Characterization of Polyamide 66 Obturator 

Materials by Differential Scanning Calorimetry and 

Size-Exclusion Chromatography 

by Frederick L. Beyer, Eugene Napadensky, and Christopher R. Ziegler 

ARL-TR-3689 December 2005 

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Army Research Laboratory 

Aberdeen Proving Ground, MD 21005-5069 

ARL-TR-3689 December 2005 

Characterization of Polyamide 66 Obturator 

Materials by Differential Scanning Calorimetry and 

Size-Exclusion Chromatography 

Frederick L. Beyer and Eugene Napadensky 

Weapons and Materials Research Directorate, ARL 

Christopher R. Ziegler

University of Massachusetts, Amherst 

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Characterization of Polyamide 66 Obturator Materials by Differential Scanning 

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Frederick L. Beyer, Eugene Napadensky, and Christopher R. Ziegler*

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14. ABSTRACT 

Samples of two polyamide 6/6 materials used to make obturators were characterized by differential scanning calorimetry (DSC) 

and by size-exclusion chromatography (SEC). The two materials, commercially available DuPont Zytel 42A and Zytel 101, 

have been used in obturators, but an increase in undesired part failures occurred when Zytel 101 was replaced with the newer 

Zytel 42A. DSC analysis of these materials revealed very little variation in the nature of the semicrystalline domains, consistent 

with a previous analysis using x-ray diffraction. Molecular weight characterization by SEC, however, revealed that the Zytel 

101 samples as processed have molecular weights ~10% greater than that of the Zytel 42A samples. The change in molecular 

weight is reproducible, but contradicts previously collected SEC data from similar samples also from obturator specimens. One 

factor that is thought to be contributing to the change in molecular weight is the change in the annealing medium from mineral 

oil to dry nitrogen gas. The apparent variability and significant difference in molecular weight is concluded to be the likely

cause of the change in mechanical properties leading to the increased failure rate. 

15. SUBJECT TERMS

nylon 66, polyamide, obturator, DSC, SEC, GPC 

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19a. NAME OF RESPONSIBLE PERSON

Frederick L. Beyer 

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410-306-0893 

Standard Form 298 (Rev. 8/98) 

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iii

Contents 

List of Figures iv

List of Tables iv

Acknowledgments v

1. Introduction 1

2. Experimental 2

3. Results 6

4. Discussion 10

5. Conclusions 12

6. References 13 

Distribution List 15 
iv

List of Figures 

Figure 1. Z101 blank (A) with a large wedge (B) removed. Picture (C) shows a thin section 

from the wedge with sample locations 1–7 denoted..................................................................3 

Figure 2. SEC chromatograms showing changes in elution time as the trifluoroacetylated 

PA66 ages. .................................................................................................................................5 

Figure 3. Effect of aging on MW and peak area normalized to the first run..................................6 

Figure 4. An example of typical DSC data for PA66 Z101 (left) and Z42A (right) materials. 

As would be expected, the traces are nearly identical. ..............................................................7 

Figure 5. DSC melting endotherms observed for the Z101 samples. .............................................8 

Figure 6. DSC melting endotherms observed for the Z42A samples. ............................................9 

Figure 7. UV-SEC chromatograms of samples Z42A and Z101....................................................9 

List of Tables 

Table 1. SEC results from UV detector (254 nm). .......................................................................10 
v

Acknowledgments 

Funding for this study was provided by Mr. John Lutz, PM-MAS. The authors would like to 

acknowledge discussions with Mr. Peter Dehmer in which the effect of annealing media on 

molecular weight and mechanical properties was jointly developed. The efforts of Mr. Larry 

Holmes in manufacturing specimens as well as experimental setup were greatly appreciated. 

