Co (III) acetylacetonate complex in aqueous medium. *Cellulose*, Vol. 8, No. 3,

conversion of alkali cellulose to fine carboxymethyl cellulose at mild conditions. *World Applied Science Journal,* Vol. 6, No. 4, (2009 ), pp 564-569, ISSN 1818-4952. Jia, Z.,Yong, Y., (2006); Surface Modification of Poly Acrylic Fibers (PAC) via Grafting of

Soybean Protein Isolates (SPI). *Iranian Polymer Journal*, Vol. 15, No. 10, (October

carboxymethyl chitosan using CAN as an initiator. *Polymer,* Vol*.* 47, No. 6, (March

cellulose grafting poly (acrylic acid) copolymers and their self-assembly morphologies in water. *Polymer,* Vol. 47, No. 23, (October 2006), pp 7927-7934, ISSN

*cellulose chemistry volume 2,*Wiley-VCH, ISBN 3-527-29489-9, Weinheim, Federal

Preparation of Feather Keratin Hydrolyzate‐Gelatin Composites and Their Graft Copolymers. *Journal of Macromolecular Science Part A: Pure and Applied Chemistry,*

modification of keratin biofibres by graft polymerisation of methyl methacrylate using redox initiation. *Materials Research Innovations,* Vol. 12, No. 4, (December

Microstructural characterization of keratin fibers from chicken feathers. *International Journal Environmental and Pollution,* Vol. 23, No. 2, (MES 2005), pp 162-

of Methyl methacrylate onto natural keratin. *e-polymers,* No. 016, (April 2003), pp 1-

and its application in textiles. *Carbohydrate Polymers,* 75, 1, (January 2009), pp 71-78,

*Polymer Degradation and Stability,* (1995), Vol. 50, No. 2, (March 1995), pp 189-194,

Shaikhutdinov, Lee, S.Ch., Park, K., (2008), Studies on graft copolymerization of 2 hydroxyethyl acrylate onto chitosan. *Reactive and Functional Polymers,* Vol. 68, No. 1,

## **4. Concluding remarks**

From results presented in this research work it can be conclude that is possible graft HEMA onto CFF and CMC using different initiator system, and that grafting yield obtain on depends of kind of initiator system, being higher with CAN initiator system than KMnO4 malic acid. SEM microgrpah give evidence that the grafting reaction takes place on CFF and CMC surface until a saturation of active sites, and then homopolymerization happens.

One of the most common applications of IR spectroscopy is to the identification of organic compounds. In polymers, may be used to identify the composition, to monitor polymerization process, to characterize polymer structure. In present research, IR spectroscopy showed to be a usefull toll to evaluate if the graft reaction takes place. It was possible identify main functional groups of CFF and CMC ungrafted, and PHEMA. The IR spectra of grafted copolymers presented assignments due to ungrafted materials and PHEMA giving evidence that the graft reaction carried out. Futhermore, it was possible evaluate the changes in peaks of the grafted materials according with grafting yield, increasing signals attributed to PHEMA.

## **5. Acknowledgment**

The financial support from Dirección General de Educación Superior Tecnológica (DGEST) from Public Education Secretary (SEP) through projects 3616.10-P and 2203-09-P for development of this research work is gratefully acknowledged. The authors would like to thank to Pollos Villafranca for provide chicken feathers, and the micrography department of CFATA of Universidad Nacional Autónoma de México campus Juriquilla, especially to Alicia Del Real López for technical assistance.

## **6. References**

From results presented in this research work it can be conclude that is possible graft HEMA onto CFF and CMC using different initiator system, and that grafting yield obtain on depends of kind of initiator system, being higher with CAN initiator system than KMnO4 malic acid. SEM microgrpah give evidence that the grafting reaction takes place on CFF and CMC surface until a saturation of active sites, and then homopolymerization happens.

One of the most common applications of IR spectroscopy is to the identification of organic compounds. In polymers, may be used to identify the composition, to monitor polymerization process, to characterize polymer structure. In present research, IR spectroscopy showed to be a usefull toll to evaluate if the graft reaction takes place. It was possible identify main functional groups of CFF and CMC ungrafted, and PHEMA. The IR spectra of grafted copolymers presented assignments due to ungrafted materials and PHEMA giving evidence that the graft reaction carried out. Futhermore, it was possible evaluate the changes in peaks of the grafted materials according with grafting yield,

The financial support from Dirección General de Educación Superior Tecnológica (DGEST) from Public Education Secretary (SEP) through projects 3616.10-P and 2203-09-P for development of this research work is gratefully acknowledged. The authors would like to thank to Pollos Villafranca for provide chicken feathers, and the micrography department of CFATA of Universidad Nacional Autónoma de México campus Juriquilla, especially to

Athawale, V.D., Rathi, S.C., (1997), Effect of chain length of the alkyl group of alkyl

Barone, J.R., Schmidt, W.F., Liebner, C.F., (2005). Thermally processed keratin films. *Journal*

Bickford, M., (2008). *Characterization and Analysis of Polymers.* John Wiley and Sons. ISBN

Bono, A., Ying, P.H., Yan, F.Y., Muei, C.L., Sarbatly, R., Krishnaiah, (2009), Synthesis and

Elizalde Peña, E., Flores Ramírez, N., Luna Barcenas, G., Vásquez García, S. R., Arámbula

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*of Applied Polymer Science*, Vol. 97, No. 4, (august 2005), pp 1644-1651, ISSN 1097-

Characterization of Carboxymethyl Cellulose from Palm Kernel Cake. *Advances in Natural and Applied Sciences,* Vol. 3, No. 2, (January 2009), pp 5-11, ISSN 1995-0772. Cao, Y., Qing, X., Sun, J., Zhou, F., Lin, S., (2002), Graft copolymerization of acrylamide onto

carboxymethyl starch. *European Polymer Journal,* vol. 38, No. 9, (September 2002), pp

Villa, G., Garcia Gaitan, B., Rutiaga-Quiñones, J.G., González-Hernández, J. (2007). Syntesis and characterization of chitosan-g-glycidyl methacrylate with methyl

**4. Concluding remarks**

increasing signals attributed to PHEMA.

Alicia Del Real López for technical assistance.

1921-1924, ISSN 0014-3057.

**5. Acknowledgment**

**6. References**

0014-3057.

4628.

methacrylate. *European Polymer Journal*, Vol. 43, No. 9, (September 2007) pp 3963- 3969, ISSN 0014-3057.

**13**

*Spain*

*University Carlos III of Madrid*

**Applications of FTIR on Epoxy Resins –**

**Process, Phase Separation and Water Uptake**

Epoxy resins are a family of thermosetting materials widely used as adhesives, coatings and matrices in polymer composites because of the low viscosity of the formulations, good insulating properties of the final material even at high temperatures and good chemical and thermal resistance (May, 1988). Epoxy thermosets can be described as 3D polymer networks formed by the chemical reaction between monomers (*"curing"*). This 3D covalent network structure determines the properties of thermosetting polymers: unlike thermoplastics, this kind of polymers does not melt, and once the network has been formed the material cannot be reprocessed. Maybe one of the main advantages of epoxy thermosets is that the starting monomers have low viscosity so that complex geometries can be easily shaped and fixed after curing the monomers. Thus the formation of the network via chemical reaction is a key

Epoxy formulations usually include more than one component, although there are different crosslinking mechanisms involving either chemical reaction between one single type of monomer (homopolymerization) or two kinds of monomers with different functional groups. In both cases, a common constituent is always found: the epoxy monomer. The main feature of the epoxy monomer is the oxirane functional group, which is a three member ring formed between two carbon atoms and an oxygen, as shown in Figure 1. This atomic arrangement shows enhanced reactivity when compared with common ethers because of its high strain. Due to the different electronegativity of carbon and oxygen, the carbon atoms of the ring are electrophilic. Thus epoxies can undergo ring opening reactions towards nucleophiles. The polarity of the oxirane ring makes possible detection by IR

There are mainly two families of epoxies: the glycidyl epoxies and non-glycidyl epoxies (also called aliphatic or cycloaliphatic epoxy resins). The absence of aromatic rings in aliphatic epoxies makes them UV resistant and suitable for outdoor applications and also reduces viscosity. The most common epoxy monomers of each family are diglycidylether of bisphenol A (known as DGEBA) and 3,4-Epoxycyclohexyl-3'4'-epoxycyclohexane carboxylate (ECC) respectively and their structures are given in Figure 2 (a, b). Cycloaliphatic resins are usually found in the form of pure chemicals with a definite

**1. Introduction**

spectroscopy.

aspect in this kind of materials.

María González González, Juan Carlos Cabanelas and Juan Baselga

**Identification, Monitoring the Curing**

## **Applications of FTIR on Epoxy Resins – Identification, Monitoring the Curing Process, Phase Separation and Water Uptake**

María González González, Juan Carlos Cabanelas and Juan Baselga *University Carlos III of Madrid Spain*

## **1. Introduction**

260 Infrared Spectroscopy – Materials Science, Engineering and Technology

Okieimen, F.E., Ogbeifun, D.E., (1996), Graft copolymerization of modified cellulose:

Prachayawarakorn, J., Boonsawat, K., (2007), Physical, chemical and dyeing properties of

Schmidt, W.F., (1998), Innovative feather utilization strategies. *Proceedings of National Poultry Waste Management conference,* pp 276-282, Springdale, Ar., October 19-22, 1998. Vasile, C., Bumbu, G.G., Dumitriu, R.P., Staikos, G., (2004), Comparative study of the

Xu, X. Zhou, Z., Prum, R.O., (2001), Branched integumental structures in Sinornithosaurus

Xu, X., Zhou, Z., Wong, X., Kuang, X. Zhang, F., Du, X., (2003), Four-winged dinosaurs from China. *Nature,* Vol. 421, No. 6921, pp 335-340, (January 2003), ISSN 0028-0836. Zampano, G., Bertoldo, M., Bronco, S., (2009) Poly(ethyl acrylate) surface-initiated ATRP

Zohuriaan-Mehr, J.M., Pourjavadi, A., Sadeghi, M., (2005), Modified CMC: Part1-Optimized

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(September 2006), pp 2960-2966, ISSN 1097-4628.

2004) pp 1209-1215, ISSN 0014-3057.

(January 2009), pp 22-31, ISSN 0008-6215.

0014-3057.

ISSN 0028-0836.

grafting of methyl acrylate, ethyl acrylate and ethyl methacrylate on carboxymethyl cellulose. *European Polymer Journal,* Vol. 32, No. 3, (March 1996), pp 311-315, ISSN

bomboyxmori silks grafted by 2-hydroxyethyl methacrylate. *Journal of Applied Polymer Science,* Vol. 106, No. 3., (November 2007), pp 1526-1534, ISSN 1097-4628. Radhakumary, C., Nair, P. D., Mathew, S., Nair, C.P., (2006), HEMA-Grafted Chitosan for

Dialysis Membrane Applications. *Journal of Applied Polymer Science,*Vol. 101, No 5,

behavior of carboxymethyl cellulose-g-poly(N-isopropylacrylamide) copolymers and their equivalent physical blends. *European polymer Journal,* Vol. 40, No. 6, (June

and the origin of feathers. *Nature,* Vol. 410, No. 6825, pp 200-204, (March 2001),

grafting from Wood pulp cellulose fibers. *Carbohydrate Polymers*, Vol. 75, No. 1,

Synthesis of Carboxymethyl cellulose-g-Polyacrylonitrile. *Iranian Polymer Journal,*

Epoxy resins are a family of thermosetting materials widely used as adhesives, coatings and matrices in polymer composites because of the low viscosity of the formulations, good insulating properties of the final material even at high temperatures and good chemical and thermal resistance (May, 1988). Epoxy thermosets can be described as 3D polymer networks formed by the chemical reaction between monomers (*"curing"*). This 3D covalent network structure determines the properties of thermosetting polymers: unlike thermoplastics, this kind of polymers does not melt, and once the network has been formed the material cannot be reprocessed. Maybe one of the main advantages of epoxy thermosets is that the starting monomers have low viscosity so that complex geometries can be easily shaped and fixed after curing the monomers. Thus the formation of the network via chemical reaction is a key aspect in this kind of materials.

