Zhanrong Zhang,
Duncan J. Macquarrie,
James H. Clark and
Avtar S. Matharu*
Green Chemistry Centre of Excellence, Department of Chemistry, University of York, York, England YO10 5DD, UK. E-mail: avtar.matharu@york.ac.uk
First published on 27th August 2014
Adhesives are of pivotal importance in modern society as over 6 billion pounds of adhesives are used globally per annum. Among these, hot melt adhesives (HMAs) represent the most dynamically developing area, reaching 15–21% of the global volume of production and usage of adhesives. The application of expanded high amylose corn starch (HACS) and its propionate derivatives with differing degrees of substitution (DS) in a formulation comprising polyvinyl alcohol (PVOH) and glycerol to afford 100% biodegradable HMAs is reported. Esterification of expanded starch was conducted to increase the stability and hydrophobicity of starch. The effects of amounts of esterifying reagent and reaction time on DS of starch propionates were investigated. Native starch was expanded (BET surface area, 176 m2 g−1; DS = 0) and derived propionate esters were studied by ATR-IR, TGA, 13C CPMAS NMR, 1H NMR and titrimetric methods. The HMAs, irrespective of DS, displayed a Tg at approximately 0 °C, melting (Tpeak) at approximately 160 °C and crystallisation (on cooling) at approximately 115 °C. The adhesive properties (tensile strength) with respect to DS of expanded high amylose corn starch and its propionate esters show a distinct structure–property relationship. Expanded high amylose corn starch (DS = 0) gives the strongest adhesion, outperforming native (non-expanded) starch. The expansion process is beneficial in promoting adhesion which may be linked to the increased availability of hydroxyl moieties promoting better non-covalent interactions and mixing with PVOH and glycerol. Adhesion strengths decrease with increasing DS of base polymer and those of starch propionates with DS in the range 1.46–1.82 are comparable to that of non-expanded HACS based HMA. This is the first reported occurrence of the use of expanded starch and its propionate esters as HMAs.
HMAs are solid materials at low temperatures (<80 °C) and can melt to liquid or viscous-flow state at elevated temperatures, in which form they are applied on the surface of substrates. They regain their solid form and cohesive strength during cooling by solidification and/or crystallization, thus bonding two substrates together.2 Compared with conventional solvent-based adhesives which generally involve evaporation and/or removal of solvents or polymerization to bond substrates together, hot melt adhesives show significant advantages. For example, the elimination of a carrier fluid or solvent in HMA formulations not only overcomes the hazards associated with solvent usage and emissions of volatile organic compounds (VOCs), but also allows for faster production speeds and lower costs. Also, their properties could be relatively easily modified to meet different application requirements. Last but not least, they are clean and easy to handle.3
Currently, almost all the base/major polymers for HMAs on the market are primarily derived from petroleum resources, such as ethylene vinyl acetate (EVA), block copolymers of styrene and butadiene (SBS) or isoprene (SIS), polyesters, polyamides, polyurethanes and polyolefins. To this, a variety of tackifiers, plasticizers, waxes, and antioxidants are incorporated to meet special application requirements.3,4 However, such compositions are derived from depleting petroleum resources, and there are concerns over their degradation ability. Concerns of bio-degradation abilities are not only about the adhesive themselves, but also the substrates bonded with them, especially in the paper and pulp industry.3
To reduce the environmental impacts associated with substrate recycling and to overcome the shortcomings associated with traditional petroleum resource based HMAs and meet the global growing demand for HMAs, especially when over 6 billion pounds of adhesives (most derived from petroleum based feedstock) are consumed annually,5 considerable research has been done to develop natural product based HMAs, such as starch and its derivatives,6,7 (poly)lactic acid,8 soy protein isolate,9 and blends of some of these polymers.10 Among these, starch has attracted much attention due to its abundant and guaranteed supply, low cost, renewability and biodegradability. In an U.S. patent, Billmers et al. reported several HMA formulations comprising selected modified starch esters with ester component of about 2 to 18 carbons with DS varying from around 0.3 to 3.0.6 No work was reported on expanded starch or its derivatives.
However, natural starches are water/moisture unstable and mechanical properties of starches are poorer than those of synthetic polymers, something which hampers more widespread use of these materials in modern industry. Native starches are generally chemically and/or physically modified to overcome the limitations associated with starch and to improve its performance as an adhesive. Esterification of starch has been intensively studied and employed due to the large number of hydroxyl groups within starch molecules. However, access to these hydroxyl groups is significantly hindered due to the dense packing of polysaccharide chains within starch granules. Harsh pretreatments and chemical modification conditions are required to obtain desired starch derivatives. Expansion of starch has been proposed as an effective method to increase the accessibility of hydroxyl groups by increasing the surface area of native starch (<5 m2 g−1) to around 180 m2 g−1.11,12 After expansion of starch, chemical modification, including esterification could take place under relatively mild conditions. This is of pivotal importance, especially when mild, environmentally friendly process conditions are desired.