Mr. Ziegler was supported by an appointment to the Research Participation Program at the 

U.S. Army Research Laboratory (ARL) administered by the Oak Ridge Institute for Science and 

Education through an interagency agreement between the U.S. Department of Energy and ARL. 
vi

INTENTIONALLY LEFT BLANK. 
1

1. Introduction 

Nylon 6/6, or polyamide 6/6 (PA66), is a semicrystalline, thermoplastic commodity polymer that 

finds widespread use in applications that require considerable strength but low toughness 

(Kohan, 1973). One application of PA66 in U.S. Army systems is as an obturator in high-energy 

kinetic-penetrator rounds. In this application, the PA66 part serves a critical role in the firing of 

the projectile. The obturator provides the seal between the gun tube and the projectile, allowing 

the propellant to pressurize the tube behind the round, and guides the projectile smoothly down 

the barrel. When the round exits the gun tube, the sabots which guided the round down the tube 

must release the round. Pressure on the obturator from the sabots should cause it to immediately 

fail, allowing the sabots to separate from each other and release the projectile. Any failure of the 

obturator either prior to or significantly after the round exits the gun tube will have a detrimental 

effect on the performance to the round. 

The impetus for this study was a change in the failure behavior of PA66 obturators following a 

change in the stock material used and the manner in which the material was processed. The 

material was changed from DuPont Zytel 101 to Zytel 42A, and the annealing medium was 

changed from mineral oil to dry nitrogen gas. The polymer morphology, including crystalline 

phase, degree of crystallinity, and crystallite orientation, could be affected. The molecular 

weight averages and distribution may also be affected. These changes have the potential to have 

a dramatic impact on the physical behavior of the final part. Crystal structure and orientation 

was previously analyzed and described (Beyer and Ziegler, 2004). In this study, the molecular 

weight distribution and general variations in crystallinity have been characterized. 

The mechanical properties of PA66 can be dramatically influenced by the morphology of the 

final part, which is in turn influenced by the manufacturing and operating conditions. In the 

most stable PA66 crystalline structure, the triclinic α-phase, crystallites are comprised of stacks 

of crystalline sheets (Bunn and Garner, 1947; Cooper et al., 1998; Jones et al., 2000). The sheets 

are formed by individual PA66 molecules hydrogen-bonded in all-trans conformations. These 

sheets are not rectangular, but have a slight shear due to a progressive offset between adjacent 

PA66 chains. Adjacent sheets are also regularly and cumulatively offset, tilting 42° relative the 

lamellar plane, resulting in a “pleated” crystallite. The second crystalline phase found in PA66, 

the β-phase, is also triclinic and characterized by sheets that shear alternately in the c-direction, 

resulting in a 13° offset from the lamellar normal. A third, nonequilibrium crystal phase is 

observed in PA66 at temperatures near the melting point. The γ-phase, or pseudohexagonal 

phase, begins to form when PA66 is heated through the “Brill transition.” For PA66, the Brill 

transition temperature (TB) occurs between 170 °C and 220 °C, well below the melting 

temperature (Tm), which is in the range of 250 °C to 272 °C (Jones et al., 2000; Pfluger, 1975; 
2

Ramesh et al., 1994). Any change in crystal structure would be expected to have an effect on 

physical behaviors including toughness and tensile strength. 

The molecular weight (MW) distribution of a material will also have a significant impact on its 

mechanical properties (Kohan, 1973). The MW of nylons is often measured by testing relative 

viscosity. Increasing relative viscosity, which occurs with increasing MW, correlates with 

increasing impact toughness and is generally desirable. Increases in crystallinity also improve 

toughness by providing physical crosslinks. However, in both cases, there is some maximum 

MW beyond which the effects become detrimental. This maximum depends on the mechanical 

property, the breadth of the MW distribution, and the specific chemistry of the polymer. 

In this study, the two PA66 materials used in the obturators were both characterized by 

differential scanning calorimetry (DSC) and by size-exclusion chromatography (SEC). DSC 

allows the analysis of physical changes that affect the absorption and release of heat by the 

sample, such as melting and glass transitions. The nature and degree of crystallinity of a material 

may often be obtained from DSC analysis, supporting analysis by other methods. SEC analysis 

allows the characterization of the MW of the materials, which is a relatively unknown parameter 

in this particular case due to the in situ polymerization that occurs during extrusion and 

annealing of the obturator blanks. 