Epoxy formulations usually include more than one component, although there are different crosslinking mechanisms involving either chemical reaction between one single type of monomer (homopolymerization) or two kinds of monomers with different functional groups. In both cases, a common constituent is always found: the epoxy monomer. The main feature of the epoxy monomer is the oxirane functional group, which is a three member ring formed between two carbon atoms and an oxygen, as shown in Figure 1. This atomic arrangement shows enhanced reactivity when compared with common ethers because of its high strain. Due to the different electronegativity of carbon and oxygen, the carbon atoms of the ring are electrophilic. Thus epoxies can undergo ring opening reactions towards nucleophiles. The polarity of the oxirane ring makes possible detection by IR spectroscopy.

There are mainly two families of epoxies: the glycidyl epoxies and non-glycidyl epoxies (also called aliphatic or cycloaliphatic epoxy resins). The absence of aromatic rings in aliphatic epoxies makes them UV resistant and suitable for outdoor applications and also reduces viscosity. The most common epoxy monomers of each family are diglycidylether of bisphenol A (known as DGEBA) and 3,4-Epoxycyclohexyl-3'4'-epoxycyclohexane carboxylate (ECC) respectively and their structures are given in Figure 2 (a, b). Cycloaliphatic resins are usually found in the form of pure chemicals with a definite

Applications of FTIR on Epoxy Resins –

Neckers. 2001; Yagci & Reetz, 1998).

Identification, Monitoring the Curing Process, Phase Separation and Water Uptake 263

Wang et al., 2003) or homopolymerized via a cationic mechanism induced by UV radiation (Crivello, 1995; Crivello & Fan,1991; Crivello & Liu, 2000; Hartwig et al., 2003; Wang &

The chemical reactivity of the epoxies enables using a wide variety of molecules as curing agents depending on the process and required properties. The commonly used curing agents for epoxies include amines, polyamines, polyamides, phenolic resins, anhydrides, isocyanates and polymercaptans. The choice of both the resin and the hardener depends on the application, the process selected, and the properties desired. It is worthy to note that the reaction mechanism, the curing kinetics and the glass transition temperature (Tg) of the final material are also dependent on the molecular structure of the hardener. As it has been previously mentioned, amines are the best performance curing agents for diglycidylethertype epoxies. Aliphatic diamines like m-xylylenediamine or 1,2-trans-cyclohexyldiamine can be used for curing from room to moderate temperatures (Paz-Abuin, 1997a, 1997b, 1998), although the glass transition temperature of the material is also moderate. For high Tg materials aromatic amines, like 4,4´- methylen- bis (3- chloro- 2,6- diethylaniline) or 4,4´ diaminodiphenyl sulphone (Blanco et al., 2004; Girard-Reydet et al., 1999; Marieta et al.,

2003; Siddhamalli, 2000a) are used, although high curing temperatures are needed.

The curing process is the set of chemical reactions that leads to the formation of a highly crosslinked 3D network. For epoxy/amine the chemical process that leads to network

Fig. 3. Epoxy-amine reaction scheme. k1 and k2 correspond to the non catalyzed kinetic constants for the addition of primary and secondary amines respectively. k'1 and k'2

The reaction between monomers leads to the formation of the network and there are two important points during this process: gelation and vitrification. During the first stage the primary amino groups transform sequentially in secondary and tertiary amino groups. If R1 and R2 blocks contain a second reactive group (oxirane and amino, respectively), addition of more molecules proceeds at the ends of the branched molecule as well as with fresh monomers. Therefore, during the chemical reaction, both molecular weight and polydispersity increase until one single macromolecule is formed. At this point, if temperature is high enough, the behavior of the system changes irreversibly from liquid-like to rubber-like: the reactive system becomes a gel. According to the Flory-Stockmayer's theory of gelation (Flory, 1953) the extent of reaction at this point can be determined using

**1.1 Curing process. Gelation and vitrification. Conversion degree**

formation can be described according to the scheme:

correspond to the catalyzed processes.

the expression:

Fig. 1. Oxirane ring

Fig. 2. Chemical structures of common epoxy resins: a) 2,2-Bis[4-(glycidyloxy)phenyl] propane (DGEBA); b) 3,4-Epoxycyclohexylmethyl-3,4-epoxycyclohexane carboxylate (ECC); c) DGEBA oligomer, n = 0.2 typically.

molecular mass. But DGEBA-based resins are synthesized via the addition of epichlorohydrine and bisphenol A so oligomers with a relatively narrow distribution of polymerization degrees are obtained instead; their chemical structure is presented in Figure 2 (c) where *n* is typically 0.2. DGEBA oligomers typically contain a certain amount of hydroxyl groups, that play an important catalytic role in the kinetics of the curing process, providing a higher viscosity which is dependent on *n*. In addition, all of them have at least two oxirane functional groups, so they can finally lead to the 3D network. The nature and functionality of the epoxy monomer will determine its reactivity as well as the properties and performance of the final material.

Despite of having the same main functional group, the reactivity of both families of epoxies is completely different as a consequence of the structure of the molecules. It is worthy to note that the linkage between the aromatic ring and the oxygen (ether) in DGEBA has a strong electron-withdrawing effect that makes the oxirane group highly reactive towards nucleophilic compounds (like amines), unlike the cyclohexyl group in aliphatic epoxies which is reactive towards Lewis acids like anhydrides (Mark, 2004). Additionally, a protecting effect of axial and equatorial protons of the cyclohexyl ring against nucleophilic attack has been proposed as an explanation of the characteristic low reactivity of the oxirane ring in these aliphatic epoxies (Soucek et al., 1998). This way, the best performance and the highest crosslinking degree for DGEBA-based resins is achieved when cured via an addition mechanism with diamines (either aliphatic or aromatic), whilst cycloaliphatic epoxies are commonly cured with anhydrides (Barabanova et al., 2008; Chen et al., 2002; Tao et al., 2007;

Fig. 2. Chemical structures of common epoxy resins: a) 2,2-Bis[4-(glycidyloxy)phenyl] propane (DGEBA); b) 3,4-Epoxycyclohexylmethyl-3,4-epoxycyclohexane carboxylate (ECC);

molecular mass. But DGEBA-based resins are synthesized via the addition of epichlorohydrine and bisphenol A so oligomers with a relatively narrow distribution of polymerization degrees are obtained instead; their chemical structure is presented in Figure 2 (c) where *n* is typically 0.2. DGEBA oligomers typically contain a certain amount of hydroxyl groups, that play an important catalytic role in the kinetics of the curing process, providing a higher viscosity which is dependent on *n*. In addition, all of them have at least two oxirane functional groups, so they can finally lead to the 3D network. The nature and functionality of the epoxy monomer will determine its reactivity as well as the properties

Despite of having the same main functional group, the reactivity of both families of epoxies is completely different as a consequence of the structure of the molecules. It is worthy to note that the linkage between the aromatic ring and the oxygen (ether) in DGEBA has a strong electron-withdrawing effect that makes the oxirane group highly reactive towards nucleophilic compounds (like amines), unlike the cyclohexyl group in aliphatic epoxies which is reactive towards Lewis acids like anhydrides (Mark, 2004). Additionally, a protecting effect of axial and equatorial protons of the cyclohexyl ring against nucleophilic attack has been proposed as an explanation of the characteristic low reactivity of the oxirane ring in these aliphatic epoxies (Soucek et al., 1998). This way, the best performance and the highest crosslinking degree for DGEBA-based resins is achieved when cured via an addition mechanism with diamines (either aliphatic or aromatic), whilst cycloaliphatic epoxies are commonly cured with anhydrides (Barabanova et al., 2008; Chen et al., 2002; Tao et al., 2007;

Fig. 1. Oxirane ring

c) DGEBA oligomer, n = 0.2 typically.

and performance of the final material.

Wang et al., 2003) or homopolymerized via a cationic mechanism induced by UV radiation (Crivello, 1995; Crivello & Fan,1991; Crivello & Liu, 2000; Hartwig et al., 2003; Wang & Neckers. 2001; Yagci & Reetz, 1998).

The chemical reactivity of the epoxies enables using a wide variety of molecules as curing agents depending on the process and required properties. The commonly used curing agents for epoxies include amines, polyamines, polyamides, phenolic resins, anhydrides, isocyanates and polymercaptans. The choice of both the resin and the hardener depends on the application, the process selected, and the properties desired. It is worthy to note that the reaction mechanism, the curing kinetics and the glass transition temperature (Tg) of the final material are also dependent on the molecular structure of the hardener. As it has been previously mentioned, amines are the best performance curing agents for diglycidylethertype epoxies. Aliphatic diamines like m-xylylenediamine or 1,2-trans-cyclohexyldiamine can be used for curing from room to moderate temperatures (Paz-Abuin, 1997a, 1997b, 1998), although the glass transition temperature of the material is also moderate. For high Tg materials aromatic amines, like 4,4´- methylen- bis (3- chloro- 2,6- diethylaniline) or 4,4´ diaminodiphenyl sulphone (Blanco et al., 2004; Girard-Reydet et al., 1999; Marieta et al., 2003; Siddhamalli, 2000a) are used, although high curing temperatures are needed.

#### **1.1 Curing process. Gelation and vitrification. Conversion degree**

The curing process is the set of chemical reactions that leads to the formation of a highly crosslinked 3D network. For epoxy/amine the chemical process that leads to network formation can be described according to the scheme:

Fig. 3. Epoxy-amine reaction scheme. k1 and k2 correspond to the non catalyzed kinetic constants for the addition of primary and secondary amines respectively. k'1 and k'2 correspond to the catalyzed processes.

The reaction between monomers leads to the formation of the network and there are two important points during this process: gelation and vitrification. During the first stage the primary amino groups transform sequentially in secondary and tertiary amino groups. If R1 and R2 blocks contain a second reactive group (oxirane and amino, respectively), addition of more molecules proceeds at the ends of the branched molecule as well as with fresh monomers. Therefore, during the chemical reaction, both molecular weight and polydispersity increase until one single macromolecule is formed. At this point, if temperature is high enough, the behavior of the system changes irreversibly from liquid-like to rubber-like: the reactive system becomes a gel. According to the Flory-Stockmayer's theory of gelation (Flory, 1953) the extent of reaction at this point can be determined using the expression:

Applications of FTIR on Epoxy Resins –

therefore heterogeneous.

1996; Rajagopalan et al., 2000).

**2. Epoxy resins and FTIR**

in this region:

characterize the growth of the nascent structures.

Identification, Monitoring the Curing Process, Phase Separation and Water Uptake 265

Morphology development in modified thermosets takes place essentially between the "cloud point" conversion (beginning of the phase separation) and the gel point conversion (Bucknall & Partridge, 1986; Inoue, 1995; Mezzenga et al., 2000a), although it keeps evolving up to the vitrification of the system. Thermodynamics is the driving force for RIPS, but diffusion kinetics between phases is the controlling factor from the gel point on (Kiefer et al.,

As a consequence of phase separation particles or domains of very small size and different refraction index appear. When they are big enough they become light scatterers and the mixture becomes cloudy in the visible range. But the size of domains plays with the wavelenght, so IR radiation can also be used to determine the onset of phase separation and

For in-situ monitoring processes such as curing, phase separation or even ageing, the

Mid infrared spectroscopy has been widely used for characterization of organic compounds and plenty of reliable information and spectra libraries can easily be found. Both qualitative and quantitative information can be obtained by this technique, although its use in epoxy systems is quite restricted because of the location and intensity of the oxirane ring absorptions. Two characteristic absorptions of the oxirane ring are observed in the range between 4000 cm-1 and 400 cm-1. The first one, at 915 cm-1, is attributed to the C-O deformation of the oxirane group, although some works done by Dannenberg (Dannenberg & Harp, 1956) showed that this band does not correspond exclusively to this deformation but also to some other unknown process. The second band is located at 3050 cm-1 approximately and is attributed to the C-H tension of the methylene group of the epoxy ring. This band is not very useful since its intensity is low and it is also very close to the strong O-H absorptions; but in low polymerization degree epoxy monomers it can be used

Near IR is far more useful for epoxies. nIR spectrum covers the overtones of the strong vibrations in mIR and combination bands. In this range, fewer and less overlapped bands are observed so it has been used by several authors (Mijovic & Andjelic, 1995; Poisson et al., 1996; Xu & Schlup, 1998) for monitoring the curing reaction. The intensity of the bands in this region is much lower than in the mid range, allowing the use of thicker and undiluted samples to get good quality data. There are two absorptions related with the oxirane group

a. 4530 cm-1: It corresponds to a combination band of the second overtone of the epoxy ring stretching with the fundamental C-H stretching at 2725 cm-1 (Chicke et al., 1993).

system. Segregation generates the final two-phase morphology.

interpretation of the spectra and the assignment of the bands are critical.

as a qualitative indicative of the presence of epoxy groups.

$$\alpha\_{\text{gel}} \cdot \mathcal{J}\_{\text{gel}} = \frac{1}{(f\_c - 1)(f\_a - 1)}$$

Where *gel* and *gel* are epoxy and amine conversions at the gel point and *fe* and *fa* are the functionality of the epoxy and amine components respectively (*fe* = 2 and *fa* = 4 typically, so under stoichiometric conditions, gel point appears at *ge l = gel* = 0.57) . Gelation usually has no effect on the curing kinetics.