Herein, we report our preliminary research on the application of expanded starch and its propionates with various degrees of substitutions as the base/main polymer in 100% biodegradable HMA formulations. For esterification of expanded starch, the effects of amounts of esterifying reagent (propionic anhydride) and reaction time were investigated. The propionates were characterized by titration, Fourier transform infrared spectroscopy (FT-IR), thermogravimetric analysis (TGA), solid state 13C CPMAS and liquid 1H NMR spectroscopy. Properties of formulated HMAs were characterized with differential scanning calorimetry (DSC) and FT-IR. Tensile stresses of the HMA bonded aluminium plates were tested.
Propionic anhydride (g) | Propionic anhydride (mol) | Expanded HACSb (mol) | Reaction time (h) | DS |
---|---|---|---|---|
a For all the reactions, DMAP (0.4 g, 3.3 mmol) was added as catalyst.b Expanded HACS with surface area 176 m2 g−1 (10 g, 0.062 mol) was used as base polymer for esterification. | ||||
5 | 0.038 | 0.062 | 6 | 0.38 |
7.5 | 0.058 | 0.062 | 6 | 0.78 |
10 | 0.077 | 0.062 | 6 | 1.00 |
12.5 | 0.096 | 0.062 | 6 | 1.46 |
15 | 0.115 | 0.062 | 6 | 1.82 |
17.5 | 0.134 | 0.062 | 6 | 1.91 |
20 | 0.154 | 0.062 | 6 | 1.95 |
30 | 0.231 | 0.062 | 6 | 1.99 |
40 | 0.307 | 0.062 | 6 | 2.05 |
40 | 0.307 | 0.062 | 12 | 2.54 |
In this work, we prepared a series of starch propionates with various degree of substitution (DS) by changing the amount of esterifying reagent (propionic anhydride) and reaction time using 4-dimethylaminopyridine (DMAP) as catalyst. The reaction conditions and DS of yielded starch propionates are summarized in Table 1. For 6 h reactions, with increasing amounts of propionic anhydride, the DS of starch propionates significantly increased from around 0.38 (5 g, 0.038 mol, propionic anhydride) to 1.91 (17.5 g, 0.134 mol, propionic anhydride). Thereafter, the reaction equilibrium was reached, DS increased from around 1.91 (17.5 g, 0.134 mol, propionic anhydride) just to 2.05 (40 g, 0.307 mol, propionic anhydride). To further increase the DS, one more experiment was conducted with propionic anhydride (40 g, 0.307 mol) for 12 h. By doubling reaction time, DS increased from 2.05 (6 h) to 2.54 (12 h).
For reference, the esterification of non-expanded HACS was conducted with propionic anhydride (10 g, 0.077 mol) and DMAP (0.4 g, 3.3 mmol) for 6 h. The DS of resulted starch propionate is around 0.02, which is dramatically lower than that of the one obtained with expanded starch under the same reaction conditions (1.00).
Wavenumber (cm−1) | Assignment |
---|---|
3600–3000 | O–H stretching vibration |
2960–2850 | C–H vibrations |
1745 | C![]() |
1648 | Tightly bound water |
1456 | CH3 asymmetric bending vibration |
1360 | CH deformation vibration |
1152 | Ester C–O–C asymmetric stretching |
1079, 1013 | C–O vibration (anhydroglucose ring) |
929, 763 | Anhydroglucose ring stretching vibration |
In the spectrum of expanded HACS, some characteristic absorption bands for starch could be identified, such as bands centred at 1079 cm−1, 1013 cm−1 which are assigned to C–O bond stretching.15,16 Also, there are several additional characteristic absorption bands due to the entire anhydroglucose ring stretching vibrations, such as bands at 929 cm−1 and 763 cm−1.15 All these bands also exist in the spectra of starch propionates.
Decomposition of expanded HACS starts at approximately 260 °C and is a one step process with peak decomposition temperature (dTG peak) at 310 °C. It is noteworthy that there is a clear shift towards higher decomposition temperatures with increasing of DS. For instance, the major peak decomposition temperature of starch propionate with DS 2.54 (376 °C) is much higher than that of expanded HACS, indicating the thermal stability increased with DS. With the increasing of DS, more hydroxyl groups on anhydroglucose units were converted to ester groups. As the thermal decomposition of starch is primarily due to inter- and/or intra-molecular dehydration reactions with water as a main product, the dehydration reactions became increasingly difficult and slow with increasing of DS.17,18 This effect finally results in higher thermal stabilities of the derived starch propionates.