2. Experimental 

Samples of the two different commercially available nylon materials, DuPont Zytel 101 and 

Zytel 42A (Wilmington, DE), henceforth “Z101” and “Z42A,” were provided by Quadrant 

Engineering Plastics Products (Reading, PA) at two different stages of the obturator 

manufacturing process. Both samples were processed according to the recommendations from 

DuPont, although the exact processing conditions are proprietary. Both materials were extruded 

at temperatures in excess of 260 °C (500 °F) for several minutes and cooled in a temperature 

controlled post extrusion die line at a rate of a few in/min. The Z101 materials were then 

annealed in an industrial-grade mineral oil bath while the Z42A materials were annealed in a dry 

nitrogen atmosphere, both at ~232.2 °C (450 °F). The annealing time, including ramp up and 

cool-down time, was ~23 hr. The Z101 sample provided was a large, annealed hollow 

cylindrical blank. The Z101 blank had an outer diameter of ~5 in and an inner diameter of ~3 in. 

The Z42A sample was supplied as a fully machined obturator manufactured from a blank similar 

to the Z101 blank. 

To prepare samples for study, wedges were first cut from both the Z42A obturator and Z101 

blank using a Felker FRS-51 water-cooled saw (Olathe, KS). Figure 1 shows the geometry of 

the sections removed from the Z101 blank. Sections were collected in the same manner from the 

Z42A obturator provided. Water-cooled saws were used to minimize undesirable sample
3

Figure 1. Z101 blank (A) with a large wedge (B) removed. Picture (C) shows a thin 

section from the wedge with sample locations 1–7 denoted. 

heating during preparation. The wedges were then trimmed down to a smaller size so that the 

wedges fit inside the sample clamp for a low-speed Buehler Isomet 2000 water-cooled diamond 

saw (Lake Bluff, IL). Using a diamond blade and a cutting speed of ~100 rpm, slices 

<1 mm thick were taken from the wedges. This thickness was chosen to facilitate the X-ray 

diffraction analysis, described previously (Beyer and Ziegler, 2004). Multiple slices of Z101 and 

Z42A were collected in this manner. 

For DSC characterization, seven evenly spaced locations along the radial direction of each 

sample slice were marked, as shown in figure 1. Locations 1, 4, and 7 correspond to the inner 

surface, the center, and the outer radius of the obturator or blank, respectively. Samples cut from 

these locations are denoted by Z101-1, Z101-2, etc., indicating both the material and the radial 

position of the specimen. 

Samples weighing ~10 mg each were punched from the slices using a leather punch, weighed, 

and sealed in aluminum autosampler DSC pans for DSC analysis. DSC analysis was performed 

using a TA 2920 DSC (TA Instruments, New Castle, DE). The DSC instrument was calibrated 

using an Indium standard. The procedure for DSC characterization was adapted from PA66 

measurements performed by Khanna and Kuhn (1997). After loading each sample into 

aluminum autosampler pans and crimping the pans closed, a needle was used to create a small 

hole in the pan lid. The sample was then placed under vacuum at room temperature overnight to 

dry the sample. After drying, the pan was immediately put into the DSC for a second drying step 

in which the sample was heated from 25 to ~55 °C at a rate of 20 °C/min, held for 2 min, and 

then air-cooled to room temperature. The purpose of the second step was to remove additional 

water and to allow enthalpic relaxations in the amorphous regions of the polyamide that occur as 

a result of removing moisture during the initial drying step (Khanna and Kuhn, 1997). Khanna 

and Kuhn found that relaxation of amorphous material causes uncertainty in the baseline above 

Tg which can lead to incorrect interpretations of crystallinity. After the two drying steps were 

completed, the sample was heated from 0 to 300 °C at a rate of 20 °C/min and then allowed to 
4

air cool. Specific heat and melt temperature information was obtained through the TA 

Instruments data acquisition software. 

