Authors:C. Bacharan, C. Dessaux, A. Bernès, and C. Lacabanne
Thermally Stimulated Current (TSC) spectrometry has been applied to the characterization of polymeric materials. The study
of a series of amorphous polymers having different physical structures has shown that the compensation parameters are independent
of physical aging; contrarily, the activation enthalpy distribution reflects the evolution of the heterogeneity of the amorphous
In copolymers, TSC allows us to identify segregated amorphous phases. In semi-crystalline polymers, with semi-rigid chains,
we have shown the existence of an amorphous crystalline interphase characterized by a plateau in the temperature distribution
of activation enthalpy.
Authors:G. Dlubek, A. Clarke, H. Fretwell, S. Dugdale, and M. Alam
Positron lifetime spectroscopy has been applied to estimate the free-volume hole size distribution in glassy polycarbonate (PC) and polystyrene (PS) as well as in plastically deformed and undeformed, semi-crystalline polyethylene (HDPE). The hole radius density distribution is determined from the ortho-positronium lifetime distribution which is obtained via a Laplace-inversion of the positron lifetime spectrum. The hole volume density distribution and the number density distribution of holes is estimated from the hole radius density distribution. In PC and in PS all of the distributions may be well approximated by a single Gaussian. The hole radius and the hole number density distributions have centres <r> and <vn> at 0.29 nm and 0.1 nm3 in PC, and at 0.28 nm and 0.09 nm3 in PS. The FWHM of the corresponding distributions are 0.042 nm and 0.040 nm3 (PC), and 0.039 nm and 0.34 nm3 (PS), respectively. Both, the shape and the width of the distributions correlate well with the free volume theory of BUECHE. In PE the lifetime spectra consist of four components. The o-Ps lifetime distribution is bimodal and may be attributed to o-Ps annihilation in the crystalline and in the amorphous phase of the polymer. The corresponding hole size distributions show definite changes of their position and width following plastic deformation which we attribute to homogeneous crystal lattice dilatation and/or a local disorder in the crystals and to an increase in the eccentricity of holes in the amorphous phase.
Annealing experiments have been carried out at a few degrees below the melting point of different polyethylenes (LDPE, LLDPE,
HDPE), of polypropylene (PP) and of Nylon-6. The heat capacities decrease during the annealing, within a 2-4 min time scale,
to a lower value which corresponds to the extrapolated heat capacity values obtained for the cooling cycle when the polymer
is cooled from the melt. Heat capacities in the heating cycle following the cooling cycle of PP, Nylon-6 and HDPE have the
same value as during the cooling section. This is not the case for LDPE and LLDPE.
Exothermic total heat flow in the cooling section following the annealing indicates that the crystallisation takes place during
the cooling rather than during the annealing period. The total melting enthalpy measured before and after the annealing cycle
is the same.
The reversing heat flow shows an excellent fit to the change of the crystallinity measured by small angle scattering of synchrotron
radiation during a heating cycle at temperatures below the melting peak.
A coupled thermodynamic interaction of the crystalline and the amorphous phases is concluded from this study. This kind of
interaction is possible at the lateral end of polymeric chains incorporated into the crystalline phase. This is an indication
of the portion of tie molecules in the system, i.e. the portion of fringed micelle type of crystalline morphology with respect
to that of folded chain lamellae.
This is a study for criteria to judge the melting point of semi-crystalline polymers from the DSC endotherm for polymer melting. Beyond standard indium DSC melting results an evaluation has been made on a series of polyethylenes for which crystal sizes were measured and predicted from Raman LAM analysis. The results confirm the conclusion of Prof. Wunderlich that the DSC content of melting is the proper basis of reporting melting points.
Authors:C. Schick, J. Dobbertin, M. Pötter, H. Dehne, A. Hensel, A. Wurm, A. Ghoneim, and S. Weyer
The relaxation strength at the glass transition for semi-crystalline polymers observed by different experimental methods shows
significant deviations from a simple two-phase model. Introduction of a rigid amorphous fraction, which is non-crystalline
but does not participate in the glass transition, allows a description of the relaxation behavior of such systems. The question
arises when does this amorphous material vitrify. Our measurements on PET identify no separate glass transition and no devitrification
over a broad temperature range. Measurements on a low molecular weight compound which partly crystallizes supports the idea
that vitrification of the rigid amorphous material occurs during formation of crystallites. The reason for vitrification is
the immobilization of co-operative motions due to the fixation of parts of the molecules in the crystallites. Local movements
(Β-relaxation) are only slightly influenced by the crystallites and occur in the whole non-crystalline fraction.
Sintering of polymeric powders is a peculiar characteristic of many processing technologies, including rotational moulding
and selective laser sintering (SLS). During polymer sintering, viscosity reduction in the melt state promotes densification
of polymer powders, through a double stage mechanism, involving powder coalescence and bubble removal. In particular, sintering
of semi-crystalline polymers is strongly influenced by the melting behaviour. Nevertheless, melting itself in absence of pressure
is not necessarily accompanied by powder sintering, unless low viscosities are achieved. In this work, the melting and sintering
behaviour of recycled high density polyethylene (rHDPE) have been analysed through differential scanning calorimetry (DSC)
and Thermomechanical Analysis (TMA). Efficient models capable of describing the melting temperature distribution and rate
of sintering of rHDPE powders have been developed, highlighting the inherent differences between the two distinct processes.
Authors:S. H. Murphy, G. A. Leeke, and M. J. Jenkins
The infrared spectrum of polycaprolactone has been recorded as a function of temperature in the range where melting and crystallisation of the polymer can occur. Examination of the carbonyl band of the spectra reveals a clear morphological sensitivity; heating the semi-crystalline polymer through the melting region results in a decrease in the intensity of the crystalline component of the carbonyl band. Accordingly, there was a subsequent increase in intensity of the crystalline carbonyl band on cooling. To enable comparison of these findings with a more conventional method of thermal analysis, similar experiments were conducted using a differential scanning calorimeter. The heated ATR accessory adopted for use in the FTIR spectrometer imposed significant limitations in the range of possible heating and cooling rates, but when these rates were carefully matched between FTIR and DSC, close correlation between the melting point and onset of re-crystallisation was observed. The results confirm that FTIR can be used as an alternative, if more laborious, way of investigating melting and re-crystallisation.
accomplishments, the most important ones were the creation and characterization of equilibrium crystals (extended chain crystals) of polyethylene, the discovery of the rigid amorphous phase in semi-crystallinepolymers, the precise measurement and publication of