Unlike expanded HACS, thermal decomposition of starch propionates mainly consists of two steps. From the dTG traces (Fig. 3), it is obvious that the 1st and 2nd decomposition step of starch propionates show almost the same peak decomposition temperatures: around 321 °C for the 1st step and 376 °C for the 2nd decomposition step. Also, from the TG traces (Fig. 2), with increasing of DS, mass loss in the 1st decomposition step decreased from approximately 60% (DS, 0.38) to 3.6% (DS, 2.54). On the contrary, mass loss in the 2nd decomposition step increased from around 20% (DS, 0.38) to 82% (DS, 2.54). This phenomenon probably indicates that inter- or intra-molecular dehydration reactions primarily occur during the 1st decomposition step. As the amounts of available hydroxyl groups reduce with increasing DS, mass loss of the 1st decomposition step decreases, while that of the 2nd decomposition step increases. For both expanded HACS and its propionates, approximately 15 ± 5 wt% remains after heating to 600 °C.
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Fig. 4 Solid-state 13C CPMAS NMR spectra of (A) expanded HACS and (B) starch propionate (DS, 1.00). The repeating unit shown in B is with the ester group connected to the most probable C position (C-6).18 |
The 1H NMR spectra of expanded HACS and starch propionates with DS (0.38, 1.46, 1.99 and 2.54) in DMSO-d6 are illustrated in Fig. 5. The broad, strong signals ranging from 3.2 to 4.0 ppm are assigned to starch chain protons (H-2, 3, 4, 5, 6), but is mainly attributed to residual water (centred at 3.30 ppm), because of the hygroscopic nature of starch and DMSO-d6.22
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Fig. 5 1H NMR spectra of expanded HACS and starch propionates (DS: 0.38, 1.46, 1.99 and 2.54) in DMSO-d6. * Possible artefact. |
According to Chi et al., we assigned the resonance signals of the three hydroxyl groups on C-2, 3, 6 (OH-2, 3, 6) at 5.40, 5.50 and 4.59 ppm, respectively.15 Also, resonance signal of the anomeric hydrogen atom (H-1), which corresponding to the internal α-1,4 linkages, is observed at 5.10 ppm.15,22
During the esterification process, the propionate moieties are gradually introduced into starch molecules. From the spectra of starch propionates, the characteristic resonance bands of anhydroglucose units are still visible, even though the resolution of spectra decreased with increasing of the DS, which is probably due to the subsequent increased viscosity of the NMR solution. However, subtle changes of the resonance of protons on anhydroglucose units can be observed compared with that of expanded HACS, which is resulted from slightly changed chemical environments.
With increasing DS, it is obvious that the resonance bands of OH-2, 3, 6 (centred at 5.40, 5.50, 4.59 ppm) gradually diminish, referenced to the intensity of the anomeric hydrogen (H-1) band at 5.10 ppm. In all the spectra of starch propionates, the resonance signals for CH2 and CH3 groups of propionate moieties are found between 2.0 to 2.45 ppm and 0.6 to 1.3 ppm, respectively.
Fig. 6 and 7 shows the 2nd heating and cooling traces of expanded HACS and its propionates with DS of 0.38, 1.00, 1.82 and 2.54 based HMA formulations, respectively. The glass transition of the HMAs (approximately between −5 °C to 5 °C) is observed in both heating and cooling traces. From the heating traces shown in Fig. 6, slightly endothermic transitions of the HMAs could be observed around 115 °C; however, a significant large endothermic peak is shown between 135 °C to 175 °C for all the traces, corresponding to the major melting of HMA formulations. From the cooling traces (Fig. 7), all the samples show an exothermic crystallization peak between 130 °C to 90 °C. All these transitions are characteristics for HMA formulations. As the major endothermic melting transition for all the HMA formulations ends around 175 °C, a higher temperature (190 °C) is chosen for the application of such HMAs during the adhesion experiments.
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Fig. 6 DSC traces of the 2nd heating run of expanded HACS and starch propionates (DS: 0.38; 1.00; 1.82; 2.54) based HMAs. |
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Fig. 7 DSC traces of the 2nd cooling run of expanded HACS and starch propionates (DS: 0.38; 1.00; 1.82; 2.54) based HMAs. |
In order to study the stability/reusability of the expanded HACS and its propionates based HMA formulations, the starch propionate (DS, 1.00) based HMA was characterized in DSC for more heat–cool cycles using the same method stated in the Experimental section. The traces are shown in Fig. 8. Even though the peak temperatures of melting and crystallization shift slightly due to changes of the environment within sealed Tzero aluminium pans, characteristics of glass transitions, melting and crystallization transitions basically remain even after 5 heat–cool cycles, indicating high stability of the formulated HMAs.