Determining MW of polyamides via SEC is not straight-forward because polyamides are 

difficult to dissolve in common organic solvents. Concentrated acids, phenol, and fluorinated 

alcohols are examples of solvents strong enough to dissolve these materials. Using these 

solvents in standard SEC equipment is very difficult, if not impossible, due to their corrosive 

properties and toxicity. However, by reacting polyamide with trifluoroacetic anhydride, one can 

disrupt the intermolecular hydrogen bonding to the point where the polymer will be soluble in 

common organic solvents, including tetrahydrofuran (THF), a solvent commonly used for SEC. 

This reaction (given in equation 1) was developed by Schuttenberg and Schulz (Jacobi et al., 

1980), and according to Weisskopf and Meyerhoff (1983) does not result in polymer 

degradation. 

R C N R

O

H

(CF3CO)2O

CH2Cl2

R C N R

O

CF3 C O

n n . (1)

To perform SEC, small pieces, 19–23 mg each, of both PA66 materials under investigation were 

cut from the thin slices cut for wide-angle x-ray scattering (WAXS). The samples were taken 

from the center of the slices since the edges showed some yellowing, often indicative of 

oxidative degradation. Each sample was placed in a small vial which was then sealed. Using a 

septum pierced with a syringe, the sealed vials were then purged for 10 min with dry nitrogen. 

One mL of dichloromethane and 0.1 mL of trifluoroacetic anhydride (~4 molar equivalents as 

compared to the amount of -NH groups) were then added to both vials. The samples and 

solvents, sealed in the vials and at room temperature, were stirred overnight, yielding a clear 

solution. Once clear solutions were available, the vials were opened and the liquids 

(dichloromethane, trifluoroacetic anhydride, and trifluoroacetic acid) were evaporated out by 

exposure to a warm bath (40–50 oC). The residue, N-trifluoroacetylated polyamide, was further 

dried using dry nitrogen gas, then redissolved in 1 mL of dichloromethane. These solutions were 

then diluted with 20 mL of THF resulting in solution concentrations of ~1 mg/mL. Each 

solution was injected into the SEC instrument for analysis after filtration through a 0.45-μm 

syringe filter. Each solution was prepared immediately prior to analysis in order to minimize 

aggregation effects and analyzed only twice to ensure that polymer recrystallization would not be 

an issue. 

SEC analyses were performed using a Waters SEC (Waters Corporation, Milford, MA) system 

composed of a Waters 717-plus autosampler (held at 40 oC), a Waters 510 pump, a Waters 486 

Tunable UV detector set to 254 nm, and a Waters 410 Refractive Index Detector held at 40 oC. 

Three columns, a Phenogel 5μ 105

 Å, a Phenogel 5μ 104 Å, and a Phenogel 5μ 103 Å 

(Phenomenex, Rancho Palos Verde, CA), each 300 × 7.8 mm, held at 40 oC, were used to 
5

separate MWs. The solvent used during this analysis was unstabilized HPLC-grade THF, 

pumped at a rate of 1 mL/min. Calibration was based on narrow MW polystyrene standards. 

The injection volume for the polyamides was 50 μL. For polystyrene standards, the injection 

volume was 100 μL due to lower concentration. 

An important issue with N-trifluoroacetylated polyamides is sample stability. Unless the 

solution is used immediately after preparation, significant changes occur that make MW analysis 

meaningless. To determine empirically the useful shelf life of the solutions prepared from the 

PA66 obturator samples, experiments were preformed to observe changes in consecutive SEC 

chromatograms as the a sample solution aged at 40 oC. The material used for this analysis was 

Nylon-6 (20 mg), prepared exactly as just previously described. “Solution age” refers to the time 

elapsed between the time the solution was made to its injection into the SEC instrument. 

Examining the overlay of those chromatograms (shown in figure 2), one can see that the 

retention time of the peak increases with increasing elapsed time. Increasing retention time 

corresponds to decreasing in molecular weight. Additionally, the area under the peak, which is 

proportional to amount of polymer detected, decreases, indicating the phenomenon is not simply 

a decrease in molecular weight due to a reversal of the reaction and loss of the CF3CO group. 

