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Isothermal crystallization kinetics of poly(phenylene sulfide)/TLCP composites.


Blending thermotropic liquid crystalline polymers (TLCP TLCP Thermotropic Liquid Crystalline Polymer
TLCP Toxicity Characteristic Leaching Procedure
) with thermpoplastics permits the design of new high-performance composite materials with high strength and stiffness. During the composite processing, the mesogenic moieties of TLCPs promote high degree of molecular alignment, resulting in the formation of fibrillar fi·bril·lar or fi·bril·lar·y
1. Relating to a fibril.

2. Relating to the fine rapid contractions or twitchings of fibers or of small groups of fibers in skeletal or cardiac muscle.
 structure in the molten state. However, the long relaxation time relaxation time
n. Physics
The time required for an exponential variable to decrease to 1/e (0.368) of its initial value.

Noun 1.
 allows the orientation of the molecular chains to be frozen in the solid state, leading to the in situ In place. When something is "in situ," it is in its original location.  reinforcement of thermoplastics (1). This microstructure mi·cro·struc·ture  
The structure of an organism or object as revealed through microscopic examination.


a structure on a microscopic scale, such as that of a metal or a cell
 development has a strong influence on the overall crystallization Crystallization

The formation of a solid from a solution, melt, vapor, or a different solid phase. Crystallization from solution is an important industrial operation because of the large number of materials marketed as crystalline particles.
 kinetics kinetics: see dynamics.
Kinetics (classical mechanics)

That part of classical mechanics which deals with the relation between the motions of material bodies and the forces acting upon them.
 of thermoplastic/TLCP composites and mostly depend on the compatibility between the TLCP dispersed phase Noun 1. dispersed phase - (of colloids) a substance in the colloidal state
dispersed particles

phase, form - (physical chemistry) a distinct state of matter in a system; matter that is identical in chemical composition and physical state and separated from
 and thermoplastic A polymer material that turns to liquid when heated and becomes solid when cooled. There are more than 40 types of thermoplastics, including acrylic, polypropylene, polycarbonate and polyethylene.  in the molten and solid states. However, conflicting results were reported in the literature concerning the effects of TLCP on the crystallizability of crystalline thermoplastic in thermoplastic/TLCP composites (2), (3). It is reported that in some cases, the TLCPs act as nucleating sites for the growth of spherulites during crystallization process of thermoplastics (4-7), whereas on the other hand, some reports indicated that the TLCPs depress de·press
1. To lower in spirits; deject.

2. To cause to drop or sink; lower.

3. To press down.

4. To lessen the activity or force of something.
 the crystallization rate (3), (8), (9). Even though, apart from producing in situ fibril-microstructure composite and improving the composites processability, the TLCPs are still considered to be competitive with other fibrillar materials where the potential for accelerating the rate of crystallization is an essential requirement. An increased crystallization rate enhances the productivity and thus the current trend is to optimize the processing conditions for the shorter cycle times and high cooling rate (10). The subject is comprehensively reviewed by Tjong (11).

In isothermal i·so·ther·mal
Of, relating to, or indicating equal or constant temperatures.

isothermal, isothermic

having the same temperature.
 crystallization of polymer composites, it is assumed that the nuclei appear randomly in space, in supercooled melt, and subsequently grow at a constant rate in three dimensions. When the crystallization occurs below the melting point melting point, temperature at which a substance changes its state from solid to liquid. Under standard atmospheric pressure different pure crystalline solids will each melt at a different specific temperature; thus melting point is a characteristic of a substance and  of crystallizable crys·tal·lize also crys·tal·ize  
v. crys·tal·lized also crys·tal·ized, crys·tal·liz·ing also crys·tal·iz·ing, crys·tal·liz·es also crys·tal·iz·es
 matrix polymer in composite; the crytsallizable component, diffuses toward the crystal growth front. At such a situation the polymer transport, in fact the resulting morphological formations are kinetically controlled by thermal history and the composition. The majority of the theories proposed for this process are based on the Avrami treatment (12-14). Although the Avrami approach has many disadvantages, to large extent the n and k parameters can be used to interpret the nucleation nu·cle·a·tion
1. The beginning of chemical or physical changes at discrete points in a system, such as the formation of crystals in a liquid.

2. The formation of cell nuclei.
 mechanism and crystallization rate of the polymer, respectively. Avrami equation The Avrami equation describes how solids transform from one phase (state of matter) to another. It can specifically describe the kinetics of crystallisation, can be applied generally to other changes of phase in materials, like chemical reaction rates, and can even be meaningful in  describing kinetics of isothermal transformation Isothermal transformation diagrams (also known as time-temperature-transformation or TTT diagrams) are plots of temperature versus the logarithm of time, denoting the transformations of an austenitized alloy as it undergoes a heat treatment.  is valid and the effects of secondary crystallization are negligible. However, otherwise also the overall crystallization rates are not as simple to be interpreted as spherulitic spher·u·lite  
A small, usually spheroidal body consisting of radiating crystals, found in obsidian and other glassy lava rocks.

 radial growth due to the combination of nucleation and growth processes. In fact, the crystal growth process is controlled by the secondary nucleation. In this context, the kinetic theory of polymer crystallization by Hoffman et al. (15) allows to calculate the temperature dependence of the linear growth rate of the theoretically defined crystallization regimes incorporating the initial recognition of the importance of chain folding.