Common diamines with relatively small molecular volume act as crosslinking points of the 3D network (since each diamine has four active hydrogen atoms, they can be visualized as points in space from which four chains emerge, each of them connecting other points of the network). As the reaction proceeds, along with molecular weight, the crosslinking degree of the system increases, and so the viscosity and the glass transition temperature (Tg). In those processes in which curing temperature is not very high, Tg of the reacting mixture may reach the curing temperature value; then, molecular mobility becomes severely restricted so diffusion of reactants controls the kinetics and the reaction rate decreases dramatically. At this point, the reaction becomes almost stopped and the properties of the material (at room temperature) depend on the extent of the reaction achieved. Unlike gelation, vitrification is a reversible process, so when heating above Tg the reaction is reactivated and higher conversions are attained. Postcuring processes, which are designed to allow volume and internal stresses relaxation, make use also of this chemical reactivation and have deep effects on the mechanical performance of these systems.

The extent of reaction is very commonly determined by differential scanning calorimetry (DSC) as the ratio between the heat released by the reaction at each moment and the total heat released. Although this procedure is useful, accuracy at high conversions is low and problems arise when monitoring fast reactions. Additionally, DSC only provides an overall conversion degree being impossible to independently determine epoxy and amine conversions. On the contrary, infrared spectroscopy allows a very accurate determination of both conversions by band integration of the corresponding IR signals (epoxy and amino) being low the integration error and allowing more accurate values at high conversions. Considering the reaction mechanism, we can define the extent of reaction in terms of epoxy groups () and in terms of N-H bonds (β) from the areas of the oxirane ring and the N-H absorptions respectively:

$$
\alpha\_{\varepsilon} = \frac{A\_{\varepsilon}(0) - A\_{\varepsilon}(t)}{A\_{\varepsilon}(0)} \quad \beta\_{N-H} = \frac{A\_{N-H}(0) - A\_{N-H}(t)}{A\_{N-H}(0)} \tag{1}
$$

In equation (1) subscript "e" indicates epoxy, "N-H" amine, "0" initial and "t" indicates a certain reaction time. Although epoxy and amino groups have absorptions in the mid-range, more accurate results are obtained working in the near range

#### **1.2 Epoxy blends. Reaction induced phase separation**

The main drawback of epoxy thermosets is its brittleness. To solve this problem, they are commonly modified with reinforcements of different nature (elastomers, thermoplastics, inorganic particles), geometry (particles, fibers, platelets) and size (micro and nano) which provide additional mechanical energy absorption mechanisms. The dispersion of a second phase can be obtained using mainly two strategies (Pascault et al., 2002):

Morphology development in modified thermosets takes place essentially between the "cloud point" conversion (beginning of the phase separation) and the gel point conversion (Bucknall & Partridge, 1986; Inoue, 1995; Mezzenga et al., 2000a), although it keeps evolving up to the vitrification of the system. Thermodynamics is the driving force for RIPS, but diffusion kinetics between phases is the controlling factor from the gel point on (Kiefer et al., 1996; Rajagopalan et al., 2000).

As a consequence of phase separation particles or domains of very small size and different refraction index appear. When they are big enough they become light scatterers and the mixture becomes cloudy in the visible range. But the size of domains plays with the wavelenght, so IR radiation can also be used to determine the onset of phase separation and characterize the growth of the nascent structures.

## **2. Epoxy resins and FTIR**

264 Infrared Spectroscopy – Materials Science, Engineering and Technology

( )( ) 1 1 *gel gel e a f f*

functionality of the epoxy and amine components respectively (*fe* = 2 and *fa* = 4 typically, so

Common diamines with relatively small molecular volume act as crosslinking points of the 3D network (since each diamine has four active hydrogen atoms, they can be visualized as points in space from which four chains emerge, each of them connecting other points of the network). As the reaction proceeds, along with molecular weight, the crosslinking degree of the system increases, and so the viscosity and the glass transition temperature (Tg). In those processes in which curing temperature is not very high, Tg of the reacting mixture may reach the curing temperature value; then, molecular mobility becomes severely restricted so diffusion of reactants controls the kinetics and the reaction rate decreases dramatically. At this point, the reaction becomes almost stopped and the properties of the material (at room temperature) depend on the extent of the reaction achieved. Unlike gelation, vitrification is a reversible process, so when heating above Tg the reaction is reactivated and higher conversions are attained. Postcuring processes, which are designed to allow volume and internal stresses relaxation, make use also of this chemical reactivation and have deep effects

The extent of reaction is very commonly determined by differential scanning calorimetry (DSC) as the ratio between the heat released by the reaction at each moment and the total heat released. Although this procedure is useful, accuracy at high conversions is low and problems arise when monitoring fast reactions. Additionally, DSC only provides an overall conversion degree being impossible to independently determine epoxy and amine conversions. On the contrary, infrared spectroscopy allows a very accurate determination of both conversions by band integration of the corresponding IR signals (epoxy and amino) being low the integration error and allowing more accurate values at high conversions. Considering the reaction mechanism, we can define the extent of reaction in terms of epoxy groups () and in terms of

N-H bonds (β) from the areas of the oxirane ring and the N-H absorptions respectively:

0 0

*A A*

In equation (1) subscript "e" indicates epoxy, "N-H" amine, "0" initial and "t" indicates a certain reaction time. Although epoxy and amino groups have absorptions in the mid-range,

The main drawback of epoxy thermosets is its brittleness. To solve this problem, they are commonly modified with reinforcements of different nature (elastomers, thermoplastics, inorganic particles), geometry (particles, fibers, platelets) and size (micro and nano) which provide additional mechanical energy absorption mechanisms. The dispersion of a second

0 0 ( ) () ( ) () ( ) ( ) *e e NH NH <sup>e</sup> N H e N H A At A A t*

 (1)

under stoichiometric conditions, gel point appears at

on the mechanical performance of these systems.

more accurate results are obtained working in the near range

phase can be obtained using mainly two strategies (Pascault et al., 2002):

**1.2 Epoxy blends. Reaction induced phase separation**

Where

*gel* and

no effect on the curing kinetics.

1

*gel* are epoxy and amine conversions at the gel point and *fe* and *fa* are the

*ge l =*

*gel* = 0.57) . Gelation usually has

For in-situ monitoring processes such as curing, phase separation or even ageing, the interpretation of the spectra and the assignment of the bands are critical.

Mid infrared spectroscopy has been widely used for characterization of organic compounds and plenty of reliable information and spectra libraries can easily be found. Both qualitative and quantitative information can be obtained by this technique, although its use in epoxy systems is quite restricted because of the location and intensity of the oxirane ring absorptions. Two characteristic absorptions of the oxirane ring are observed in the range between 4000 cm-1 and 400 cm-1. The first one, at 915 cm-1, is attributed to the C-O deformation of the oxirane group, although some works done by Dannenberg (Dannenberg & Harp, 1956) showed that this band does not correspond exclusively to this deformation but also to some other unknown process. The second band is located at 3050 cm-1 approximately and is attributed to the C-H tension of the methylene group of the epoxy ring. This band is not very useful since its intensity is low and it is also very close to the strong O-H absorptions; but in low polymerization degree epoxy monomers it can be used as a qualitative indicative of the presence of epoxy groups.

Near IR is far more useful for epoxies. nIR spectrum covers the overtones of the strong vibrations in mIR and combination bands. In this range, fewer and less overlapped bands are observed so it has been used by several authors (Mijovic & Andjelic, 1995; Poisson et al., 1996; Xu & Schlup, 1998) for monitoring the curing reaction. The intensity of the bands in this region is much lower than in the mid range, allowing the use of thicker and undiluted samples to get good quality data. There are two absorptions related with the oxirane group in this region:

a. 4530 cm-1: It corresponds to a combination band of the second overtone of the epoxy ring stretching with the fundamental C-H stretching at 2725 cm-1 (Chicke et al., 1993).

Applications of FTIR on Epoxy Resins –

DGEBA

HDGEBA

DGEBA

HDGEBA

Mijovic et al., 1995).

Identification, Monitoring the Curing Process, Phase Separation and Water Uptake 267

2965- 2873 StretchingC-H of CH2 and CH aromatic and aliphatic

**Resin Band (cm-1) Assignment**

3057 Stretching of C-H of the oxirane ring

3052 Stretching of C-H of the oxirane ring

2937- 2862 StretchingC-H of CH2 and CH 1448 Deformation C-H of CH2 and CH3 1368 Deformation CH3 of C-(CH3)2 1098 Stretching C-O-C of ethers 909 Stretching C-O of oxirane group 846 Stretching C-O-C of oxirane group

Table 1. Characteristic bands of DGEBA and HDGEBA in the mid IR.

**Resin Band (cm-1) Assignment**

6072 First overtone of terminal CH2 stretching mode

4623 Overtone of C-H stretching of the aromatic ring

6060 First overtone of terminal CH2 stretching mode

Table 2. Characteristic bands of DGEBA and HDGEBA in the near IR. (George et al., 1991;

5239 Combination assymetric stretching and bending of O-H

<sup>4526</sup>Combination band of the second overtone of the epoxy ring stretching with the fundamental C-H stretching

5840- 5734 Overtones of -CH and -CH2 stretching

5244 Combination asymmetric stretching and bending of O-H

<sup>4531</sup>Combination band of the second overtone of the epoxy ring stretching with the fundamental C-H stretching

5988- 5889 Overtones of -CH and -CH2 stretching

4066 Stretching C-H of aromatic ring

1608 Stretching C=C of aromatic rings

1509 Stretching C-C of aromatic 1036 Stretching C-O-C of ethers 915 Stretching C-O of oxirane group 831 Stretching C-O-C of oxirane group

3500 O-H stretching

772 Rocking CH2

759 Rocking CH2

7099 O-H overtone

7028 O-H overtone

3500 O-H stretching

Anyway, this band is sufficiently separated from others and is suitable for quantitative analysis (Mijovic et al., 1995; Paz-Abuín et al., 1997a; Poisson et al., 1996; Xu & Schlup, 1998).

b. 6070 cm-1: First overtone of terminal CH2 stretching mode (Musto et al., 2000). This band interferes with the aromatic C-H stretching overtone at 5969 cm-1 (Xu et al., 1996), so in case there are aromatic rings in the structure (i.e. DGEBA) is not suitable for quantification.

### **2.1 Characterizing epoxy resins by IR**

Characterization of epoxies involves much more than the location of the oxirane ring bands. There are many epoxy resins with different structures, different polimerization degrees...etc. IR spectroscopy can be used to characterize the nature of the epoxy. Figure 4 shows the mIR and nIR spectra of two similar epoxy resins: Diglycidylether of bisphenol A (DGEBA) and its hydrogenated derivative (HDGEBA).

Fig. 4. FTIR spectra of DGEBA and HDGEBA in the medium and near ranges

The difference between both resins is the absence of aromatic rings in HDGEBA, which conditions both the properties (Tg, viscosity...etc) and reaction rate towards amines. Table 1 shows the assignation of bands for both resins in the mid range. The C-O deformation band is centered at 915 cm-1 in DGEBA and at 909 cm-1 in HDGEBA. C-H stretching of terminal oxirane group is observed in both cases at 3050 cm-1. The broad band at 3500 cm-1 is assigned to O-H stretching of hydroxyl groups, revealing the presence of dimers or high molecular weight species. There are also bands corresponding to the ether linkage located at 1000-1100 cm-1 in both cases. In HDGEBA no signals corresponding to neither aromatic rings nor double bonds are observed, so these two epoxies can be easily distinguished through these bands.

