Thermal aging of HTPB/IPDI-based polyurethane as a function of NCO/OH ratio

Thermal aging of HTPB/IPDI-based polyurethane as a function of NCO/OH ratio

Luciene Dias VillarI,^*; Thiago Cicaglioni^II; Milton Faria Diniz^I; Marta Ferreira Koyama Takahashi^I; Luis Cláudio Rezende^I

^IDivisão de Química, Instituto de Aeronáutica e Espaço,Departamento de Ciência e Tecnologia Aeroespacial – DCTA, Praça Marechal do Ar Eduardo Gomes, 50, São José dos Campos, SP, Brazil

^IIDepartamento de Engenharia Química, Escola da Engenharia de Lorena,Universidade de São Paulo, CP 116, Lorena, SP, Brazil

ABSTRACT

Thermal aging of hydroxy-terminated polybutadiene/isophorone diisocyanate (HTPB/IPDI)-based polyurethane was studied as a function of NCO/OH ratio (1.0 and 0.85). Samples were aged in air ovens at 50, 60, 65, and 70 ºC for periods of time from 1 to 34 weeks. Changes in chemical (swelling testing and FT-IR spectroscopy) and mechanical (tension testing and hardness) properties were evaluated throughout the aging assays. Correlation between equilibrium swelling ratio and elastic modulus, coupled with changes in FT-IR spectra, indicated oxidative cross-linking as the dominant mechanism for both molar ratios investigated. However, determination of Arrhenius activation energy resulted in values of (82 ± 10) kJ.mol^–1 and (156 ± 30) kJ.mol^–1 for 1.0 and 0.85 NCO/OH ratios, respectively, thus revealing faster oxidative degradation kinetics for higher urethane linkage networks.

Keywords: aging, HTPB, polyurethane

1. Introduction

Hydroxy-terminated polybutadiene (HTPB)-based polyurethanes are used in a wide range of applications, from sealants and coating materials to binders of solid rocket propellants. Propellant binders are obtained by cross-linking the terminal hydroxyl groups (OH) of HTPB prepolymer with di- or polyfunctional isocyanates (NCO), thus resulting in an elastomeric network, which can withstand the stress loading variations occurring from storage to ignition and flight¹.

Nevertheless, due to the unsaturated character of the repeated unit, polybutadiene is well-known to be sensitive to oxidation, even in the presence of stabilizers², thus resulting in hardening and embrittlement of HTPB-based polyurethanes, which are attributed to the cross-linkage through the double bonds of polybutadiene³. Therefore, depending on the environmental conditions, changes on mechanical properties of propellant binders may compromise the structural integrity of solid rockets, leading to service life constraints⁴.

Since the service life of rockets are largely dependent on the behavior of mechanical properties during aging, a formulation parameter such as NCO/OH ratio, which undoubtfully affects the mechanical properties^5,6, may also affect the aging behavior of solid propellant binders and, by doing so, the reliability of rocket systems. A study⁷ carried out for aging of sixteen HTPB/IPDI-composite propellants has found out that changes were faster when formulations were prepared with higher NCO/OH and triol/diol ratios. However, the remarks from this study are limited, once they have worked with a very narrow range of molar ratio (from 0.81 to 0.85).

This work analyzes the effect of NCO/OH molar ratio (1.0 and 0.85) on the aging behavior of chemical (swelling testing and FT‑IR spectroscopy) and mechanical (tension testing and hardness) properties of HTPB/IPDI-based polyurethanes.

2. Materials and Methods

2.1. HTPB/IPDI-based polyurethane

The polyurethane material was prepared from polymerization of HTPB (Petroflex S.A.) with IPDI (Veba Chemie A.G.) and addition of 0.012% w/w ferric acetylacetonate (Merck, Inc.) as catalyst. Sheets of 2 mm thickness were cast and cured for 1 week at 50 ºC. IPDI and HTPB were mixed into a 1.0 or 0.85 NCO/OH ratio, rendering F1 and F2 formulations, respectively.