Poly(p-phenylene sulfide) (PPS (Packets Per Second) The measurement of activity in a local area network (LAN). In LANs such as Ethernet, Token Ring and FDDI, as well as the Internet, data is broken up and transmitted in packets (frames), each with a source and destination address. ), a semicrystalline polymer belongs to high-performance engineering thermoplastics class. Because of its chemical structure, composed of phenyl phenyl (fĕn`əl), C6H5, organic free radical or alkyl group derived from benzene by removing one hydrogen atom.  groups linked by a sulfur atom, it has excellent thermal, mechanical, and chemical properties. PPS has been widely used for applications in the aerospace, automotive, electric, and electronic industries. It can be reinforced with various fillers and fibers, thereby extending its property spectrum, suitable used in making injection molded components of complex shapes for engineering applications (16). Blending with TLCP, PPS produces a high-performance composite, with varying degree of overall crystallinity depending on blending conditions, and thereby modifying the composite morphology (17), (18). Also the TLCP might form fibril fibril /fi·bril/ (fi´bril) a minute fiber or filament.fibril´larfib´rillary

collagen fibrils
 morphology depending on the compatibility with PPS and its concentration in composite (19).

The crystallization behavior of neat PPS (20-28), of PPS filled with solid fillers (29-36), and PPS blended with different thermoplastic polymers (37-41) has been investigated extensively under isothermal and nonisothermal conditions. Similarly, during the last few years, a number of papers have been appeared in the literature, dealing with the effect of TLCPs on both isothermal and nonisothermal crystallization of PPS (5), (42-50) Minkova et al. (5) reported isothermal crystallization behavior of blend of PPS with the aromatic copoly(ester imide imide /im·ide/ (im´id) any compound containing the bivalent group, dbondNH, to which are attached only acid radicals.

) Vectra B950 (Hoechst-celanese, USA). They reported that the Vectra B950 strongly accelerates the isothermal crystallization, as a result of an increased nucleation density whereas no reduction of PPS degree of crystallinity was observed. These PPS/Vectra B950 blends were shown to be practically biphasic bi·pha·sic  
Having two distinct phases: a biphasic waveform; a biphasic response to a stimulus. 
 and immiscible immiscible /im·mis·ci·ble/ (i-mis´i-b'l) not susceptible to being mixed.

Incapable of being mixed or blended, as oil and water.
. In another study, on the isothermal and nonisothermal crystallization of blends of PPS and TLCP (HX4000-Du Pont), Gabellini and Bretas (49) observed increase in the overall crystallization rate and the dimensionality of the PPS crystalline morphology due to heterogeneous nucleation.

Previous studies of crystallization behavior of PPS/Vectra A950 are very scarce. Budgell and Day (50) studied the crystallization kinetics of PPS (Fortran and Ryton) blended with Vectra A950 (TLCP Hoechst). They found that Vectra A950 retards the Fortran crystallization but has very little effect on the Ryton PPS. These PPS/Vectra A950 blends are reported immiscible. No calculation of lateral ([sigma]) and fold surface interfacial free energies ([[sigma].sub.e]) are reported to correlate with these findings. Gopalkumar et al. (48) made an investigation of the morphology, mechanical, and thermal properties of uncompatibilized PPS/Vectra A950 blends. The reported thermal data indicate that in uncompatibilized PPS/TLCP blends the crystallization rate of PPS increases, as seen from a decrease in the supercooling Supercooling is the process of chilling a liquid below its freezing point, without it becoming solid. Description
A liquid below its freezing point will crystallize in the presence of a seed crystal or nucleus around which a crystal structure can form.
 ([DELTA][T.sub.c] = [T.sub.m] - [T.sub.c]) of PPS in blends decreased significantly when compared with pure PPS.

With the purpose of establishing the basis for the structure-physical property relationship of the melt blended thermoplastic/TLCP blends in this first part of the study with a large effort, we thoroughly investigated the isothermal crystallization kinetics of a composite system containing poly(phenylene phen·yl·ene  
A bivalent organic radical, C6H4, derived from benzene by removal of two hydrogen atoms.


The radical C6H4
 sulfide)(PPS), a high-performance engineering thermoplastic and a liquid crystalline polymer--Vectra A950. In this study, we report the crystallization kinetics of PPS in PPS/TLCP composite as a function of crystallization temperature and composite composition and analyzed by the Avrami theory. Thermal analysis Thermal analysis is a branch of materials science where the properties of materials are studied as they change with temperature. Techniques include:
  • Differential scanning calorimetry
  • Dynamic mechanical analysis
  • Thermomechanical analysis
 by differential scanning calorimeter calorimeter: see calorimetry.

Device for measuring heat produced during a mechanical, electrical, or chemical reaction and for calculating the heat capacity of materials.
 (DSC (1) (Digital Signal Controller) A microcontroller and DSP combined on the same chip. It adds the interrupt-driven capabilities normally associated with a microcontroller to a DSP, which typically functions as a continuous process. See microcontroller and DSP. ) is employed to study the melting and crystallization behavior of PPS. The spherulitic growth rate is calculated using isothermal crystallization DSC data. The molecular thermodynamic ther·mo·dy·nam·ic
1. Characteristic of or resulting from the conversion of heat into other forms of energy.

2. Of or relating to thermodynamics.
 parameters which control the crystalline growth of PPS in PPS/TLCP composites have been discussed. In this work, attention is also focused on the isothermal crystallization processes of these composites from the melt in order to analyze the effect of the concentration of TLCP on the morphological changes particularly on the growth of PPS crystals. For the first time in this article, the influence of TLCP blending on crystalline regime transition temperatures of PPS proposed by Hoffmann et al. will be reported. The results should be particularly interesting for the comprehension of crystallization behavior of PPS in PPS/TLCP composites to achieve the tailor-made properties.