Such a reversal would likely produce only a shift in the peak position, not a large decrease in 

area. The observed shift and decrease in peak area is most likely caused by a decrease in the 

quantity of sample reaching the detector, and the missing part corresponds to the higher 

molecular weight portion of the polymer, as implied by the shape of the peaks. Since polymer 

solution recrystallizes in the solution within 24 hr (Jeon et al., 2004), it is reasonable to assume 

that the missing higher molecular weight portion of the polymer is forming an insoluble gel that 

is unable to pass through the SEC column packing. It is interesting to note that the 

polydispersity of the measured sample seems unaffected by the loss of the high MW fraction. 

18 20 22 24 26 28 30

0 hr

0.8 hr

2.2 hr

3.1 hr

3.9 hr

Retention time (min)

Figure 2. SEC chromatograms showing changes in elution time as the 

trifluoroacetylated PA66 ages.
6

For the purposes of this study, it is only important to note that the SEC results remain steady for 

enough time to allow at least two consecutive measurements of the same sample. Figure 3 

supports this conclusion, showing changes in the measured MW and peak area as the samples 

age, normalized to the data obtained for just-prepared solution (elapsed time = 0). Analyzing 

samples that are older than one hour would be inadvisable, a situation that was avoided by 

preparing solutions immediately prior to use. 

30

40

50

60

70

80

90

100

110

0.0 0.5 1.0 1.5 2.0 2.5 3.0 3.5 4.0

Sample age (hr)

Mw

Area

Figure 3. Effect of aging on MW and peak area normalized to the first run. 

3. Results 

Figure 4 shows examples of typical DSC data collected from PA66 materials Z42A and Z101. 

In general, DSC data for both PA66 materials Z42A and Z101 have a broad endotherm around 

~175 °C and a complex melting endotherm that begins at ~240 °C and ends at ~270 °C. The 

absence of a crystallization exotherm just above Tg indicates that there is little secondary 

crystallization occurring in the amorphous regions of the samples. This is expected due to the 

prolonged annealing regimen employed by the obturator manufacturer and the drying procedure 

used prior to DSC. 
7

-30

-25

-20

-15

-10

-5

0

Heat Flow (W/g)

0 50 100 150 200 250

Temperature (°C)

Z101-1

-30

-25

-20

-15

-10

-5

0

Heat Flow (W/g)

0 50 100 150 200 250

Temperature (°C)

Z42A-3

Figure 4. An example of typical DSC data for PA66 Z101 (left) and Z42A (right) materials. As 

would be expected, the traces are nearly identical. 

Figures 5 and 6 show the DSC data collected in the range of the melting endotherm for each of 

the seven sample locations for the Z101 and Z42A materials, respectively. The breadth of the 

melting endotherm reveals both α-phase melting and the effects of the Brill transition, in which 

α-phase crystalline regions transform into the metastable γ-phase (Ramesh et al., 1994; Zhang 

et al., 2003). What appeared to be one strong endotherm in figure 4 is actually a combination of 

separate endotherms at 249, 256, and 262 °C. Both materials, Z101 and Z42A, exhibit this 

behavior. The first peak, at 249 °C, is a result of the melting of α-phase crystallites (Hybart and 

Platt, 1967; Jones et al., 1997). The high heating rate (20 °C/min) prevents the complete 

transformation of the α-phase crystallites, around 40% of the bulk of the material (Beyer and 

Ziegler, 2004), into γ-phase. The two higher temperature peaks comprise a double melting 

endotherm which results from melting of two different forms of the γ-phase (Zhang et al., 2003). 

The first peak in the double melting endotherm, “γ1,” seen at 256 °C, is from melting of γ-phase 

crystallites that are weakly hydrogen bonded. The second peak in the double melting endotherm, 

“γ2,” which occurs at 262 °C, arises from melting of more strongly hydrogen-bonded γ-phase 

crystallites. 