Spectra in the near range are shown in Figure 4 also and assignments in Table 2. The combination band of the second overtone of the epoxy ring stretching with the fundamental C-H stretching is centered at 4531 cm-1 in DGEBA and at 4526 cm-1 in HDGEBA. The region from 4000 to 4500 cm-1 contains the overtones from the fingerprint of the molecule.

The hydroxyl bands are sometimes useful for characterization although its quantitative use is very limited. Their presence is associated to the use of oligomers of low polymerization

b. 6070 cm-1: First overtone of terminal CH2 stretching mode (Musto et al., 2000). This band interferes with the aromatic C-H stretching overtone at 5969 cm-1 (Xu et al., 1996), so in case there are aromatic rings in the structure (i.e. DGEBA) is not suitable for

Characterization of epoxies involves much more than the location of the oxirane ring bands. There are many epoxy resins with different structures, different polimerization degrees...etc. IR spectroscopy can be used to characterize the nature of the epoxy. Figure 4 shows the mIR and nIR spectra of two similar epoxy resins: Diglycidylether of bisphenol A (DGEBA) and

Fig. 4. FTIR spectra of DGEBA and HDGEBA in the medium and near ranges

The difference between both resins is the absence of aromatic rings in HDGEBA, which conditions both the properties (Tg, viscosity...etc) and reaction rate towards amines. Table 1 shows the assignation of bands for both resins in the mid range. The C-O deformation band is centered at 915 cm-1 in DGEBA and at 909 cm-1 in HDGEBA. C-H stretching of terminal oxirane group is observed in both cases at 3050 cm-1. The broad band at 3500 cm-1 is assigned to O-H stretching of hydroxyl groups, revealing the presence of dimers or high molecular weight species. There are also bands corresponding to the ether linkage located at 1000-1100 cm-1 in both cases. In HDGEBA no signals corresponding to neither aromatic rings nor double bonds are observed, so these two epoxies can be easily distinguished through these bands.

Spectra in the near range are shown in Figure 4 also and assignments in Table 2. The combination band of the second overtone of the epoxy ring stretching with the fundamental C-H stretching is centered at 4531 cm-1 in DGEBA and at 4526 cm-1 in HDGEBA. The region

The hydroxyl bands are sometimes useful for characterization although its quantitative use is very limited. Their presence is associated to the use of oligomers of low polymerization

from 4000 to 4500 cm-1 contains the overtones from the fingerprint of the molecule.

1998).

quantification.

**2.1 Characterizing epoxy resins by IR**

its hydrogenated derivative (HDGEBA).

Anyway, this band is sufficiently separated from others and is suitable for quantitative analysis (Mijovic et al., 1995; Paz-Abuín et al., 1997a; Poisson et al., 1996; Xu & Schlup,

Table 1. Characteristic bands of DGEBA and HDGEBA in the mid IR.

Table 2. Characteristic bands of DGEBA and HDGEBA in the near IR. (George et al., 1991; Mijovic et al., 1995).

Applications of FTIR on Epoxy Resins –

corresponding to organic bonds appear.

usually weak.

the secondary amines show one single band.

Fig. 6. mIR and nIR spectra of metaxylylenediamine

diamines in both ranges are shown in Figure 6.

absorption bands at ≈ 3050 cm-1 or at 900 cm-1.

**3.1 Monitoring the curing process**

**3. Curing process**

Identification, Monitoring the Curing Process, Phase Separation and Water Uptake 269

The quantitative use of these bands is limited because of its position in the spectra: the N-H stretching is very close to the strong O-H absorption band (minimal amount of water perturbs its area), while the deformation band is located in the region where many signals

In the near range, the bands of amines are well defined and intense. There are also differences between the absorptions of primary and secondary amines. Primary amines N-H stretching first overtone is composed of two bands (symmetric and antisymmetric) located between 6897 cm-1 and 6452 cm-1, being the symmetric more intense. For secondary amines there is a single band. When both species coexist, this band cannot be used because the two bands overlap. Combination of N-H stretching and bending is observed at around 4900-5000 cm-1, and it can be used for quantitative purposes. (Weyer & Lo, 2002). Example spectra of

As shown in Figure 3, curing of epoxy resins with diamines can be described as a two step reaction: Firstly an epoxy group reacts with a primary amine yielding a secondary amine,

Considering these chemical reactions, the process can be monitored through the evolution of concentration of epoxy groups, primary amines or in some extent, secondary amines. The concentration of species is quantitatively related to the area of the absorption band only in the linear region, where Lambert Beer's law is satisfied. Taking this into account, changes in concentration of epoxy groups may be determined by mIR measuring the area of the

which in the second step reacts with another epoxy group yielding a tertiary amine

degree, as shown in Figure 2. In the mid range, quantification of OH is quite difficult because of the shape and overlapping of the band at around 3500 cm-1. In the near range, the absorption of the first O-H overtone is located at around 7000 cm-1, and although it has been used for quantification, no good results were obtained because of its weakness.

3,4-Epoxycyclohexyl-3'4'-epoxycyclohexane carboxylate (ECC) is probably the most common cycloaliphatic epoxy. The oxirane ring is in this case located in a six-member aliphatic cycle (Figure 2), shifting its absorptions in the mid range towards lower wave numbers, so the main absorption band is located at 790 cm-1 (Figure 5). This band has been used for quantitative analysis of photochemical reactions (Hartwig et al., 2002; Kim et al., 2003). Apart from the oxirane absorptions this resin shows the bands corresponding to the stretching C-O-C of ethers (1100 cm-1) and the C=O stretching (1730 cm-1) of esters, which can be useful for identification.

Fig. 5. FTIR spectra of ECC in the mid and near ranges

In the near range (Figure 5), it is worthy to note that the oxirane combination band (bending+ stretching) usually located at around 4530 cm-1 for common epoxies cannot be observed in the nIR spectrum of ECC probably because it may be overlapped with C-H combination bands. Neither the C=O second overtone (usually located at around 5100-5200 cm-1) is clearly observed. The main features observed in the spectrum are only the overtones of C-H and CH2 stretching bands. Although near infrared spectroscopy does not provide much useful information for this resin, it can still be used for monitoring the curing process through the evolution of the bands assigned to the curing agent (M. Gonzalez et al., 2011).

#### **2.2 Characterizing diamine hardeners by IR**

Among all the curing agents used to obtain epoxy thermosets, this chapter will be focused on one specific type: diamines. Their high reactivity is attributed to the high nucleophilicity of the nitrogen atom of the amino group although it is conditioned by its chemical structure. For instance, aliphatic diamines such as ethylene diamine, show a very high reactivity, while substituted aromatic amines like 4,4´-methylene-bis(3-chloro-2,6-diethylaniline) show lower reactivity because of the electronic effects of the aromatic ring and the susbstituents.

The amino group shows well defined absorptions both in the mid and in the near infrared ranges. The main absorptions in the mid range are stretching and deformation of N-H bonds. These bands also reflect some differences between primary and secondary amines:

The quantitative use of these bands is limited because of its position in the spectra: the N-H stretching is very close to the strong O-H absorption band (minimal amount of water perturbs its area), while the deformation band is located in the region where many signals corresponding to organic bonds appear.

Fig. 6. mIR and nIR spectra of metaxylylenediamine

In the near range, the bands of amines are well defined and intense. There are also differences between the absorptions of primary and secondary amines. Primary amines N-H stretching first overtone is composed of two bands (symmetric and antisymmetric) located between 6897 cm-1 and 6452 cm-1, being the symmetric more intense. For secondary amines there is a single band. When both species coexist, this band cannot be used because the two bands overlap. Combination of N-H stretching and bending is observed at around 4900-5000 cm-1, and it can be used for quantitative purposes. (Weyer & Lo, 2002). Example spectra of diamines in both ranges are shown in Figure 6.

## **3. Curing process**

268 Infrared Spectroscopy – Materials Science, Engineering and Technology

degree, as shown in Figure 2. In the mid range, quantification of OH is quite difficult because of the shape and overlapping of the band at around 3500 cm-1. In the near range, the absorption of the first O-H overtone is located at around 7000 cm-1, and although it has been

3,4-Epoxycyclohexyl-3'4'-epoxycyclohexane carboxylate (ECC) is probably the most common cycloaliphatic epoxy. The oxirane ring is in this case located in a six-member aliphatic cycle (Figure 2), shifting its absorptions in the mid range towards lower wave numbers, so the main absorption band is located at 790 cm-1 (Figure 5). This band has been used for quantitative analysis of photochemical reactions (Hartwig et al., 2002; Kim et al., 2003). Apart from the oxirane absorptions this resin shows the bands corresponding to the stretching C-O-C of ethers (1100 cm-1) and the C=O stretching (1730 cm-1) of esters, which

In the near range (Figure 5), it is worthy to note that the oxirane combination band (bending+ stretching) usually located at around 4530 cm-1 for common epoxies cannot be observed in the nIR spectrum of ECC probably because it may be overlapped with C-H combination bands. Neither the C=O second overtone (usually located at around 5100-5200 cm-1) is clearly observed. The main features observed in the spectrum are only the overtones of C-H and CH2 stretching bands. Although near infrared spectroscopy does not provide much useful information for this resin, it can still be used for monitoring the curing process through the evolution of the bands assigned to the curing agent (M. Gonzalez et al., 2011).

Among all the curing agents used to obtain epoxy thermosets, this chapter will be focused on one specific type: diamines. Their high reactivity is attributed to the high nucleophilicity of the nitrogen atom of the amino group although it is conditioned by its chemical structure. For instance, aliphatic diamines such as ethylene diamine, show a very high reactivity, while substituted aromatic amines like 4,4´-methylene-bis(3-chloro-2,6-diethylaniline) show lower

The amino group shows well defined absorptions both in the mid and in the near infrared ranges. The main absorptions in the mid range are stretching and deformation of N-H bonds. These bands also reflect some differences between primary and secondary amines:

reactivity because of the electronic effects of the aromatic ring and the susbstituents.

used for quantification, no good results were obtained because of its weakness.

can be useful for identification.

Fig. 5. FTIR spectra of ECC in the mid and near ranges

**2.2 Characterizing diamine hardeners by IR**

#### **3.1 Monitoring the curing process**

As shown in Figure 3, curing of epoxy resins with diamines can be described as a two step reaction: Firstly an epoxy group reacts with a primary amine yielding a secondary amine, which in the second step reacts with another epoxy group yielding a tertiary amine

Considering these chemical reactions, the process can be monitored through the evolution of concentration of epoxy groups, primary amines or in some extent, secondary amines. The concentration of species is quantitatively related to the area of the absorption band only in the linear region, where Lambert Beer's law is satisfied. Taking this into account, changes in concentration of epoxy groups may be determined by mIR measuring the area of the absorption bands at ≈ 3050 cm-1 or at 900 cm-1.

Applications of FTIR on Epoxy Resins –

secondary amines into tertiary amines.

Identification, Monitoring the Curing Process, Phase Separation and Water Uptake 271

region the overtones of both primary and secondary amines overlap, so an initial decrease is observed, followed by an increase and a shift towards lower wavenumbers (because of the generation of secondary amines) and a final decrease consequence of the transformation of

For quantitative analysis, changes in concentration of epoxy and primary amines can be directly determined from the integration of the bands at ≈ 4530 cm-1 and at ≈ 4900 cm-1 respectively, and the epoxy () and primary amine (β) conversion degrees can be calculated as shown in eq (1). This fact opens the possibility of using complex models in which the concentration of all species (primary, secondary, tertiary amine and epoxy) can be considered during the curing process and kinetic parameters for the different steps of the reaction can be obtained. In Figure 8 typical conversion-time profiles for both and β at different temperatures are shown. After an initial fast increase in conversion a "plateau" region is reached, corresponding to the diffusion controlled stage (vitrification). As it is shown, the "plateau" for the primary amine conversion is often achieved at conversions

very close to 1, indicating that during curing the primary amine is fully consumed.