Poly (phenylene sulfide) (PPS) (d = 1.360) used in this investigation was procured (Lot. No. 08115EZ) from M/S M/S Meter(s) per Second
M/S Milestone
M/S Modeling and Simulation
M/S Master/Slave
M/S Messieurs (plural of Mister)
M/S Minesweeping
M/S miles per second
M/S Miniature Sheet
 Aldrich Chemical Company, Milwaukee, Wl. The melting temperature Melting temperature may refer to:
  • Melting temperature, the temperature at which a substance changes from solid to liquid state.
  • DNA melting temperature, the temperature at which a DNA double helix dissociates into single strands.
 ([T.sub.m]) observed from DSC of PPS is 557 K. The TLCP used here is a Vectra A950 (TLCP), a commercial product, supplied by Polyplastic, Japan. This TLCP is a semicrystalline random aromatic copolyester of 4-hydoxy benzoic acid benzoic acid (bĕnzō`ĭk), C6H5CO2H, crystalline solid organic acid that melts at 122°C; and boils at 249°C;. It is the simplest aromatic carboxylic acid (see aryl group and carboxyl group).  (HBA) and 2-hydroxy-6-naphthoic acid (HNA HNA Hereditary Neuralgic Amyotrophy
HNA Hawaii Nurses Association
HNA High North Alliance
HNA Morioka, Japan - Hanamaki (Airport Code)
HNA Hospice Nurses Association (now Hospice and Palliative Nurses Association) 
) with a monomer monomer (mŏn`əmər): see polymer.

Molecule of any of a class of mostly organic compounds that can react with other molecules of the same or other compounds to form very large molecules (polymers).
 ratio of 73/27. The melting point ([T.sub.m]) of the as-received TLCP granules Granules
Small packets of reactive chemicals stored within cells.

Mentioned in: Allergic Rhinitis, Allergies
 is 557 K. The TLCP forms a nematic The stage between a crystal and a liquid that has a threadlike nature; for example, a liquid crystal. See crystalline and LCD.  melt above this temperature.

Composite Preparation

PPS and TLCP were dried at 373 K for 4 h in air circulating oven and stored in a dry environment before melt blending. A wide range of PPS/TLCP compositions 100/00, 90/10, 80/20, 70/30, 60/40, and 50/50 were prepared by melt compounding in a Haake (Rheomix 600) internal mixer at the co-screw temperature of 583 K with rotor speed 50 rpm. Blending was carried out for 5 min until the torque was stabilized. The composites were recovered in an air and allowed to solidify at room temperature.

Differential Scanning Calorimetry Differential scanning calorimetry or DSC is a thermoanalytical technique in which the difference in the amount of heat required to increase the temperature of a sample and reference are measured as a function of temperature.  Measurements

A DSC (Perkin-Elmer, DSC-7) operating on a UNIX UNIX

Operating system for digital computers, developed by Ken Thompson of Bell Laboratories in 1969. It was initially designed for a single user (the name was a pun on the earlier operating system Multics).
 platform was used to record isothermal crystallization exotherms and subsequent melting endotherms of neat PPS and PPS/TLCP composites. The DSC was calibrated cal·i·brate  
tr.v. cal·i·brat·ed, cal·i·brat·ing, cal·i·brates
1. To check, adjust, or determine by comparison with a standard (the graduations of a quantitative measuring instrument):
 using an Indium indium (ĭn`dēəm), a metallic chemical element; symbol In; at. no. 49; at. wt. 114.82; m.p. 156.6°C;; b.p. about 2,080°C;; sp. gr. 7.31 at 20°C;; valence +1, +2, or +3.  standard (melting temperature [T.sub.m] = 429.4 K and enthalpy of fusion The enthalpy of fusion (symbol: ), also known as the heat of fusion or specific melting heat  = 28.884 X [10.sup.-3] J [kg.sup.-1] to ensure accuracy of the data obtained. The sample mass was kept constant (9.000 [+ or -] 0.001 mg of PPS/TLCP) throughout the study for high reproducibility and used only once. Additional empty aluminium pan lids were placed in reference compartment as means of improving the thermal response. All the thermograms were obtained under nitrogen atmosphere to prevent thermal degradation.

For isothermal crystallization studies, each sample was heated from 323 K at a heating rate of 10 K [min.sup.-1] to a melt annealing temperature, 583 K. The sample was then held for 5 min to ensure complete melting and to eliminate residual anisotropy anisotropy /an·isot·ro·py/ (an?i-sot´rah-pe) the quality of being anisotropic.
anisotropy (an´āsôt´r
. Subsequently, each sample was rapidly cooled at the rate of 160 K [min.sup.-1] to the isothermal crystallization temperature ([T.sub.c]) of interest 523, 525, 528, 531, and 533 K. The sample was held at desired isothermal temperature for the completion of the crystallization process till no change in the heat flow as a function of time was further observed. It is then possible to monitor the resulting crystallization of sample as a function of time. The isothermal crystallization exotherms and subsequent melting endotherms at the heating rate of 10 K [min.sup.-1] were recorded. The weight fraction of crystalline material at a specific time, i.e., the ratio of the area under the isotherm isotherm, line drawn on a map of a particular region of the earth's surface connecting points of equal temperature; each point reflects one temperature reading or an average of several readings over a period of time.  at time t to the total area was calculated for each isothermal crystallization using DSC 7 kinetic software. The kinetics of isothermal crystallization process was carried out by directly fitting the experimental data to the macrokinetic Avrami model.

Optical Microscopy

The morphology development of spherulites, which appears as bright areas under polarized A one-way direction of a signal or the molecules within a material pointing in one direction.  light in the dark background of neat PPS and PPS/TLCP composites was observed under cross polarizers using a Leica Laborlux 12 Pol S polar light microscope Noun 1. light microscope - microscope consisting of an optical instrument that magnifies the image of an object
binocular microscope - a light microscope adapted to the use of both eyes
. The photomicrographs were taken with a Canon Powershot The PowerShot products are a line of consumer grade digital cameras, launched by Canon in 1995. The PowerShot line has been successful for Canon, and is one of the best-selling digital camera lines worldwide.  S 50 digital camera.