The results obtained from the SEC analysis are given in figure 7. Both samples were evaluated 

based on the data collected from the ultraviolet (UV) detector (254 nm) rather than the refractive 

index detector due to significantly better signal-to-noise ratio. A slight but reproducible shift in 

retention times between samples can be observed. The stability of the samples is also confirmed; 

runs “a” were injected immediately after solution preparation, while runs “b” were injected at an 

elapsed time of 45 min, with no marked differences arising during that period of elapsed time. 

The calculated MWs derived from the SEC data are given in table 1. 
8

-60

-50

-40

-30

-20

-10

0

Heat Flow (W/g)

230 240 250 260 270 280

Temperature (°C)

1

2

3

4

5

6

7

1 - Z101-1

2 - Z101-2

3 - Z101-3

4 - Z101-4

5 - Z101-5

6 - Z101-6

7 - Z101-7

Figure 5. DSC melting endotherms observed for the Z101 samples. 
9

-60

-50

-40

-30

-20

-10

0

Heat Flow (W/g)

230 240 250 260 270 280

Temperature (°C)

2

3

4

5

6

7

1 - Z42A-1

2 - Z42A-2

3 - Z42A-3

4 - Z42A-4

5 - Z42A-5

6 - Z42A-6

7 - Z42A-7

1

Figure 6. DSC melting endotherms observed for the Z42A samples. 

15 16 17 18 19 20 21 22 23 24 25 26 27

Retention Time (min)

Z42A-a

Z42A-b

Z101-a

Z101-b

Figure 7. UV-SEC chromatograms of samples Z42A and Z101.
10

Table 1. SEC results from UV detector (254 nm). 

Sample Mn 

(g/mol) 

Mw

(g/mol) 

Mz 

(g/mol) 

PDI 

(Mw/Mn) 

Z42A 121,000 233,000 363,000 1.9 

Z101 131,000 253,000 390,000 1.9 

4. Discussion 

In the most general terms, the DSC data collected for both Z101 and Z42A materials can be 

described as very uniform. This is surely a result of the long annealing process applied to both 

samples during processing, so that even a large specimen like the blanks has many hours to 

equilibrate at the annealing temperature. Subtle variations, however, were observed and may 

correlate to very small differences in morphology within the parts. 

The PA66 Z101 DSC data, given in figure 5, show the overall uniformity that arises from the 

very long annealing process. However, a systematic change in the endothermic peak positions is 

observed with increasing sample number, or distance from the center of the part. Sample Z101-1 

shows a fairly strong α-phase melting peak, a strong γ1 peak, and a weaker γ2 peak for strongly 

hydrogen bonded γ-phase. These data are reasonable when viewed in the context of the earlier 

WAXS results which indicated minimal γ-phase content, where one would expect a large portion 

of the γ-phase content to be have formed rapidly, be poorly-organized, and thus weakly hydrogen 

bonded (Beyer and Ziegler, 2004). 

As the outer surface of the part is approached, the relative strengths and positions of the three 

endotherms vary somewhat. The α-phase melting endotherm stays generally constant until the 

outer surface is reached (sample Z101-7). The γ1 peak, however, stays relatively steady until the 

middle of the part is reached and then begins to shift to a slightly lower temperature and weaken 

in relative intensity. This weakening is to the benefit of the γ2 peak, which shifts to a higher 

temperature and becomes stronger as the outer surface of the part is reached. This behavior 

seems to indicate an increase in the amount of previously existing γ-phase content at the outer 

surface of the part. One would expect any γ-phase trapped during the sample cooling process to 

be more refined in structure, and thus of the stronger hydrogen-bonded type, than that which 

would form upon heating. Additionally, the shift to a lower temperature of the γ1 peak would be 

expected if more of the γ-phase is forming on and around the γ2 materials. However, the 

variations in the γ-phase melting endotherms are generally minor, and do not seem to indicate 

that the Z101 samples contain any significant γ-phase portion prior to heating. 