2.2. Thermal aging assays

Thermal aging of the HTPB/IPDI-based elastomers were carried out in type IIB forced ventilation ovens (ASTM E145-94 (Reapproved 2006)) under atmospheric pressure and RH less than 20%. Aging conditions were set up by following ASTM D3045-92 (Reapproved 2003) recommendations. The first assay was carried out at 50, 60, and 70 ºC having withdraws after 0, 2, 8, 24, and 34 weeks of storage. An additional assay was designed with shorter periods of aging time (0, 1, 2, 3, 4, 6, and 8 weeks) at 60 and 65 ºC.

2.3. Mechanical testing

Dumbbell-shaped specimens were cut from the HTPB/IPDI 2 mm-sheets and assayed for uniaxial tension tests, according to ASTM D412-06a in a Zwick 1474 testing machine at (23 ± 2) ºC and a cross-head speed of 500 mm/min. Actual strain was measured with an optical extensometer. The initial modulus of elasticity (Young modulus) was defined as the secant modulus between 3 and 10 % of elongation. Hardness was measured in circular specimens with 7 mm thickness by using Zwick Shore A tester according to ASTM D2240- 05. All reported results of mechanical properties and hardness are averages of ten and five measured values, respectively.

2.4. Swelling testing

Swelling testing was performed gravimetrically⁸. Circular discs (10 mm in diameter, 2 mm-thickness, 0.3 to 0.4 g) were previously weighted and placed, in triplicate, into chloroform at room temperature until equilibrium was reached (7 days). The swollen sample disks were weighted (w₁) and placed to dry up to constant mass (w₂). Swelling ratio was calculated by following Equation 1^[8]:

where, q_v is the swelling ratio by volume, r₁ and r₂ are the densities at 25 ºC of the solvent (r₁ = 1.47 g.mL^–1 for chloroform) and of the polymer after swelling and drying, respectively. Density measurement of HTPB-elastomers relied on the Archimedes approach, by using the weight difference of an approximately 0.20 g-sample weighted in air and in distilled water.

2.5. FT-IR analysis

Fourier transform infrared spectra (FT-IR) were collected by using a PerkinElmer Spectrum One spectrometer equipped with an Universal Attenuated Total Reflectance (UATR) and an Attenuated Total Reflectance (ATR/Ge/45º) devices at: spectral range 4000‑700 cm^-1; 40 scans and 4 cm^-1 resolution. Samples aged at 70 ºC were analyzed at surface and core regions. Surface analysis was made without any previous treatment of samples. Core region was examined by slicing of the samples throughout their thickness.

3. Results and Discussion

3.1. Mechanical properties

Tensile strength and elongation at break, elastic modulus and hardness of unaged HTPB/IPDI-based elastomers for both formulations investigated are presented in Table 1. As it should be expected, the higher number of urethane linkages present in the binder prepared with stoichiometric NCO/OH ratio resulted in a remarkable increase in hardness and modulus, and a decrease in elongation. A less pronounced difference was observed in tensile strength.

The behavior of elastic modulus during thermal aging of the HTPB/IPDI polyurethanes is showed in Figure 1. Solid and open symbols are for long- (up to 34 weeks) and short-term (up to 8 weeks) assays, respectively. Since the mechanical tension testing was unable to be carried out for samples showing severe embrittlement, the latter assay was planned to fulfill the data required to better establish the aging behavior.

A general trend of modulus increase could be observed for both formulations at all the temperatures tested (Figure 1). A correspondent decrease in tension strength and elongation at break was observed (data not shown), thus revealing a markedly tendency of polyurethane hardening. A severe embrittlement was observed for F1-samples aged at 70 ºC for times longer than 2 weeks, whereas F2-samples showed a greater resistance by withstanding a period of 8 weeks before embrittlement was observed.

Table 2 presents the aging constant rate (k) obtained from the linear regression of elastic modulus and ln(t/t₀), as empirically proposed by Christiansen et al.⁹.

At temperatures from 50 to 65 ºC, aging rates resulted higher for stoichiometric HTPB/IPDI-formulation, as indicated by the ratio k_F1/k_F2(Table 2), meanwhile similar rates was observed at 70 ºC.In fact, the very few number of experimental data obtained at the higher aging temperature may have resulted in low accuracy of the calculated rates. In spite of that, the application of Arrhenius equation to determine the activation energy for HTPB-binder oxidation resulted in values of (82 ± 10) kJ.moL^–1 and (156 ± 30) kJ.moL^–1 for NCO/OH ratios of 1.0 and 0.85, respectively, with linear regression coefficients higher than 0.96 (data not shown).