Analysis of the morphology was performed closely to the same conditions as experienced by samples during crystallization in the DSC experiments. As the nucleation density of PPS was very high, extra thin films of neat PPS and PPS/TLCP composites were prepared by melt pressing at 583 K between a glass slide and a cover slip and holding it at this temperature for 5 min to ensure complete melting. The microslide was then transferred to the hot stage held at the desired isothermal crystallization temperature. The system allowed the microslide to reach desired temperature in 15-20 sec, giving an average cooling rate 160 K [min.sup.-1], similar to the same as used with DSC. The sizes of the growing spherulites were determined by plotting their radius as a function of time and then calculating the slope of the best fit straight line.

Scanning Electron Microscopy electron microscopy

Technique that allows examination of samples too small to be seen with a light microscope. Electron beams have much smaller wavelengths than visible light and hence higher resolving power.

To observe phase behavior of PPS and PPS/TLCP composites, the morphology features of the cryogenically fractured surfaces of the PPS/TLCP composites were investigated using JEOL JEOL Japan Electron Optics Laboratory  JSM JSM Journal of Sexual Medicine
JSM Just Shoot Me (sitcom)
JSM Journal of Sport Management
JSM Journal of Software Maintenance
JSM Jabber Session Manager
JSM John Sidney McCain
JSM JEOL Scanning Microscope
 6380 LA analytical scanning electron microscope scan·ning electron microscope
n. Abbr. SEM
An electron microscope that forms a three-dimensional image on a cathode-ray tube by moving a beam of focused electrons across an object and reading both the electrons scattered by the object and
 (SEM), applying 20 kV accelerating voltage. The samples were prepared by dipping the samples in liquid nitrogen Noun 1. liquid nitrogen - nitrogen in a liquid state
atomic number 7, N, nitrogen - a common nonmetallic element that is normally a colorless odorless tasteless inert diatomic gas; constitutes 78 percent of the atmosphere by volume; a constituent of all living
 for 5 min and then breaking. An SPI (1) (Stateful Packet Inspection) See stateful inspection.

(2) (Service Provider Interface) The programming interface for developing Windows drivers under WOSA.
 sputter coater (JEOL JFC-1600 auto fine coater) was used to coat these fractured surfaces with gold for enhanced conductivity.


Miscibility miscibility (miˈ·s·biˑ·l  of PPS/TLCP Composites

The examination of glass transition temperature The glass transition temperature is the temperature below which the physical properties of amorphous materials vary in a manner similar to those of a solid phase (glassy state), and above which amorphous materials behave like liquids (rubbery state).  ([T.sub.g]) values of PPS in composites (Table 1) suggests that blending TLCP has a little effect on temperatures. The ([T.sub.g]) values in general slightly decrease from 366 K for pure PPS to 361 K for PPS in PPS/TLCP 60/40 composites These results indicate that TLCP is not miscible miscible /mis·ci·ble/ (mis´i-b'l) able to be mixed.

Capable of being and remaining mixed in all proportions. Used of liquids.
 in present case with PPS but acts as a diluent diluent /dil·u·ent/ (dil´oo-int)
1. causing dilution.

2. an agent that dilutes or renders less potent or irritant.

Serving to dilute.

 (plasticizer) in composites. Further in support of this immiscibility im·mis·ci·ble  
That cannot undergo mixing or blending: immiscible elements.

 of two components in PPS/TLCP composites, the morphology study of these composites was also carried out employing SEM. The fractures of the PPS/TLCP composites (90/10, 70/30, and 50/50 compositions) presented in Fig. 1 clearly indicates the immiscibility of two components in composites. In all the composite samples, well-segregated spherical TLCP-particles of the minor component phase are observed. The boundaries of the TLCP-particles are well defined and dispersed in the PPS-matrix, with some observed spherical voids due to detachment of the TLCP-particles during the cryo-fracture process. This also indicates the weak adhesion at interface between TLCP-domain and PPS-matrix. It is also observed that domain size increases (from 6 /[micro] in 90/10 to 11 [micro]m in 70/30 and then to 23, [micro]m in 50/50 composition) with increasing its concentration in composites. Such an observed macrophase separation supports to immiscibility and may steer the high interfacial tension Noun 1. interfacial tension - surface tension at the surface separating two non-miscible liquids
interfacial surface tension

surface tension - a phenomenon at the surface of a liquid caused by intermolecular forces
 occurring between PPS and TLCP during melt mixing process.

TABLE 1. Melting behavior of PPS/TLCP composites.

                                         Melting peak
                                        ([T.sub.m]) K

PPS/TLCP  [T.sub.g] (K)  [T.sub.c] (K)      I    II

 100/00        366            523          534  556
                              525          534  558
                              528          536  560
                              531          539  559
                              533          543  560
 90/10         358            523          534  556
                              525          533  557
                              528          536  558
                              531          539  560
                              533          544  560
 80/20         363            523          534  548
                              525          533  557
                              528          539  557
                              531          539  559
                              533          544  559
 70/30         357            523          536  554
                              525          534  557
                              528          540  557
                              531          539  559
                              533          544  559
 60/40         361            523          534  548
                              525          533  557
                              528          539  557
                              531          539  559
                              533          544  559
 50/50         363            523          536  554
                              525          534  557
                              528          540  557
                              531          539  559
                              533          544  559

           Heat of fusion        Heat of
             [DELTA]H        crystallization        [x.sub.c]
            [DELTA]H X     [[DELTA]H.sub.c] X       ([[DELTA]
            [10.sup.-3]        [10.sup.-3]           H.sub.c]
PPS/TLCP  (J. [kg.sup.-1]    (J [kg.sup.-1])    /[[DELTA]H.sub.l])