Fig. 8. Epoxy () and primary amine (β) conversions at different temperatures for

usually bands corresponding to overtones of the resin skeleton are used.

cm-1 (Kradjel & Lee, 2008; Mijovic and Andjelic, 1995; M. Gonzalez et al., 2011).

Shrinkage during curing or initial sample thermostatting can lead to major errors in epoxy and primary amino bands integration. To avoid this difficulty, it is useful to normalize the integrated areas to a characteristic band not changing during curing. For this purpose,

Curing cycloaliphatic epoxies with amines is not common because of the low reactivity of the system even at high temperatures. Anyway, its thermal curing with some complex amines (like poly (3-aminopropylmethylsiloxane)) has been reported. Determining conversion in these systems by IR is not an easy task, since the combination bands of the epoxy group in the near range overlap with other bands. Nevertheless, it is possible a semiquantitative approach considering the primary amine combination band at ≈ 4900 cm-1 and at longer reaction times (when primary amine is exhausted) progress of the reaction can be qualitatively followed from the primary and secondary amine combination band at 6530

HDGEBA/poly(3-aminopropylmethyl)siloxane.

Nevertheless, following curing by IR is not always easy, because the epoxy band at higher wavenumbers shows low sensitivity to changes in concentration as a consequence of its intrinsic low intensity and the 900 cm-1 band may be affected by the uncleanliness of the region where it is located. This may induce some uncertainty at the final stages of reaction when the concentration of epoxy groups is small. On the other hand, the quantification of primary and secondary amines in epoxy/amine reactive systems is not possible since the band corresponding to primary amines overlaps both with the band corresponding to secondary amines and the one corresponding to hydroxyl groups, which are species appearing as a consequence of the advance of the chemical reaction. Despite all these facts, mIR has been successfully used for monitoring the epoxy amine chemical reaction in several cases (Nikolic et al., 2010).

Fortunately nIR can be safely used for quantitatively monitor the chemical reaction (Paz-Abuin et al., 1997a, 1997b; Mijovic & Andjelic 1995a; Mijovic et al. 1995). In this region we can find well defined bands free of overlapping related with the epoxy and primary amine: the combination band of the second overtone of the epoxy ring stretching with the fundamental C-H stretching (≈ 4530 cm-1) and the combination band of NH stretching and bending (≈ 4900-5000 cm-1). In Figure 7, a typical spectral evolution on cure can be observed.

Fig. 7. Time evolution of FTnIR spectra during the isothermal curing at 70 ºC of the stoichiometric HDGEBA/poly(3-aminopropylmethyl)siloxane system.

The reaction mechanism indicates that the epoxy concentration decreases, and this is observed in the spectra as the decrease of the band centered at ≈ 4530 cm-1 and also of the weak overtone of terminal CH2 at ≈ 6060 cm-1. The primary amine combination band decreases too (≈ 4900 cm-1), and once it is exhausted it can be observed that there are still epoxy groups in the reaction media, which will react with the previously formed secondary amines up to vitrification or until the reaction is completed. The band correponding to O-H overtones (≈ 7000 cm-1) also increases during curing as a consequence of the oxirane ringopening, although this band is not suitable for quantification because of the low signal/noise ratio. The behavior of the band located at ≈ 6500 cm-1 is more complex: in this

Nevertheless, following curing by IR is not always easy, because the epoxy band at higher wavenumbers shows low sensitivity to changes in concentration as a consequence of its intrinsic low intensity and the 900 cm-1 band may be affected by the uncleanliness of the region where it is located. This may induce some uncertainty at the final stages of reaction when the concentration of epoxy groups is small. On the other hand, the quantification of primary and secondary amines in epoxy/amine reactive systems is not possible since the band corresponding to primary amines overlaps both with the band corresponding to secondary amines and the one corresponding to hydroxyl groups, which are species appearing as a consequence of the advance of the chemical reaction. Despite all these facts, mIR has been successfully used for monitoring the epoxy amine chemical reaction in several

Fortunately nIR can be safely used for quantitatively monitor the chemical reaction (Paz-Abuin et al., 1997a, 1997b; Mijovic & Andjelic 1995a; Mijovic et al. 1995). In this region we can find well defined bands free of overlapping related with the epoxy and primary amine: the combination band of the second overtone of the epoxy ring stretching with the fundamental C-H stretching (≈ 4530 cm-1) and the combination band of NH stretching and bending (≈ 4900-5000 cm-1). In Figure 7, a typical spectral evolution on cure can be observed.

Fig. 7. Time evolution of FTnIR spectra during the isothermal curing at 70 ºC of the

The reaction mechanism indicates that the epoxy concentration decreases, and this is observed in the spectra as the decrease of the band centered at ≈ 4530 cm-1 and also of the weak overtone of terminal CH2 at ≈ 6060 cm-1. The primary amine combination band decreases too (≈ 4900 cm-1), and once it is exhausted it can be observed that there are still epoxy groups in the reaction media, which will react with the previously formed secondary amines up to vitrification or until the reaction is completed. The band correponding to O-H overtones (≈ 7000 cm-1) also increases during curing as a consequence of the oxirane ringopening, although this band is not suitable for quantification because of the low signal/noise ratio. The behavior of the band located at ≈ 6500 cm-1 is more complex: in this

stoichiometric HDGEBA/poly(3-aminopropylmethyl)siloxane system.

cases (Nikolic et al., 2010).

region the overtones of both primary and secondary amines overlap, so an initial decrease is observed, followed by an increase and a shift towards lower wavenumbers (because of the generation of secondary amines) and a final decrease consequence of the transformation of secondary amines into tertiary amines.

For quantitative analysis, changes in concentration of epoxy and primary amines can be directly determined from the integration of the bands at ≈ 4530 cm-1 and at ≈ 4900 cm-1 respectively, and the epoxy () and primary amine (β) conversion degrees can be calculated as shown in eq (1). This fact opens the possibility of using complex models in which the concentration of all species (primary, secondary, tertiary amine and epoxy) can be considered during the curing process and kinetic parameters for the different steps of the reaction can be obtained. In Figure 8 typical conversion-time profiles for both and β at different temperatures are shown. After an initial fast increase in conversion a "plateau" region is reached, corresponding to the diffusion controlled stage (vitrification). As it is shown, the "plateau" for the primary amine conversion is often achieved at conversions very close to 1, indicating that during curing the primary amine is fully consumed.

Fig. 8. Epoxy () and primary amine (β) conversions at different temperatures for HDGEBA/poly(3-aminopropylmethyl)siloxane.

Shrinkage during curing or initial sample thermostatting can lead to major errors in epoxy and primary amino bands integration. To avoid this difficulty, it is useful to normalize the integrated areas to a characteristic band not changing during curing. For this purpose, usually bands corresponding to overtones of the resin skeleton are used.

Curing cycloaliphatic epoxies with amines is not common because of the low reactivity of the system even at high temperatures. Anyway, its thermal curing with some complex amines (like poly (3-aminopropylmethylsiloxane)) has been reported. Determining conversion in these systems by IR is not an easy task, since the combination bands of the epoxy group in the near range overlap with other bands. Nevertheless, it is possible a semiquantitative approach considering the primary amine combination band at ≈ 4900 cm-1 and at longer reaction times (when primary amine is exhausted) progress of the reaction can be qualitatively followed from the primary and secondary amine combination band at 6530 cm-1 (Kradjel & Lee, 2008; Mijovic and Andjelic, 1995; M. Gonzalez et al., 2011).

Applications of FTIR on Epoxy Resins –

Identification, Monitoring the Curing Process, Phase Separation and Water Uptake 273

Fig. 9. Typical evolution of concentration of primary (A1), secondary (A2) and tertiary amine (A3) groups during curing. Reactive system: DGEBA/m-Xylylenediamine at 80ºC. (Used with permission from (González, M.; Kindelán, M.; Cabanelas, J.C.; Baselga,J.

1

 <sup>0</sup> 1 1

1 1 [ ] ´ [ ] *<sup>d</sup> OH K K dt E*

*d Bd OH B KK dt dt E*

2 1 10

1 10

**3.2.2 Reactivity ratio between primary and secondary amines**

[ ] ´ ´[ ] *K kE K kE*

<sup>0</sup>

[ ] R ´

2 2

Some kinetic models assume that the reactivity of primary and secondary amines is the same. Considering that primary amines have two reactive hydrogen atoms, equal reactivity yields R = 0.5. Nevertheless, in most of epoxy amine systems higher reactivity of primary amines (R<0.5) has been experimentally observed (Matejka, 2000; Paz-Abuin et al.,1997a, 1997b, 1998; Liu et al., 2004; Varley et al., 2006). This behavior is not surprising since the addition of the epoxy molecule to a primary amine causes an steric hindrance. On the other hand, the chemical nature of the new substituent usually decreases the nucleophilic character (and thus the reactivity) of the nitrogen atom in the amine group due to a negative inductive effect.

Paz-Abuín et al. developed a method for quantifying the reactivity ratio from the concentration-time plots of amines (Paz-Abuin et al., 1997a). Considering the classical reaction mechanism, applying the condition for maximum to *[A2]*, it is obtained that

1 1

0

(2)

(3)

[ ]

1 1 ´ <sup>R</sup> ´ *k k k k*

0

*Macromolecular Symposia,* Vol.200. Copyright (2003)).

2

where:

## **3.2 Modeling kinetics**

Curing kinetics is a key aspect in epoxy systems, since it determines the time spam available for shaping, storing... As in most chemically reactive systems, reaction rate is temperature dependent.

Several models have been developed for epoxy/amine kinetics through the study of model compounds (Schechter et al., 1956). An acceleration of reaction in the presence of OH groups was observed and explained considering a third order reaction mechanism (Smith, 1961). Horie and coworkers proposed a model in 1970 (Horie et al., 1970) considering the catalysis of both initial OH (due to DGEBA oligomers and impurities) and OH generated during chemical reaction (autocatalysis) which has been used and validated in many epoxy/amine systems at different temperatures (Simon et al., 2000; Vyazovkin & Sbirrazouli, 1996; Cole et al., 1991; Riccardi et al., 1984). Later on, modifications to the model have been introduced, for example considering the different reactivity of hydrogens belonging to primary and secondary amines and the possible homopolymerization reactions between epoxy groups under certain conditions (Cole et al., 1991; Riccardi & Williams, 1986). Thus, following the evolution of concentration of the different species during curing is useful for modeling epoxy/amine systems.

The commonly accepted kinetic scheme for epoxy-amine reactions considers two reaction paths: a non-catalyzed and an autocatalyzed path. The autocatalysis is attributed to the formation of complex between generated or initially present hydroxyl groups, amino groups and epoxy groups. A simple reaction mechanism is presented in Figure 3 although it can be improved considering some equilibrium reactions for the complexes formation (Ehlers et al., 2007). With appropriate mass balances it is possible to set out rate equations that can be fitted to experimental data to extract the relevant kinetic parameters

## **3.2.1 Determining concentrations during curing**

Considering the reaction scheme, the concentration of epoxy groups, primary, secondary and tertiary amine, as well as hydroxyl groups can be determined through the following mass balances:

$$\begin{aligned} [A\_1] = [A\_1]\_0 - [A\_2] - [A\_3] \ & \vdots & [E] = [E]\_0 - [A\_2] - 2[A\_3] \ & \vdots & [OH] = [OH]\_0 + [E]\_0 - [E] \end{aligned} $$

If initial concentrations of epoxy and primary amine are known, the concentration of all species at each instant can be determined from the conversion data obtained by nIR:

$$\begin{array}{cccc} [E] = [E]\_0 \left( 1 - \alpha \right) & ; & [A\_1] = [A\_1]\_0 \left( 1 - \beta \right) & ; & [A\_2] = [E]\_0 \left( \beta B - \alpha \right) & ; & [A\_3] = [E]\_0 \left( \alpha - \beta \frac{B}{2} \right) \end{array}$$

Where *B=2[A1]0/[E]0* is the ratio between the initial concentration of primary amine and epoxy. A typical variation of all these species with time is presented in Figure 9.

