
759
760
761
762
763
764
765
766
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767
Table 4. Thermomechanical Data of Tα, E30’ (Glassy Modulus), Td5, Td30 (Temperature at 5%
768
and 30% Weight Loss), Ts (Statistic Heat−Resistant Index Temperature) and Char600 (Char
769
Residue at 600 °C) of Epoxy Networks Derived from TPs and BPA. Tα
E30’
Td5
Td30
Ts
Char600
(°C)
(MPa)
(°C)
(°C)
(°C)
(%)
ENM0
132
2745
257
341
151
20
ENM2
125
2598
206
321
135
17
ENM2’
120
2249
218
324
138
18
ENM4
118
2477
184
296
123
14
ENBPA
100
2042
305
371
169
8
sample
770 771 772 773 774 775 776 777 778 779 780 781 782 783 784
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785
for Table of Contents use only
786 787 788
Synopsis: Methoxy group affects the thermomechanical properties and feasibility of lignin−derived triphenol−based epoxy thermosets.
789 790 791
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