               I  II

 100/00        4  31               18                   0.22
               2  38               37                   0.46
               3  38               40                   0.50
               3  37               36                   0.45
               4  27               21                   0.26
 90/10         3  31               21                   0.26
               3  35               33                   0.41
               3  33               34                   0.42
               3  33               13                   0.42
               3  23               21                   0.16
 80/20         2  18               14                   0.17
               2  23               29                   0.36
               2  16               30                   0.37
               2  21               26                   0.33
               3  11               11                   0.14
 70/30         2  12               14                   0.18
               2  19               24                   0.30
               2  11               26                   0.32
               2  17               24                   0.30
               2  10               10                   0.13
 60/40         2  18               10                   0.12
               2  23               22                   0.27
               2  16                7                   0.09
               2  21               17                   0.21
               3  11                6                   0.08
 50/50         2  12                6                   0.07
               2  19               17                   0.21
               2  11                5                   0.06
               2  17               15                   0.19
               2  10                6                   0.07

Melting Behavior

PPS displays multiple melting peaks when scanned in DSC. The studies of Chung and Cebe (51) conversely indicated that the multiple melting behaviors and the dependence of melting temperature are a function of degree of crystal perfection, which depends on the degree of under cooling during crystallization. They attributed this behavior to the function of a broad distribution of crystals and thus the multiple peaks are due to the melting of two types of crystal populations formed during the entire crystallization process at [T.sub.c].

In this investigation, after completion of isothermal crystallization at [T.sub.c] = 523, 525, 528, 531, and 533 K, the samples were subjected to heating directly from [T.sub.c] to 573 K with a heating rate of 10 K [min.sup.-1]. The melting temperatures [T.sub.m] were obtained from peak temperatures of endo-therms. Figure 2 show the DSC heating curves of PPS and PPS/TLCP blends composed of a dominant upper main melting peak and a significant but broad lower premelting peak, after completion of isothermal crystallization at various [T.sub.c]. The data on the melting behavior of the blends are summarized in Table 1. From Fig. 2, it can be noted that in the main melting region of PPS, these two endothermic endothermic /en·do·ther·mic/ (-ther´mik) characterized by or accompanied by the absorption of heat.

en·do·ther·mic or en·do·ther·mal
 peaks are observed in the range of 528-552 K ([T.sub.m](I))and 541-564 K ([T.sub.m](II)). The positions of ([T.sub.m](I)) and ([T.sub.m](II)) are relatively constant for particular [T.sub.c] even with increasing TLCP loading in composites. The first melting peak ([T.sub.m](I)) is almost an appreciable endotherm endotherm

So-called warm-blooded animals; that is, those that maintain a constant body temperature independent of the environment. The endotherms include the birds and mammals.
 by about 281 K above the crystallization temperatures. The intensity is relatively small and further decreases with decreasing PPS contents in the blends. The second melting peak ([T.sub.m](II)) shows sharp dependence on the [T.sub.c], being associated with the fusion of crystals grown at [T.sub.c]. Both the area and the position of this second endotherm increase with [T.sub.c]. However, the intensity of ([T.sub.m](II)) decreases with increasing TLCP content.


Depending upon the degree of undercooling [T.sub.c], the bimodal bi·mod·al  
1. Having or exhibiting two contrasting modes or forms: "American supermarket shopping shows bimodal behavior
 melting behavior of PPS in PPS/TLCP blends in the present case is attributed to the existence of the preformed imperfect PPS crystal populations because of rapid nucleation from the state of low mobility formed by reorganization and then by remelting during DSC scans (51). The first [T.sub.m](I) endotherm can then be due to the melting of the imperfect infilling lamellae lamellae
n the nearly parallel layers of bone tissue found in compact bone.
 (out of secondary crystallization) between the more perfect crystal structures, existing before DSC scanning. The second main melting endotherm [T.sub.m](II) can be assigned to the melting of the comparatively more perfect primary lamellae structures formed by a primary crystallization, which partly melted and recrystallized during DSC scanning. On increasing the crystallization temperatures [T.sub.c] from 523 to 533 K, the onset as well as completion temperatures of [T.sub.m](I) and [T.sub.m](II) endotherms marginally shift toward higher temperatures. The experimental data show that PPS crystals formed over present range (523-533 K) of crystallization temperature are subject to dominating melting process of reorganization and then remelting. Thus the crystal structure and overall morphology in melting PPS/TLCP blends are still in the reorganization domain. This process, however, involves in crystal perfection and crystal thickening.

The melting temperature of a perfect crystal formed by infinite molecular weight chains, understood as an equilibrium melting temperature ([T.sub.m.sup.0]), is determined by the Hoffmann-Weeks relationship (52). A general method of determining ([T.sub.m.sup.0]) involves the construction of a Hoffmann-Weeks plot. To provide a more reliable database in this work, the experimentally determined extrapolated onset melting temperature for each blend composition was used for the determination of ([T.sub.m.sup.0]). The advantage of using onset temperature rather than melting peak temperature is well reflected by the better values of average correlative Having a reciprocal relationship in that the existence of one relationship normally implies the existence of the other.

Mother and child, and duty and claim, are correlative terms.
 coefficient of plots (53), (54). Assuming chain folding during crystallization, the dependence of the apparent melting temperature, [T.sub.m], on the crystallization temperature, [T.sub.c], is given by the following Hoffmann-Weeks equation:

[T.sub.m] = [T.sub.m.sup.0] (1 - 1/[beta]) + [T.sub.c]/[beta] (1)

where [T.sub.m] is the experimental onset melting temperature, [T.sub.c] is the crystallization temperature and [beta] is a factor that depends on the final lamellar lamellar /la·mel·lar/ (lah-mel´ar)
1. pertaining to or resembling lamellae.