Assuming that the reactivity ratio between primary and secondary amines (R) is independent of the reaction path, the kinetic equations for the epoxy and primary amine conversion are:

Fig. 9. Typical evolution of concentration of primary (A1), secondary (A2) and tertiary amine (A3) groups during curing. Reactive system: DGEBA/m-Xylylenediamine at 80ºC. (Used with permission from (González, M.; Kindelán, M.; Cabanelas, J.C.; Baselga,J. *Macromolecular Symposia,* Vol.200. Copyright (2003)).

$$\frac{d\alpha}{dt} = \frac{\mathcal{B}}{2}\frac{d\beta}{dt} + \mathcal{R}\left(\mathcal{B}\beta - \alpha\right)\left(1 - \alpha\right)\left(K\_1 + K\_1'\left(\frac{\left[OH\right]\_0}{\left[E\right]\_0} + \alpha\right)\right) \tag{2}$$

$$\frac{d\beta}{dt} = (1 - \beta)(1 - \alpha)\left(K\_1 + K\_1' \left(\frac{[OH]\_0}{[E]\_0} + \alpha\right)\right) \tag{3}$$

where:

272 Infrared Spectroscopy – Materials Science, Engineering and Technology

Curing kinetics is a key aspect in epoxy systems, since it determines the time spam available for shaping, storing... As in most chemically reactive systems, reaction rate is temperature

Several models have been developed for epoxy/amine kinetics through the study of model compounds (Schechter et al., 1956). An acceleration of reaction in the presence of OH groups was observed and explained considering a third order reaction mechanism (Smith, 1961). Horie and coworkers proposed a model in 1970 (Horie et al., 1970) considering the catalysis of both initial OH (due to DGEBA oligomers and impurities) and OH generated during chemical reaction (autocatalysis) which has been used and validated in many epoxy/amine systems at different temperatures (Simon et al., 2000; Vyazovkin & Sbirrazouli, 1996; Cole et al., 1991; Riccardi et al., 1984). Later on, modifications to the model have been introduced, for example considering the different reactivity of hydrogens belonging to primary and secondary amines and the possible homopolymerization reactions between epoxy groups under certain conditions (Cole et al., 1991; Riccardi & Williams, 1986). Thus, following the evolution of concentration of the different species during curing is useful for modeling

The commonly accepted kinetic scheme for epoxy-amine reactions considers two reaction paths: a non-catalyzed and an autocatalyzed path. The autocatalysis is attributed to the formation of complex between generated or initially present hydroxyl groups, amino groups and epoxy groups. A simple reaction mechanism is presented in Figure 3 although it can be improved considering some equilibrium reactions for the complexes formation (Ehlers et al., 2007). With appropriate mass balances it is possible to set out rate equations that can be

Considering the reaction scheme, the concentration of epoxy groups, primary, secondary and tertiary amine, as well as hydroxyl groups can be determined through the following

1 10 2 3 02 3 0 0 [ ] [ ] [ ] [ ];[] [] [ ] [ ];[ ] [ ] [] [] *A A A A E E A A OH OH E E* 2

If initial concentrations of epoxy and primary amine are known, the concentration of all

<sup>0</sup> 1 10 2 0 3 0 1 1 <sup>2</sup> [] [] ; [ ] [ ] ; [ ] [] ; [ ] [] *<sup>B</sup> EE A A A E B A E*

Where *B=2[A1]0/[E]0* is the ratio between the initial concentration of primary amine and

Assuming that the reactivity ratio between primary and secondary amines (R) is independent of the reaction path, the kinetic equations for the epoxy and primary amine

species at each instant can be determined from the conversion data obtained by nIR:

epoxy. A typical variation of all these species with time is presented in Figure 9.

fitted to experimental data to extract the relevant kinetic parameters

**3.2.1 Determining concentrations during curing**

**3.2 Modeling kinetics**

epoxy/amine systems.

mass balances:

conversion are:

dependent.

$$\begin{aligned} K\_1 &= k\_1 [E]\_0 \\ K'\_1 &= k'\_1 [E]\_0^2 \end{aligned} \qquad \qquad \qquad \qquad \quad \mathbf{R} = \frac{k\_2}{k\_1} = \frac{k'\_2}{k'\_1}$$

#### **3.2.2 Reactivity ratio between primary and secondary amines**

Some kinetic models assume that the reactivity of primary and secondary amines is the same. Considering that primary amines have two reactive hydrogen atoms, equal reactivity yields R = 0.5. Nevertheless, in most of epoxy amine systems higher reactivity of primary amines (R<0.5) has been experimentally observed (Matejka, 2000; Paz-Abuin et al.,1997a, 1997b, 1998; Liu et al., 2004; Varley et al., 2006). This behavior is not surprising since the addition of the epoxy molecule to a primary amine causes an steric hindrance. On the other hand, the chemical nature of the new substituent usually decreases the nucleophilic character (and thus the reactivity) of the nitrogen atom in the amine group due to a negative inductive effect.

Paz-Abuín et al. developed a method for quantifying the reactivity ratio from the concentration-time plots of amines (Paz-Abuin et al., 1997a). Considering the classical reaction mechanism, applying the condition for maximum to *[A2]*, it is obtained that

Applications of FTIR on Epoxy Resins –

Identification, Monitoring the Curing Process, Phase Separation and Water Uptake 275

Fig. 11. and as a function of curing time for DGEBA / m-XDA at 60 ºC. Lines: fitting to

() () ( ) ( ) *i i*

were O(ti) and C(ti) are the observed and calculated values of (or ) respectively. (Used with permission from (González, M.; Kindelán, M.; Cabanelas, J.C.; Baselga,J. *Macromolecular*

Phase separation in blends involves the development of a second phase which usually has a different refractive index, and can be detected by the appearance of turbidity. Most studies analyze the so-called "cloud point" (instant when the sample is no longer transparent) measuring visible transmittance. Particles scatter light when its size is similar to the wavelength of the incident radiation; since infrared radiation ranges from 780 nm to 15 μm (from 780 nm to 1.1 μm for the near range and from 1.1 μm to 15 μm for the mid range), the onset of phase separation can be detected using nIR or mIR although with less accuracy (Bhargava et al, 1999) than using visible light. Therefore, IR measurements give delayed values of the cloud point. This fact is clear, and even more sophisticated techniques like SAXS may give information of the incipient phase separation process, but there is an advantage for IR: it provides additional chemical information during phase separation. Because of its longer wavelength, mIR is rarely used for characterizing phase separation phenomena, although it is used for characterizing other systems containing particles of

*Ot Ct r t O t*

*i*

*i*

eqs (1) and (2). Below: weighted residuals calculated as:

**4. Phase separation influence on IR spectra**

bigger size or to avoid interferences due to the color of the systems.

*Symposia,* Vol.200. Copyright (2003)).

*R=[A1]/[A2].* Thus, R value can determined from the concentration curves as the ratio of the concentration of primary amine and secondary amine at the maximum of secondary amine concentration. Usually the R value is below 0.5, i.e. it shows the higher reactivity of primary amines. If R is not very low, the uncertainty in the determination of the maximum is small and the R value can be precisely determined.

#### **3.2.3 Solving kinetic equations**

Rate constants can be obtained solving the rate equations (2) and (3) mentioned above. Since both equations are interdependent, two approaches for solving them may be used:

$$\mathcal{A} = \frac{[A\_2]}{[E]\_0}$$

Thus a single equation in terms of the derivative of epoxy conversion is obtained, so that the global kinetic constants can be obtained as the intercept and slope of the linear fit at low conversions (far from the diffusion controlled region) of the expression:

$$\frac{\frac{da}{dt}}{(1-a)\left(\lambda + R\left(B - 2\lambda - a\right)\right)} = K\_1 + K\_1'\left(\frac{[OH]\_0}{[E]\_0} + a\right).$$

A typical example of the linearization method is presented in Figure 10.

Fig. 10. Determination of K1 and K´1.

*R=[A1]/[A2].* Thus, R value can determined from the concentration curves as the ratio of the concentration of primary amine and secondary amine at the maximum of secondary amine concentration. Usually the R value is below 0.5, i.e. it shows the higher reactivity of primary amines. If R is not very low, the uncertainty in the determination of the maximum is small

Rate constants can be obtained solving the rate equations (2) and (3) mentioned above. Since

2 0 [ ] [ ] *A E*

*dt OH K K R B E*

0

[ ] ´ [ ]

1 1

Thus a single equation in terms of the derivative of epoxy conversion is obtained, so that the global kinetic constants can be obtained as the intercept and slope of the linear fit at low

both equations are interdependent, two approaches for solving them may be used:

<sup>0</sup> 1 2

and the R value can be precisely determined.

conversions (far from the diffusion controlled region) of the expression:

A typical example of the linearization method is presented in Figure 10.

*d*

**3.2.3 Solving kinetic equations**

Fig. 10. Determination of K1 and K´1.

Gonzalez et al., 2003).

Fig. 11. and as a function of curing time for DGEBA / m-XDA at 60 ºC. Lines: fitting to eqs (1) and (2). Below: weighted residuals calculated as:

$$r(t\_i) = \frac{O(t\_i) - C(t\_i)}{\sqrt{O(t\_i)}}$$

were O(ti) and C(ti) are the observed and calculated values of (or ) respectively. (Used with permission from (González, M.; Kindelán, M.; Cabanelas, J.C.; Baselga,J. *Macromolecular Symposia,* Vol.200. Copyright (2003)).

### **4. Phase separation influence on IR spectra**

Phase separation in blends involves the development of a second phase which usually has a different refractive index, and can be detected by the appearance of turbidity. Most studies analyze the so-called "cloud point" (instant when the sample is no longer transparent) measuring visible transmittance. Particles scatter light when its size is similar to the wavelength of the incident radiation; since infrared radiation ranges from 780 nm to 15 μm (from 780 nm to 1.1 μm for the near range and from 1.1 μm to 15 μm for the mid range), the onset of phase separation can be detected using nIR or mIR although with less accuracy (Bhargava et al, 1999) than using visible light. Therefore, IR measurements give delayed values of the cloud point. This fact is clear, and even more sophisticated techniques like SAXS may give information of the incipient phase separation process, but there is an advantage for IR: it provides additional chemical information during phase separation. Because of its longer wavelength, mIR is rarely used for characterizing phase separation phenomena, although it is used for characterizing other systems containing particles of bigger size or to avoid interferences due to the color of the systems.

Applications of FTIR on Epoxy Resins –

information on dimensional changes of the specimens.

bonded respectively (Musto et al., 2002).

be calculated as:

Identification, Monitoring the Curing Process, Phase Separation and Water Uptake 277

and many different techniques have been used: from the fast and easy gravimetry to more complex techniques such as NMR spectroscopy (Zhou & Lucas 1999) or fluorescence (Mikes et al., 2003). Also infrared spectroscopy has been widely used. IR shows an advantage when compared with gravimetry: it is not only an accurate technique for determining water concentration, but also provides information at the molecular level about the interactions between water molecules and the thermoset structure and can be used to provide

Water has three active vibration modes in infrared corresponding to the stretching of O-H bond (≈ 3800- 3600 cm-1 in liquid state) and bending (≈ 1650-1590 cm-1 in liquid state). The position of the bands of this molecule is particularly sensitive towards interactions like hydrogen bonding, which originates displacements towards lower wavenumbers (< 3600 cm-1), enabling the distinction between free water, hydrogen bonded and intramolecular hydrogen bonding (Socrates, 1994). When absorbed in epoxy resins, two types of water are found: highly mobile free water molecules (≈ 3600 cm-1) and water bounded to specific sites through hydrogen bonding (≈ 3300 cm-1) (Blanco et al., 2006; Cotugno et al., 2005; Grave et al, 1998). Signals can also be observed in the near infrared range: at 5215 cm-1 resulting from the combination of asymmetric stretching and bending and in the range 7800 - 6000 cm-1 hydroxyl vibrations are also found. The latter band can be deconvoluted into three peaks centered at 7075, 6820 and 3535 cm-1 attributed to free water, self-associated and hydrogen

Infrared spectroscopy in both ranges has been used to monitor water uptake and diffusion coefficients have been determined using Fick's law. The band located at 5215 cm-1 can be used to quantify water, although it must be normalized for sample thickness. The band at higher wavenumbers is used to determine the kind of interactions between water and network (Mijovic & Zhang, 2003; Cabanelas et al., 2003), but not with quantitative purposes since it is superimposed on the O-H overtone of the resin (Musto et al., 2000). To overcome the thickness variation it is possible to normalize water signal with a reference band invariant against the presence of water (for example, the band at 4623 cm-1, corresponding to aromatic rings of DGEBA). This peak, in principle should not change by the water ingress, only by the volume change due to swelling. In this way, the fractional absorbed water can

> 5215 0 5215 4623 0 4623

, , , , , ,

*A A*

*A*

Ingress of water swells the specimens changing its dimensions. The volume changes related with swelling have been characterized measuring a reference band and using the following

0 4623

3 2 0

<sup>1</sup> ( ) *t*

0 0 5215

*W A A*

*t*

*t t*

*W A*

expression that can be easily derived from Lambert-Beer law (Cabanelas et al. 2003).