The kinetic results presented herein indicate that the presence of a higher number of urethane linkages may accelerate the oxidation of HTPB-based polyurethanes. Although the present work was not able to point out any reasons for this finding, it is well known that a higher urethane group concentration lowers thermal stability of polyurethanes¹⁰.

3.2. Swelling ratio

Determination of density for dried HTPB/IPDI-based elastomers after equilibrium swelling testing resulted in r₂ values of (0.84 ± 0.05) and (0.90 ± 0.01) g.mL^–1 for F1- and F2- formulations, respectively. The binder formulation prepared with the lower NCO/OH ratio presented a volume swelling degree of 26.3 ± 0.1, against only 6.1 ± 0.1 for the other formulation, thus giving an indication of the great difference in cross-linking density between both elastomeric binders.

Figure 2 summarizes the changes in elastic modulus and equilibrium swelling ratio by volume for all the temperatures investigated during the aging assays. A noticeable exponential correlation between cross-linking increase and hardening of HTPB‑binder can be observed, thus confirming cross-linkage as the main mechanism of degradation for the tested material. Such mechanism was present in both formulations, although by the correlation showed in Figure 2, at higher NCO/OH ratio a small change in the swelling ratio may have a more pronounced effect on modulus, thus making the service life of the HTPB-binder to be shorter.

3.3. FT-IR analysis

Infrared spectra of HTPB/IPDI-based elastomers differing at NCO/OH ratio are presented in Figure 3 for the following conditions: a) surface of unaged sample; b) surface of aged sample at 70 ºC for 8 weeks; and c) core region of aged sample at 70 ºC for 8 weeks. Conditions (a) and (b) were examined by ATR/Ge/45º device, meanwhile condition (c) was examined by UATR device, due to the breakage of Germanium crystal during the analysis performance. Vibrational modes were indicated as follows: ν, for axial stretching; δ, for angular deformation; and ω, for wagging vibration.

Inspection of unaged spectra showed similar absorptions for both formulations (Figure 3a). Even the hydroxyl-free groups (νOH), assigned in the 3350-3400 cm^-1 region, and present in F2 due to excess amount of HTPB, were not possible to differentiate due to the presence of NH groups (νNH), which absorb in the same region (3357 cm^-1). It is worthwhile to mention that absorption bands at 1260 cm^-1 (δSiCH ₃) and 1083 cm^-1 (νSiOSi), observed at the surface of the samples (Figure 3a), were due to a polysiloxane-based contaminant used for mold releasing. After aging (Figure 3b), there was an intensification of these bands probably due to exudation of the absorbed contaminant.

Changes in the infrared spectra of 8-week aged samples analyzed at surface (Figure 3b) can be related to breakage of double bonds and to hydroxyl and carbonyl build-up. The breakage of double bonds was indicated through some loss of absorption of CH stretching bands (3100-2800 cm^-1), meanwhile CH wag bands at 994 and 911 cm^-1 (ωCH and ωCH₂vinyl); 965 cm^-1 (ωCH trans) and 725 cm^-1 (ωCH cis) suffered a drastic reduction. Although the presence of the νC = O band due to the urethane functional group significantly masks carbonyl build-up, the C = O stretching region showed a higher absorption, slightly more intense for F1-formulation, and an enlargement of the overlapping twin bands related to free and hydrogen bonded νC = O at 1725 and 1712 cm^-1, respectively. In addition, an increase in OH stretching absorption between 3600 and 3200 cm^-1, which was also more pronounced for F1-formulation, could be observed, and can be assigned to formation of alcohol or carboxylic acid groups. In fact, previous work² have showed that products from polybutadiene oxidation are mostly comprised by alcohols.

All the alterations reported above were not observed for the samples analyzed at the cross-sectioned face (Figure 3c), thus indicating that the oxidative cross-linking of HTPB-binders is limited by oxygen diffusion, as previously reported by other authors¹¹.