2. lamellated (1).


pertaining to or emanating from lamella.
 thickness, which in fact describes the growth of lamellar thickness during crystallization. It is assumed that [beta] = l/l* where l and l* are the thicknesses of fully grown mature crystallite crys·tal·lite  
Any of numerous minute rudimentary, crystalline bodies of unknown composition found in glassy igneous rocks.

 and of the critical crystalline nucleus, respectively. As the crystallization temperature range chosen for present experiments is narrow, [beta] is taken as a constant equal to or greater than one (55). The [T.sub.m] vs. [T.sub.c] representative plot for pure PPS and PPS/TLCP 60/40 composition are shown in Fig. 3. [T.sub.m.sup.0] is obtained from the intersect In a relational database, to match two files and produce a third file with records that are common in both. For example, intersecting an American file and a programmer file would yield American programmers.  point of [T.sub.m] = [T.sub.c] line with the extrapolated [T.sub.m] vs. [T.sub.c] line .The [T.sub.m.sup.0] and [beta] values for all compositions are reported in Table 2. The extrapolated [T.sub.m.sup.0] value for pure PPS in present case is 579 K, which is similar to those previously reported (24). As far as PPS/TLCP composites are concerned, the [T.sub.m.sup.0] values were found increasing in the range of 580-587 K in comparison to [T.sub.m.sup.0] value of pure PPS but not vary regularly with composition. This indicates that the morphological factor [beta] is not constant in the present [T.sub.c] range and lamellar thickening is increasing with crystallization temperature in the composite samples.

TABLE 2. Extrapolated equilibrium temperature [T.sub.m.sup.0] (K) values
from H-W plots of PPS and PPS/TLCP composites.

PPS/TLCP composite  Extrapolated equilibrium temperature  [beta]

100/00                               579                   1.84
 90/10                               580                   1.81
 80/20                               582                   1.76
 70/30                               579                   1.83
 60/40                               586                   1.63
 50/50                               578                   1.84

Degree of Crystallinity

Table 1 also summarizes the dependence of isothermal heat of crystallization ([DELTA][H.sub.c], equal to the area under the crystallization exotherm) on isothermal temperature as well as on TLCP content in composites. The degree of crystallinity ([alpha].sub.c], the mass fraction crystallinity) has been calculated ([DELTA][H.sub.c]/[DELTA][H.sub.f]) from the enthalpy of fusion normalized to the PPS content in compositions, assuming that the contribution of the TLCP phase is negligible and the heat of crystallization is equal to the heat of fusion heat of fusion
The amount of heat required to convert a unit mass of a solid at its melting point into a liquid without an increase in temperature.
 for 100% crystallization PPS. The heat of fusion ([DELTA][H.sub.f]) for 100% crystalline PPS, 80 X [10.sub.-3] J [kg.sub.-1] was extrapolated from the data of Brady (56). In general, for particular isothermal temperature, the heats of fusion ([DELTA][H.sub.f]) and hence the degree of crystallinity steadily decrease with increasing TLCP content. However, for particular PPS/TLCP blend composition, it increases with increasing isothermal crystallization temperature from 523 to 528 K and then further decreases with increase of temperature ([T.sub.c]) to 531 and 533 K. The observed decrease in degree of crystallinity ([alpha]) of PPS with increasing TLCP content is a consequence of decreasing PPS concentration and thus the active number of nuclei for crystallization. Moreover, a comparatively large size TLCP domain with increasing concentration (see Fig. 1) reduces the PPS chain mobility during crystallization process. However, for a given PPS/TLCP composite, degree of crystallinity increases with increasing ([T.sub.c]); indicating a predominance pre·dom·i·nance   also pre·dom·i·nan·cy
The state or quality of being predominant; preponderance.

Noun 1. predominance - the state of being predominant over others
predomination, prepotency
 of temperature induced PPS chain mobility over nucleation. From these observations, it may be concluded that the [alpha] of the PPS in PPS/TLCP composites depends on the competitive compromise between the nucleation and chain mobility.

Morphology and Spherulite spher·u·lite  
A small, usually spheroidal body consisting of radiating crystals, found in obsidian and other glassy lava rocks.

 Growth Rate

To investigate the effect of TLCP component on the growth processes and the superstructure superstructure /su·per·struc·ture/ (soo´per-struk?chur) the overlying or visible portion of a structure.

A structure above the surface.
 of the PPS crystals in the PPS/TLCP composites, the films of neat PPS and PPS/TLCP composites were isothermally meltcrystallized at 523 and 533 K. The isothermal crystal growths in samples were followed by POM. The optical micrographs of isothermally crystalline neat PPS samples are presented in Fig. 4A. From the analysis of the micrographs, it is observed that the crystalline morphology of PPS is always spherulitic, exhibiting four-leaf-claver pattern. The spherulites with the fiber-like textures oriented along the radius of circle are being observed with well-defined Maltese cross suggesting a high order of both tangential tan·gen·tial   also tan·gen·tal
1. Of, relating to, or moving along or in the direction of a tangent.

2. Merely touching or slightly connected.

 and radical lamellae. Further, with increasing the crystallization time, the nuclei density increases indicating the thermal nucleation during isothermal crystallization and ultimately resulting in the impingement impingement (impinj´mnt),
n the striking or application of excessive pressure to a tissue by food or a prosthesis.
 of spherulites into each other due to the space confine.


Figure 4B shows the optical micrographs of PPS/TLCP composites, crystallized crys·tal·lize also crys·tal·ize  
v. crys·tal·lized also crys·tal·ized, crys·tal·liz·ing also crys·tal·iz·ing, crys·tal·liz·es also crys·tal·iz·es
 at 523 and 533 K temperatures. It is observed from these figures that the number of nuclei slightly increased with decreasing crystallization temperature. Also, as the concentration of TLCP increases from 10 to 20 and than 30 wt% in composites, the numbers of spherulites increases but with broken boundaries, reduced size, and diffuse Maltese cross. For these samples with higher TLCP content, some TLCP may also locate between the lamellar ribbons in the spherulities, which would be responsible for an imperfect shperulite appearance (Fig. 4B). These morphological changes support the fact that primary heterogeneous (athermal) nucleation of PPS is facilitated in the presence of TLCP. Consequently, the spherulitic nucleation density of composites is increased predominantly as manifested by the reduction in spherulitic size. However, further loading of 40 wt% TLCP, the spherulite size promptly decreases to too small sizes and thus resulting in the dense impingement with each other.