*V t A V A*

0

Turbidity is observed in IR spectra as an increase of baseline. This parameter can be used to follow the phase separation process in a region where no bands exist, i.e 6300 cm-1. Alternatively, this method has also been used to follow compatibilization of initially immiscible systems. As an example Cabanelas et al. (Cabanelas et al., 2005) studied the compatibilization process and phase separation of a third component in reactive blends based on DGEBA and poly(3-aminopropylmethylsiloxane) modified with PMMA. As shown in Figure 12, the initial decrease of the baseline was related with the compatibilization between DGEBA and the silicone hardener and the subsequent increase was related with the onset of phase separation of the thermoplastic modifier. IR can also provide information about the interactions between the modifier and the thermosetting matrix. Typical cured epoxy thermosets present a variety of OHN, OHNH and OHOH hydrogen bonds. In the presence of PMMA intramolecular interactions become redistributed since the carbonyl groups of PMMA interact with the initially present and newly formed OH groups as it is shown by the presence of a carbonyl-OH hydrogen bonding band centered at 3500 cm-1 (Blanco et al., 2009). These changes in IR spectra may be related with the miscibility in complex systems.

Fig. 12. Baseline from FTIR spectra at 6300 cm-1 as a function of epoxy conversion of DGEBA/PAMS for different weight concentrations of PMMA as modifier (Adapted with permission from (Cabanelas, J.C.; Serrano, B.; Baselga, J. *Macromolecules,* Vol.38, No.3, (2005),). Copyright (2005) American Chemical Society).

#### **5. Water uptake**

One of the main drawbacks of epoxy resins is its high water uptake. Water deteriorates thermomechanical properties (Tg, modulus, yield strength, toughness...), and adhesion, it induces chemical degradation of the network and also generates stresses because of swelling (Nogueira et al., 2001; Cotugno et al., 2001; Blanco et al., 2006; Ji et al., 2006; Xiao & Shanahan, 2008). Significant efforts have been done to elucidate the interactions of water with epoxy/amine networks and the diffusion mechanisms operating during water uptake,

Turbidity is observed in IR spectra as an increase of baseline. This parameter can be used to follow the phase separation process in a region where no bands exist, i.e 6300 cm-1. Alternatively, this method has also been used to follow compatibilization of initially immiscible systems. As an example Cabanelas et al. (Cabanelas et al., 2005) studied the compatibilization process and phase separation of a third component in reactive blends based on DGEBA and poly(3-aminopropylmethylsiloxane) modified with PMMA. As shown in Figure 12, the initial decrease of the baseline was related with the compatibilization between DGEBA and the silicone hardener and the subsequent increase was related with the onset of phase separation of the thermoplastic modifier. IR can also provide information about the interactions between the modifier and the thermosetting matrix. Typical cured epoxy thermosets present a variety of OHN, OHNH and OHOH hydrogen bonds. In the presence of PMMA intramolecular interactions become redistributed since the carbonyl groups of PMMA interact with the initially present and newly formed OH groups as it is shown by the presence of a carbonyl-OH hydrogen bonding band centered at 3500 cm-1 (Blanco et al., 2009). These changes in IR spectra may be

Fig. 12. Baseline from FTIR spectra at 6300 cm-1 as a function of epoxy conversion of DGEBA/PAMS for different weight concentrations of PMMA as modifier (Adapted with permission from (Cabanelas, J.C.; Serrano, B.; Baselga, J. *Macromolecules,* Vol.38, No.3,

One of the main drawbacks of epoxy resins is its high water uptake. Water deteriorates thermomechanical properties (Tg, modulus, yield strength, toughness...), and adhesion, it induces chemical degradation of the network and also generates stresses because of swelling (Nogueira et al., 2001; Cotugno et al., 2001; Blanco et al., 2006; Ji et al., 2006; Xiao & Shanahan, 2008). Significant efforts have been done to elucidate the interactions of water with epoxy/amine networks and the diffusion mechanisms operating during water uptake,

(2005),). Copyright (2005) American Chemical Society).

**5. Water uptake**

related with the miscibility in complex systems.

and many different techniques have been used: from the fast and easy gravimetry to more complex techniques such as NMR spectroscopy (Zhou & Lucas 1999) or fluorescence (Mikes et al., 2003). Also infrared spectroscopy has been widely used. IR shows an advantage when compared with gravimetry: it is not only an accurate technique for determining water concentration, but also provides information at the molecular level about the interactions between water molecules and the thermoset structure and can be used to provide information on dimensional changes of the specimens.

Water has three active vibration modes in infrared corresponding to the stretching of O-H bond (≈ 3800- 3600 cm-1 in liquid state) and bending (≈ 1650-1590 cm-1 in liquid state). The position of the bands of this molecule is particularly sensitive towards interactions like hydrogen bonding, which originates displacements towards lower wavenumbers (< 3600 cm-1), enabling the distinction between free water, hydrogen bonded and intramolecular hydrogen bonding (Socrates, 1994). When absorbed in epoxy resins, two types of water are found: highly mobile free water molecules (≈ 3600 cm-1) and water bounded to specific sites through hydrogen bonding (≈ 3300 cm-1) (Blanco et al., 2006; Cotugno et al., 2005; Grave et al, 1998). Signals can also be observed in the near infrared range: at 5215 cm-1 resulting from the combination of asymmetric stretching and bending and in the range 7800 - 6000 cm-1 hydroxyl vibrations are also found. The latter band can be deconvoluted into three peaks centered at 7075, 6820 and 3535 cm-1 attributed to free water, self-associated and hydrogen bonded respectively (Musto et al., 2002).

Infrared spectroscopy in both ranges has been used to monitor water uptake and diffusion coefficients have been determined using Fick's law. The band located at 5215 cm-1 can be used to quantify water, although it must be normalized for sample thickness. The band at higher wavenumbers is used to determine the kind of interactions between water and network (Mijovic & Zhang, 2003; Cabanelas et al., 2003), but not with quantitative purposes since it is superimposed on the O-H overtone of the resin (Musto et al., 2000). To overcome the thickness variation it is possible to normalize water signal with a reference band invariant against the presence of water (for example, the band at 4623 cm-1, corresponding to aromatic rings of DGEBA). This peak, in principle should not change by the water ingress, only by the volume change due to swelling. In this way, the fractional absorbed water can be calculated as:

$$\frac{\Delta W\_t}{W\_0} = \frac{\left(\frac{A\_{t,S215}}{A\_{t,4623}}\right) - \left(\frac{A\_{0,S215}}{A\_{0,4623}}\right)}{\left(\frac{A\_{0,S215}}{A\_{0,4623}}\right)}$$

Ingress of water swells the specimens changing its dimensions. The volume changes related with swelling have been characterized measuring a reference band and using the following expression that can be easily derived from Lambert-Beer law (Cabanelas et al. 2003).

$$\frac{\Delta V(t)}{V\_0} = \left(\frac{A\_0}{A\_t}\right)^{\frac{\lambda}{\lambda}} - 1$$

Applications of FTIR on Epoxy Resins –

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The small volume changes due to swelling are prone to large errors if determined by usual means (for example, with a caliper). Figure 13 shows good correlations between the fractional volume change during water uptake in an epoxy resin as measured gravimetrically, by FTIR or measuring the change on dimensions of the specimens.

Fig. 13. Comparison of volume change determined by n-FTIR, (V/V0)IR, and measured with a micrometer, (left) or by gravimetry (right), for fully cured DGEBA/ Poly(aminopropylsiloxane) with 0.381 mm thickness.

## **6. Conclusion**

The curing and ageing of epoxy resins are complex phenomena of the prime importance in industry. FTIR appears to be a valuable tool for both qualitative analysis and quantification of these processes. It has been shown how to extract relevant information from spectra to identify typical components of resins and hardeners. Following time variations of specific bands allows extracting relevant kinetic parameters to get more insight about the specific reaction mechanism of curing process. Inspection of subtle changes in baseline can be correlated with both, miscibilization or phase separation processes. Detailed analysis of OH bands allows extracting information about intermolecular interactions within the components of the resin. And, finally, water uptake can be easily quantified and both diffusion coefficients and dimensional changes can be measured with less error than other common methods.

## **7. Acknowledgment**

Authors wish to thank Ministerio de Ciencia e Innovación (Spain) for partial funding under project MAT2010-17091.

## **8. References**

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The small volume changes due to swelling are prone to large errors if determined by usual means (for example, with a caliper). Figure 13 shows good correlations between the fractional volume change during water uptake in an epoxy resin as measured

gravimetrically, by FTIR or measuring the change on dimensions of the specimens.

Fig. 13. Comparison of volume change determined by n-FTIR, (V/V0)IR, and measured

The curing and ageing of epoxy resins are complex phenomena of the prime importance in industry. FTIR appears to be a valuable tool for both qualitative analysis and quantification of these processes. It has been shown how to extract relevant information from spectra to identify typical components of resins and hardeners. Following time variations of specific bands allows extracting relevant kinetic parameters to get more insight about the specific reaction mechanism of curing process. Inspection of subtle changes in baseline can be correlated with both, miscibilization or phase separation processes. Detailed analysis of OH bands allows extracting information about intermolecular interactions within the components of the resin. And, finally, water uptake can be easily quantified and both diffusion coefficients and

Authors wish to thank Ministerio de Ciencia e Innovación (Spain) for partial funding under

Bhargava, R.; Wang, S.Q.; Koenig, J.L. (1999). Studying polymer-dispersed liquid-crystal

formation by FTIR spectroscopy. 2. Phase separation and ordering. *Macromolecules,*

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**6. Conclusion**

**7. Acknowledgment**

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**14**

*Italy*

**Use of FTIR Analysis to Control the**

Liberata Guadagno1,2,\* and Marialuigia Raimondo1

*1Dipartimento di Ingegneria Industriale, Università di Salerno, Fisciano (SA)*

*Università di Salerno, Fisciano (SA)*

**Self-Healing Functionality of Epoxy Resins**

*2Nano-Mates – Research Centre for NANOMAterials and nanoTEchnology,*

In recent years polymer composites are increasingly used to replace the traditional metal alloys in structural applications, ranging from civil infrastructure to high performance vehicles such as racing cars and military aircraft. This popularity is due to their lower weight, as well as to a continuous improvement of their performance aided in recent years by nanotechnology. However, limited storage stability and reliability are critical for polymer composites designed for structural applications [1-4]. In fact, in service, they are subject to damage due to microcracks that are produced in the structure under the action of various kinds of stresses, for example: a) mechanical vibrations or various types of mechanical stresses, b) sudden temperature changes, c) irradiation by electromagnetic radiation causing direct or indirect rupture of chemical bonds (UV light, γ rays, etc.), d) intentional or inadvertent contact with chemical substances that adversely affect the structure, e) various factors which in combination can contribute to compromising the integrity of the structure. Internal damage is difficult to detect and, once developed, even more difficult to repair. This critical point is a real problem in the field of aeronautic vehicles. In fact, for large components, such as parts of primary structures, several non-destructive damage detection techniques have been developed including ultrasonic, infrared thermography, x-ray tomography, and computerized vibro-thermography. This technology has helped to detect damage but repair of this damage has been limited to reinforced patch bonding and/or bolting. Actually, durability and reliability are still problematic in the field of these structural materials; in fact, in order to achieve the mechanical strength required for many structural applications, highly cross-linked polymeric materials are necessary. The trade off for this gain in mechanical strength is that the resulting materials tend to be brittle and are

therefore more prone to developing cracks trough normal usage, ultimately failing.