The data for the Z42A samples, shown in figure 6, are very similar overall to that for Z101. A 

weak endotherm corresponding to melting of α-phase crystallites is observed at ~250 °C. A 

strong γ1 endotherm is observed, corresponding to weakly hydrogen-bonded γ-phase crystallites 
11

formed during heating through TB. A weak γ2 peak is observed for all samples, indicating a 

relatively small fraction of more strongly hydrogen bonded γ-phase is present. Some variation in 

these three melting endotherms is observed, but no consistent trends are developed as they are 

for the Z101 materials. Samples Z42A-4 shows the most distinct difference from the other 

sections – a weaker and higher temperature γ1 endotherm – but in this case, this difference does 

not seem to be correlated with the γ2 endotherm, which appears generally weak for all samples. 

Analysis of the SEC data given in figure 7 revealed that the actual difference in MW between 

both samples is not large. The MW for Z101 was ~10% higher that that of Z42A. Polydispersity 

was found to be identical (~1.9). These data are the results of three separate measurements, 

which were consistent. It is important to note that the values given in table 1 are not exact 

because the measured MWs are increased by the addition of trifluoroacetate. The measurements 

were also made relative to PS standards, which introduces a slight error. 

More interesting is the observation that the data given in figure 7 and table 1 directly contradict 

similar, unpublished data collected by researchers at ATK Thiokol Propulsion on the same 

materials (Coleman, 2004). In that work, using the same SEC experimental techniques applied 

in this study, it was found that the MW was ~248.5 kg/mol for the Z101 material and 277 kg/mol 

for Z42A. The ATK researchers found that the MW averages of the Z42A samples exceeded 

those of the Z101 materials by ~11.6%, and an average polydispersity measurement was around 

2.9 to 3.0, vs. a PDI of 1.9 measured at the U.S. Army Research Laboratory (ARL). 

This dramatic difference may have come about in two ways. Human error may have resulted in 

mislabeled samples or errors in the sample characterization, although every effort was made to 

ensure correct sample labeling and rigorous adherence to characterization protocol to prevent 

such basic errors. In this case, though, at least a 10% difference in MW between the two 

different materials would remain, and the PDIs should be unchanged. Differences in 

instrumentation and calibration between the ATK and ARL instruments may have some effect on 

the absolute numbers. Another source of discrepancies could be a very large variation in the 

MW of the final parts. This idea is not necessarily unrealistic; the Zytel materials as provided by 

DuPont are not fully reacted and continue to polymerize during the extrusion and annealing 

process, affecting both MW and polydispersity of the PA66. It is not clear from this study if 

adequate processing controls were implemented to achieve reproducible MW distributions in 

either material or by either process. 

Regardless of the source of the discrepancies between the ARL and ATK SEC data, both data 

sets indicate that there is a significant difference of at least 10% in MW between the two 

materials. Controlling the MW of the materials is critical to controlling physical properties. A 

high MW clearly could embrittle a sample if it is near the upper limit of the range in which 

molecular entanglements and physical crosslinks due to crystallinity provide benefit, just as 

physical properties could be deleteriously affected by a decrease in molecular weight.
12

One final observation about controlling MW is the role of the annealing medium. The change to 

a dry nitrogen annealing atmosphere seems very likely to result in a higher molecular weight 

product simply based on the change in the equilibrium of the polycondensation reaction by 

which PA66 is made. By annealing in an atmosphere that would readily absorb water, the 

equilibrium of that reaction would be driven toward the product side of the reaction, increasing 

MW as water is removed from the reaction medium by the dry nitrogen gas. This effect would 

not occur for parts annealed in an oil bath, as the solubility of water in oil is minimal. 

5. Conclusions 

DSC data on the two PA66 materials, Z101 and Z42A, indicate that the samples are virtually 

indistinguishable with regard to thermal properties. Both materials have triple melting 

endotherms with nearly identical relative intensities of the three endotherms. Between the two 

materials, the samples of Z42A showed slightly more consistent thermal behavior while the 

samples taken from the Z101 part showed some variation in DSC. Specifically, for Z101, 

variations in the double endotherm for the γ-phase were observed, indicating the possibility of 

marginally higher γ-phase content near the outer surface of the part. 