The PPS spherulite radius as a function of crystallization time at two temperatures (523 and 533 K) of crystallization for 100/00, 90/10, 80/20, and 70/30 PPS/TLCP composites were measured. For all the samples, a linear increase in the spherulitic radius with increasing time was observed. The values of growth rate G were obtained from the slopes (results not sh wn here). Figure 5 represents the composition dependence of spherulitic growth rate G of PPS/TLCP at two temperatures of crystallization (523 and 533 K). The G values of neat PPS are comparable with those observed by others (28), (57). However, a large effect of the TLCP blending on the spherulitic growth rate of PPS in composites has been observed. A significant decrease in the growth rate of PPS in the composite system was observed over that of neat PPS, larger variations being observed at lower crystallization temperature. However, very little differences in growth rates Growth Rates

The compounded annualized rate of growth of a company's revenues, earnings, dividends, or other figures.

Remember, historically high growth rates don't always mean a high rate of growth looking into the future.
 were observed with increasing TLCP content in composites. Similar depression of the spherulite growth rate of the crystallizable component has been found in the case of polycaprolactane/polyvinyl chloride (58) and poly(tetramethylene terephthalate Ter`eph´tha`late

n. 1. (Chem.) A salt of terephthalic acid.
)/TLCP crystalline/crystalline polymer blends (3). Thus as a result, at high temperature of crystallization (533 K) the diluent effect dominates resulting in low viscosity and high chain mobility at the growth front. As a consequence, PPS lamellar crystals with a less regular fold surface are formed when the PPS/TLCP composites are allowed to crystallize crys·tal·lize also crys·tal·ize  
v. crys·tal·lized also crys·tal·ized, crys·tal·liz·ing also crys·tal·iz·ing, crys·tal·liz·es also crys·tal·iz·es
 isothermally at high temperature, resulting in decrease of the crystal nucleation rate. Similar trend in many polymer systems has been reported (3), (59-61).


Overall Crystallization Kinetics

In the present case, overall crystallization process is studied by employing DSC in isothermal conditions, by measuring the heat involved during the crystallization as a function of time, based on the assumption that the evolution of crystallinity is linearly proportional to heat released during the course of crystallization. In such a case, the relative crystallinity as a function of time X(t) can be obtained from the crystallization isotherm as the area of isotherm accumulated as of time t divided by the total exotherm area according to according to
1. As stated or indicated by; on the authority of: according to historians.

2. In keeping with: according to instructions.

 the following equation:

X(t) = [[[integral].sub.0.sup.t](d[H.sub.c]/dt)dt]/[[[integral].sub.0.sup.[infinity]](d[H.sub.c]/dt)dt] (2)

where t and [infinity] are the elapsed time e·lapsed time
The measured duration of an event.

Noun 1. elapsed time - the time that elapses while some event is occurring
 during the course of crystallization and the end of the crystallization process, respectively, and d[H.sub.c] is the enthalpy enthalpy (ĕn`thălpē), measure of the heat content of a chemical or physical system; it is a quantity derived from the heat and work relations studied in thermodynamics.  of crystallization during time interval dt.

The experimental results for the heat flow versus time during the isothermal crystallization processes of neat PPS and PPS/TLCP composites at the different crystallization temperatures [T.sub.c] were obtained. Figure 6 depict the representative isothermal crystallization exotherms for the PPS and different PPS/TLCP compositions at different crystallization temperatures (523-533 K). It is observed that the crystallization exothermic exothermic /exo·ther·mic/ (-ther´mik) marked or accompanied by evolution of heat; liberating heat or energy.

ex·o·ther·mic or ex·o·ther·mal
 peak shifts toward larger time scale. The width of the peak increases with increasing TLCP content for higher crystallization temperatures, 531 and 533 K. For lower crystallization temperatures 523-531 K, the exothermic peaks shifts to lower time scale but again with increasing width, with increasing TLCP content. This indicates that crystallization temperature is an important parameter determining the overall crystallization time.


Based on the change of heat flow with time, the temporal dependent of relative crystallinity of PPS and PPS/TLCP composites at different [T.sub.c]S are obtained according to Eq. 2 and using representative Fig. 7, which show the typical representative crystallization isotherms of PPS and PPS/TLCP composites crystallized at (a) 523, (b) 528, and (c) 533 K. Figure 8 shows the typical plots of reduced crystallinity versus time for different [T.sub.c] ranging from 523 to 533 K. It can be seen that the overall development of reduced crystallinity displays characteristic sigmoidal sig·moid   also sig·moi·dal
1. Having the shape of the letter S.

2. Of or relating to the sigmoid colon.

[Greek s
 shape with time. It is possible to observe a remarkable variation of crystallization rate, depending on the crystallization temperature as well as on TLCP contents in composites. Further, it is observed from Fig. 8 that the slope of the isotherms for particular composite composition decreases with increasing crystallization temperature [T.sub.c], indicating progressively slower crystallization rate for PPS in PPS/TLCP composites. Thus evidently, within the temperature range studied, the time to reach the ultimate crystallinity increased with increasing crystallization temperature [T.sub.c]. The other kinetic parameters, [t.sub.0.5] (time to attain the [X.sub.c](t) = 0.5, [X.sub.c]([t.sub.max]) (reduced crystallinity at [t.sub.max]) were calculated from the Fig. 8 and similar results at other [T.sub.c] are presented in Table 3.


TABLE 3. Induction time ([t.sub.i]), half-time of crystallization
([t.sub.0.5]), maximum time for crystallization ([t.sub.max])
and relative crystallinity at time X([t.sub.max]) for isothermal
crystallization of PPS and PPS/TLCP composites.