In addition to conventional methods for damage detection, and common repair methods, there has recently been the development of self-healing composites which are expected to significantly extend the life of polymeric components by autonomically healing micro-cracks

**1. Introduction**

 \*

Corresponding Author

multifunctional aromatic amines. *Industrial and Engineering Chemistry Research,*  Vol.35, No. 3, (March 1996), pp. 963-972, ISSN 0888-5885.

## **Use of FTIR Analysis to Control the Self-Healing Functionality of Epoxy Resins**

Liberata Guadagno1,2,\* and Marialuigia Raimondo1

*1Dipartimento di Ingegneria Industriale, Università di Salerno, Fisciano (SA) 2Nano-Mates – Research Centre for NANOMAterials and nanoTEchnology, Università di Salerno, Fisciano (SA) Italy*

## **1. Introduction**

284 Infrared Spectroscopy – Materials Science, Engineering and Technology

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0079-6700.

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In recent years polymer composites are increasingly used to replace the traditional metal alloys in structural applications, ranging from civil infrastructure to high performance vehicles such as racing cars and military aircraft. This popularity is due to their lower weight, as well as to a continuous improvement of their performance aided in recent years by nanotechnology. However, limited storage stability and reliability are critical for polymer composites designed for structural applications [1-4]. In fact, in service, they are subject to damage due to microcracks that are produced in the structure under the action of various kinds of stresses, for example: a) mechanical vibrations or various types of mechanical stresses, b) sudden temperature changes, c) irradiation by electromagnetic radiation causing direct or indirect rupture of chemical bonds (UV light, γ rays, etc.), d) intentional or inadvertent contact with chemical substances that adversely affect the structure, e) various factors which in combination can contribute to compromising the integrity of the structure. Internal damage is difficult to detect and, once developed, even more difficult to repair. This critical point is a real problem in the field of aeronautic vehicles. In fact, for large components, such as parts of primary structures, several non-destructive damage detection techniques have been developed including ultrasonic, infrared thermography, x-ray tomography, and computerized vibro-thermography. This technology has helped to detect damage but repair of this damage has been limited to reinforced patch bonding and/or bolting. Actually, durability and reliability are still problematic in the field of these structural materials; in fact, in order to achieve the mechanical strength required for many structural applications, highly cross-linked polymeric materials are necessary. The trade off for this gain in mechanical strength is that the resulting materials tend to be brittle and are therefore more prone to developing cracks trough normal usage, ultimately failing.

In addition to conventional methods for damage detection, and common repair methods, there has recently been the development of self-healing composites which are expected to significantly extend the life of polymeric components by autonomically healing micro-cracks

<sup>\*</sup> Corresponding Author

Use of FTIR Analysis to Control the Self-Healing Functionality of Epoxy Resins 287

properties of the manufactured materials. Since 2003, a large number of parameters were investigated by the team from the University of Illinois and other research groups. In a recent paper, the dissolution properties, initial polymerization kinetics, chemical stabilities, and thermal stabilities were analyzed for three catalysts: Grubbs' first (G1) and second generation (G2) catalysts and Hoveyda–Grubbs' second generation catalyst (HG2) [30]. Ruthenium-based catalysts are reported as exhibiting great functional group tolerance, as well as greatly enhanced air and water stability [30,31]. However, thermolytic decomposition can limit the usefulness of these ruthenium systems in self-healing composites based on epoxy resins [32-33]. This is a crucial aspect for self-healing systems in aeronautic applications because, even if linked to the cost reduction from a process aspect, resins have been developed with low temperature manufacturing (under 100 °C), yet the

In fact, we generally need a glass transition temperature after wet aging of 110 °C minimum, and a curing temperature equal to or less than 100 °C is not enough. To achieve this goal it is necessary to make a post cure with a temperature that could be as high as 180 °C. For this reason, we have carried out our investigation in the temperature range of 150–180 °C. It is worth noting that there are critical issues in the use of epoxy precursors in conjunction with Grubbs metathesis catalysts, because in self healing composites based on epoxy resins, ruthenium systems give rise to a reaction with the oxirane rings of the epoxy precursors, and, therefore, the metathesis catalyst was not subsequently able to promote the polymerization of the reactive monomer, thus losing the self-healing ability. Such phenomena could strongly limit the use in the practice, in self-healing composite materials, of Grubbs' catalysts. In particular, in this chapter, we show that selecting the appropriate curing cycle as well as the specific chemical formulation, the catalyst remains intact in the formed epoxy matrix during the curing process, and is thus capable of subsequently performing its catalytic activity of the polymerization of the reactive monomer consisting in the cyclic olefin (5-ethylidene-2-norbornene –ENB-), when the latter comes out of a microcapsule affected by a crack. Studies on the choice of an appropriate curing cycle for a different self-healing formulation have already been reported in previous papers [32-35]. Another drawback to overcome in the employment of the ROMP catalysts is related to the local availability of the catalyst particles. In particular, the catalyst for the metathesis reaction is embedded in the precursors of the epoxy matrix in the form of solid particles, i.e. powders with different morphology and crystallographic modifications [30]. In practice, the effective concentration of the catalyst depends on the availability of the aforesaid particles at the level of the fracture and on the rate of dissolution of the catalyst in the reactive monomer (healing agent) within the polymer matrix. Even with high concentrations of catalyst particles exposed at the level of the fracture, the effective concentration of the catalyst could be relatively low because of limited rates of dissolution of the catalyst. The rate of dissolution of the catalyst depends not only on the chemical nature of the various components, but also on morphological and structural characteristics of the catalyst particles. It has been found in practice that the presence of the catalyst in the form of crystalline powders has some critical aspects relating to the uniform availability of the catalyst in all the zones in which a micro-crack can potentially develop, compromising the

Figure 1 illustrates as, independently from the catalyst amount, large crystals of catalyst particles can cause loss of catalytic activity in many zones. In addition, a very effective self-

problem of the material treatment at high temperature is not resolved.

effectiveness of the self-healing process [35].

whenever and wherever they develop [5-15]. For structural applications, self-healing systems are of great interest because they would allow to overcome not only some difficulties connected to damage diagnosis, but also the following appropriate interventions to restore the material functionality. Airlines for example see polymeric composites' potential to cut fuel costs and save on maintenance very attractive, therefore, are willing to entertain the idea to put into action self-healing composites in the development of different materials for aeronautical applications. The challenge facing materials scientists is to assure these systems must be able to stem fatigue damage and preserve their integrity, increase their life span, reduce maintenance costs and provide safety during use. A lot of strategies were formulated up to now in the development of self-healing materials [5,16–27].

One of the strategies to manufacture a thermosetting self-repair material seems to be the storage of healing agents inside composites that restore the strength of the materials after damage.

The first demonstration of self-healing in an engineered material, an epoxy matrix, occurred in 2001 [5] by a team from the University of Illinois (USA). This self-healing system for thermosetting materials is very interesting also in terms of design. The concept was based on the introduction of a microencapsulated healing agent and suspended catalyst phase in a polymer matrix. Since that time, advancement has been made in the field following this conceptual approach, while at the same time alternative concepts have emerged in the scientific literature. Microencapsulation and thermally reversible networks [28] are the two main strategies used for the development of self-healing thermosetting materials. Microencapsulation is the first and most studied self-healing concept. The initial self-healing epoxy system developed by White et al. involves the incorporation of a microencapsulated healing agent, dicyclopentadiene (DCPD) and a dispersed solid catalyst, bis(tricyclohexylphosphine) benzylidine ruthenium (IV) dichloride (called Grubbs' catalyst) in an epoxy-amine network. In these systems, an approaching crack ruptures embedded microcapsules releasing a polymerizer agent into the crack plane through capillary action. Polymerization of the healing agent is triggered by contact with the embedded catalyst, bonding the crack faces. In these systems the efficiency of self-repair function, in terms of trigger, speed and yield, is related to ring-opening metathesis polymerization of the healing agent by appropriate catalysts. The healing agent is a microencapsulated liquid monomer that must include a long shelf life, prompt deliverability, high reactivity, and low volume shrinkage upon polymerization [29]. The monomer most often used as the healing agent for the manufacture of these first ingenious systems is dicyclopentadiene (DCPD) [5,29]. Very recently, however, blends of DCPD/5-ethylidene-2-norbornene (DCPD/ENB) or DCPD/ 5 norbornene-2carboxylic acid have also been proposed [30]. Thermosetting auto-repair polymers, which have been proposed so far, include Grubbs' first-generation catalyst (G1); [5,17,29-30] and currently, the possibility of applying other ruthenium catalysts for ringopening metathesis polymerization-based self-healing applications is being evaluated. This system is a challenge for epoxy structural composites: however, some drawbacks have to be re-evaluated in order to be fully applied to advanced applications. These mainly regard the thermal stability of the Grubbs' catalyst inside the epoxy resin during the curing cycle and the impossibility to utilize primary amines as hardeners, since they can poison the catalyst.

This last drawback forces the use of compounds which have not been fully explored in literature as hardener agents, especially with regard to the cure behavior and mechanical

whenever and wherever they develop [5-15]. For structural applications, self-healing systems are of great interest because they would allow to overcome not only some difficulties connected to damage diagnosis, but also the following appropriate interventions to restore the material functionality. Airlines for example see polymeric composites' potential to cut fuel costs and save on maintenance very attractive, therefore, are willing to entertain the idea to put into action self-healing composites in the development of different materials for aeronautical applications. The challenge facing materials scientists is to assure these systems must be able to stem fatigue damage and preserve their integrity, increase their life span, reduce maintenance costs and provide safety during use. A lot of strategies

One of the strategies to manufacture a thermosetting self-repair material seems to be the storage of healing agents inside composites that restore the strength of the materials after

The first demonstration of self-healing in an engineered material, an epoxy matrix, occurred in 2001 [5] by a team from the University of Illinois (USA). This self-healing system for thermosetting materials is very interesting also in terms of design. The concept was based on the introduction of a microencapsulated healing agent and suspended catalyst phase in a polymer matrix. Since that time, advancement has been made in the field following this conceptual approach, while at the same time alternative concepts have emerged in the scientific literature. Microencapsulation and thermally reversible networks [28] are the two main strategies used for the development of self-healing thermosetting materials. Microencapsulation is the first and most studied self-healing concept. The initial self-healing epoxy system developed by White et al. involves the incorporation of a microencapsulated healing agent, dicyclopentadiene (DCPD) and a dispersed solid catalyst, bis(tricyclohexylphosphine) benzylidine ruthenium (IV) dichloride (called Grubbs' catalyst) in an epoxy-amine network. In these systems, an approaching crack ruptures embedded microcapsules releasing a polymerizer agent into the crack plane through capillary action. Polymerization of the healing agent is triggered by contact with the embedded catalyst, bonding the crack faces. In these systems the efficiency of self-repair function, in terms of trigger, speed and yield, is related to ring-opening metathesis polymerization of the healing agent by appropriate catalysts. The healing agent is a microencapsulated liquid monomer that must include a long shelf life, prompt deliverability, high reactivity, and low volume shrinkage upon polymerization [29]. The monomer most often used as the healing agent for the manufacture of these first ingenious systems is dicyclopentadiene (DCPD) [5,29]. Very recently, however, blends of DCPD/5-ethylidene-2-norbornene (DCPD/ENB) or DCPD/ 5 norbornene-2carboxylic acid have also been proposed [30]. Thermosetting auto-repair polymers, which have been proposed so far, include Grubbs' first-generation catalyst (G1); [5,17,29-30] and currently, the possibility of applying other ruthenium catalysts for ringopening metathesis polymerization-based self-healing applications is being evaluated. This system is a challenge for epoxy structural composites: however, some drawbacks have to be re-evaluated in order to be fully applied to advanced applications. These mainly regard the thermal stability of the Grubbs' catalyst inside the epoxy resin during the curing cycle and the impossibility to utilize primary amines as hardeners, since they can poison the catalyst. This last drawback forces the use of compounds which have not been fully explored in literature as hardener agents, especially with regard to the cure behavior and mechanical

were formulated up to now in the development of self-healing materials [5,16–27].

damage.