More importantly, a 10% difference in MW was found between the Z101 and Z42A samples by 

SEC analysis, with the Z101 sample having the greater MW. This difference is significant, but is 

not easily explained because it contradicts data previously collected on what are thought to be 

the same materials. Researchers at ATK Thiokol Propulsion found that the Z42A samples had 

molecular weights ~12% greater than the Z101 samples. No error in sample characterization, 

preparation, or labeling could be found that explained this discrepancy. Regardless of the 

accuracy of either set of SEC data, such a change in MW is significant. More important is the 

idea that there may be a wide range of possible MWs, and thus mechanical properties, in parts 

made from these Zytel materials. 

Finally, the change in annealing conditions used for parts made from the two materials is likely 

to affect MW. Specifically, while the parts made from Z101 were annealed in an oil bath, those 

made from Z42A were annealed in a dry nitrogen atmosphere. The dry nitrogen would rapidly 

rob the parts of any water, a by-product of the polycondensation polymerization reaction that 

produces PA66, further increasing the MW of the material. This increase in MW could easily 

account for the difference in performance properties observed in the field. This idea contradicts 

the SEC data collected in this study, but is consistent with the results obtained by researchers at 

ATK.
13

6. References 

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Nylon 6 6 Obturator Materials; ARL-TR-3270; U.S. Army Research Laboratory: Aberdeen 

Proving Ground, MD, August 2004. 

Bunn, C. W.; Garner, E. V. The Crystal Structures of 2 Polyamides (Nylons). Proceedings of 

the Royal Society of London Series A-Mathematical and Physical Sciences 1947, 189 (1016); 

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Coleman, D. W. GPC Analysis of Nylon. ATK Alliant Techsystems, Brigham City, UT. Private 

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Cooper, S. J.; Atkins, E. D. T.; Hill, M. J. Temperature-Induced Changes in Lamellar Crystals 

of Monodisperse Nylon 6 and Nylon 6 6 Oligoamides, Macromolecules 1998, 31 (25); 

8947–8956. 

Hybart, F. J.; Platt, J. D. Melting of 66 Nylon - Observations by Differential Thermal Analysis. 

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Jacobi, E.; Schuttenberg, H.; Schulz, R. C. A New Method for Gel-Permeation Chromatography 

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Jeon, H. K.; Feist, B. J.; Koh, S. B.; Chang, K.; Macosko, C. W.; Dion, R. P. Reactively Formed 

Block and Graft Copolymers as Compatibilizers for Polyamide 66/PS Blends, Polymer 2004, 

45; 197–206. 

Jones, N. A.; Atkins, E. D. T.; Hill, M. J. Investigation of Solution-Crown, Chain-Folded 

Lamellar Crystals of the Even-Even Nylons 6 6, 8 6, 8 8, 10 6, 10 8, 10 10, 12 6, 12 8, 12 10, 

and 12 12. Journal of Polymer Science Part B-Polymer Physics 2000, 38 (9); 1209–1221. 

Jones, N. A.; Atkins, E. D. T.; Hill, M. J.; Cooper, S. J.; Franco, L. Chain-Folded Lamellar 

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and 

8 12. Polymer 1997, 38 (11); 2689–2699. 

Khanna, Y. P.; Kuhn, W. P. Measurement of Crystalline Index in Nylons by DSC: 

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Kohan, M. I. Nylon Plastics; Wiley: New York, NY, 1973. 
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Pfluger, R. Physical Constants of Nylon 6 and Nylon 66. In Polymer Handbook; Brandrup, J., 

Immergut, E. H., Eds.; John Wiley & Sons: New York, NY, 1975; V66–V79. 

Ramesh, C.; Keller, A.; Eltink, S. Studies on the Crystallization and Melting of Nylon 6,6 – 1. 

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