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Fig. 8 DSC traces of the 2nd to 5th heat–cool cycle of starch propionate (DS, 1.00) based HMA formulation. |
Stability of formulated HMAs was further proved by comparing the FT-IR spectra of the base material, formulated HMA before and after DSC measurement. Fig. 9 shows the FT-IR spectra of expanded HACS, and expanded HACS based HMA before and after DSC measurement (Fig. 9A) and that of starch propionate (DS, 1.82), starch propionate (DS, 1.82) based HMA before and after DSC measurement (Fig. 9B). It is obvious that all the characteristic absorption bands of both expanded HACS and its propionate based HMA formulations are still remaining almost the same before and after heating and cooling in DSC, suggesting no thermal degradation and any non-reversible reactions occurred during heating and cooling.
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Fig. 10 A typical failure pattern of formulated HMA bonded Al plates (sample shown is expanded HACS based HMA cured Al plates). |
The measured tensile strengths were normalized to effective tensile stress by calculating the surface area of effective bonding area (circled by red lines, Fig. 10). Normalized tensile stress of the HMA formulations with error bars are shown in Fig. 11. The reported values are average values of four specimens adhered with each kind of HMA formulation (50 mg).
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Fig. 11 Normalized tensile stress of non-expanded HACS, expanded HACS and its starch propionates based HMA formulations (50 mg) bonded Al plates. |
It is significant that the tensile stress of expanded HACS based HMA (2.0 MPa) is dramatically higher than that of HMA based on non-expanded HACS (1.1 MPa). This effect might result from the significant increased surface area of expanded HACS and subsequent improved accessibility of hydroxyl groups within starch molecule. This effect probably leads to higher extent of interaction (non-covalent or cross-linking) between starch, glycerol and PVOH, resulting in significant increase of tensile stress. For the starch propionates based HMA formulations, tensile stress decreased with increasing of DS. When DS increased from 0.38 to 2.54, the tensile stress of the starch propionate based HMAs dropped from 1.6 MPa to 0.6 MPa. As more and more hydroxyl groups were converted to ester groups during esterification, the amounts of available “free” hydroxyl groups decreased. As a result, the crosslinking effect between the three HMA components deteriorated, leading to decreased tensile stress. Also, as hydrophobicity of starch propionates increases with DS, starch propionates with higher DS might sacrifice their abilities to be compatible with glycerol and PVOH, which will also leads to decreased tensile stress. However, tensile stress of starch propionates (DS < 1.5) based HMA formulations are still higher than that of non-expanded HACS based HMA formulation, despite lower than that of the one based on expanded HACS.
For reference, the tensile stress of commercial ethylene vinyl acetate (EVA) based LOCTITE hot melt glue (around 6 MPa, purchased from B&Q, York, UK) was tested under the same conditions. Due to the nature of our HMA formulations and the fact that they were not engineered, the maximum tensile stress of our HMAs is around 2.3 MPa obtained with expanded HACS based HMA. However, within this work we demonstrated the great potential of application of expanded starch in HMA formulations, which to our knowledge, has never been reported previously.
Thus obtained expanded HACS and starch propionates were incorporated into 100% biodegradable HMA formulations by mixing them with glycerol and PVOH at the same weight ratio. The developed HMA formulations were characterized by Differential Scanning Calorimetry (DSC) using a heat–cool–heat–cool method. The glass transition generally occurs between −5 °C to 5 °C and the major melting step occurs between 135 °C to 175 °C. During cooling, the HMAs recrystallized between 130 °C to 90 °C.
The adhesion properties of HMAs were studied by applying each HMA formulation (50 mg) in the middle of two Al plates (surface area: 50 mm × 50 mm), and specimens were adhered in a hot press machine for 30 seconds at 190 °C. Tensile stress of the Al–HMA–Al bond was normalized. The tensile stress of expanded HACS based HMA (2.0 MPa) is dramatically higher than that of the one based on non-expanded HACS (1.1 MPa). For those based on starch propionates, tensile stress decreases with increasing of DS of the base polymer. However, tensile stresses of starch propionates (DS < 1.5) based HMAs are still higher than that of the one based on non-expanded HACS, even though lower than that of expanded HACS based HMA.
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