Infrared analysis of samples aged at 70 ºC for periods of time longer than 8 weeks showed the same behavior as presented in Figure 3 (data not shown), with spectra alterations being noticed only in the external surface.

4. Conclusions

The presence of a higher number of urethane linkages promoted by a higher NCO/OH ratio was found to accelerate the oxidation of HTPB/IPDI-based polyurethanes during thermal aging. Changes in chemical and mechanical properties have confirmed oxidative cross-linking as the main mechanism of HTPB-binder degradation.

Acknowledgments

Financial support from Agência Espacial Brasileira (AEB) is recognized. TC acknowledges CNPq for the undergraduate scholarship (PIBIC-IAE).

Received: March 16, 2011; Revised: July 8, 2011

• ¹
  Davenas A. Development of modern solid propellants. Journalof Propulsion and Power 2003; 19(6):1108-1128.  http://dx.doi.org/10.2514/2.6947
• ²
  Nagle DJ, Celina M, Llewellyn R and Fredericks PM. Infrared microspectroscopic study of the thermo-oxidative degradation of hydroxyl-terminated polybutadiene/isophorone diisocyanate polyurethane rubber. Polymer Degradation and Stability 2007; 92(8):1446-1454. http://dx.doi.org/10.1016/j.polymdegradstab.2007.05.010
• ³
  Akbas A, Aksoy S and Hasirci N. Effects of thermal ageing on the properties and lifetime prediction of hydroxyl-terminated polybutadiene. Polymer 1994; 35(12):2568-2572.  http://dx.doi.org/10.1016/0032- 3861(94)90380-8
• ⁴
  Dubois C and Perreault F. Shelf life prediction of propellants using a reaction severity index. Propellants, Explosives, Pyrotechnics 2002, 27(5):253‑261.  http://dx.doi.org/10.1002/1521-4087(200211)27:5%3C253::AID-PREP  253%3E3.0.CO;2-8
• ⁵
  Haska SB, Bayramli E, Pekel F and Ozkar S. Mechanical properties of HTPB-IPDI-based elastomers. Journal of Polymer Science 1997; 64(12):2347-2354.
• ⁶
  Manjari R, Joseph VC, Pandureng LP and Sriram T. Structure-property relationship of HTPB-based propellants. I. Effect of hydroxyl value of HTPB resin. Journal of Applied Polymer Science 1993; 48(2):271-278. http://dx.doi.org/10.1002/app.1993.070480211
• ⁷
  Hocaoglu O, Ozbelge T, Pekel F and Ozkar S. Aging of HTPB/AP-based solid propellants, depending on the NCO/OH and triol/diol ratios. Journal of Applied Polymer Science 2001; 79(6):959-964.  http://dx.doi.org/10.1002/1097-4628(20010207)79:6%3C959::AID-AP  P10%3E3.0.CO;2-G
• ⁸
  Eroglu MS. Characterization of the network structure of hydroxyl terminated poly(butadiene) elastomers prepared by different reactive systems. Journal of Applied Polymer Science 1998; 70(6):1129-1135.  http:// dx.doi.org/10.1002/(SICI)1097-4628(19981107)70:6%3C1129::AID-AP  P9%3E3.0.CO;2-Q
• ⁹
  Christiansen AG, Layton LH and Carpenter RL. HTPB propellant aging. Journal of Spacecraft and Rockets 1981; 18(3):211-215.  http://dx.doi.org/10.2514/3.57807
• ¹⁰
  Chattopadhyay DK and Webster DC. Thermal stability and flame retardancy of polyurethanes. Progress in Polymer Science 2009; 34(10):1068-1133.  http://dx.doi.org/10.1016/j.progpolymsci.2009.06.002
• ¹¹
  Ahlblad G, Reitberger T, Terselius B and Slenberg B. Thermal oxidation of hydroxyl-terminated polybutadiene rubber. II, Oxidation depth profiles studied by imaging chemiluminescence. Polymer Degradationand Stability 1999; 65(2):185-191.  http://dx.doi.org/10.1016/S0141- 3910(98)00178-5

Publication Dates

• Publication in this collection
  16 Sept 2011
• Date of issue
  Sept 2011