PPS/TLCP    [T.sub.c](K)  [t.sub.i](sec)  [t.sub.0.5](sec)

100/00           523             8                24
                 525             9                23
                 528            22                49
                 531            28                61
                 533            58               110
 90/10           523             6                18
                 525            10                24
                 528            22                45
                 531            36                70
                 533            42                84
 80/20           523            12                30
                 525            13                26
                 528            20                38
                 531            30                58
                 533            60               136
 70/30           523             7                25
                 525            14                26
                 528            21                39
                 531            28                60
                 533            50               140
 60/40           523             8                25
                 525            13                31
                 528            14                41
                 531            28                56
                 533            55               135
 50/50           523             9                26
                 525            10                22
                 528            24                53
                 531            18                59
                 533            52               138

PPS/TLCP    [t.sub.max](sec)  X ([t.sub.max])

100/00             21               40
                   22               44
                   46               43
                   59               47
                  112               51
 90/10             22               62
                   21               42
                   44               47
                   68               48
                   81               45
 80/20             30               49
                   27               57
                   36               45
                   56               45
                  131               46
 70/30             27               54
                   27               54
                   37               46
                   56               44
                  132               45
 60/40             23               44
                   29               46
                   38               44
                   53               46
                  124               44
 50/50             24               51
                   22               49
                   54               44
                   49               44
                  124               42

The overall rate of macroscopic macroscopic /mac·ro·scop·ic/ (mak?ro-skop´ik) gross (2).

mac·ro·scop·ic or mac·ro·scop·i·cal
1. Large enough to be perceived or examined by the unaided eye.

 development of crystallinity in neat PPS and each PPS/TLCP composite is further analyzed in terms of the classical theory of Avrami for phase transformation kinetics. Avrami model (12-14) is based on the geometric extension of crystalline spherulitic structures with constant density inside. It is observed that the crystallization process in polymers is highly time dependent and influenced by the perfection process inside the spherulites. However, the crystallization behavior is usual to distinguish the linear stage for the primary crystallization from the nonlinear stage for the secondary crystallization.

In the Avrami model, the quantitatively development of relative crystallinity as a function of time, [X.sub.c](t), is related to the crystallization time, t, according to the equation:

[X.sub.[epsilon]](t) = 1 - exp exp
1. exponent

2. exponential
(-K[t.sup.n]) (3)

where [X.sub.c](t) represents the volume fraction of transformed or crystallized material after time, t. K is the overall crystallization rate constant containing contributions from both nucleation and growth rate and n is the Avrami exponent exponent, in mathematics, a number, letter, or algebraic expression written above and to the right of another number, letter, or expression called the base. In the expressions x2 and xn, the number 2 and the letter n , which depends on the nucleation and growth mechanism of the crystals for a particular crystallization condition.

To deal conveniently with the thermal data operation, the Eq. 1 can be rewritten as the double logarithmic logarithmic

pertaining to logarithm.

logarithmic relationship
when the logs of two variables plotted against each other create a straight line.
 form, as follows:

log[ - ln(1 - [X.sub.c](t))] = n log t + log K (4)

A plot of double logarithm logarithm (lŏg`ərĭthəm) [Gr.,=relation number], number associated with a positive number, being the power to which a third number, called the base, must be raised in order to obtain the given positive number.  of the amorphous content, log[-ln(l-[X.sub.c](t))] as a function of the logarithm of time, log t, using Eq. 4, known as a classical Avrami plot, allows the calculation of n and K from the slope and intercept of the best-fit straight lines, respectively.

Avrami exponent n and the rate constant K can also be calculated by the use of the crystallization half time [t.sub.0.5]. The crystallization half time, [t.sub.0.5], is defined as the time at which the normalized crystalline content is 0.5. The advantage in this approach is that the analysis is based on all the isothermal data and not just a single point. Taking the logarithm of Eq. l at t = [t.sub.0.5], one obtains

K = log 2/[t.sub.0.5.sup.n]. (5)

Figure 9 illustrates the classical Avrami plot of Eq. 4 for neat PPS and PPS/TLCP composites. It can be seen that the experiment data particularly at low conversions closely agree with the Avrami equation and is due to primary crystallization. Here, it is understood that the primary crystallization consists of the outward clear growth of lamellar stacks. The observed nonlinear behavior at high conversions is due to the occurrence of the secondary crystallization which is believed to be caused by the spherulite impingement in the later stage of crystallization process and may well overlap the primary crystallization by filling in the spherulites of interstics. In this work, we focus only on primary crystallization (62). Table 4 lists the Avrami exponents of neat PPS and PPS/TLCP composites at various [T.sub.c]s.

TABLE 4. Avrami parameters and activation energy of PPS and PPS/TLCP
composites as function of crystallization temperature.

PPS/TLCP     [T.sub.c] (K)   n    K(t)    [K(t).sub.0.5]

100/00           523        2.10  4.50        4.75
                 525        2.52  7.96        7.77
                 528        3.11  1.50        1.30
                 531        2.61  0.66        0.66
                 533        2.73  0.13        0.13
 90/10           523        2.30  8.83       11.05
                 525        2.50  6.98        6.68
                 528        3.01  1.59        1.65
                 531        2.80  0.47        0.45
                 533        2.40  0.29        0.31
 80/20           523        2.59  4.02        4.17
                 525        3.37  9.89       11.61
                 528        2.92  2.74        2.63
                 531        2.62  0.71        0.76
                 533        2.64  0.08        0.08
 70/30           523        2.06  3.94        4.21
                 525        3.30  9.70       10.95
                 528        3.01  2.71        2.53
                 531        2.44  0.52        0.69
                 533        2.38  0.09        0.09
 60/40           523        2.21  4.79        4.80
                 525        2.55  3.97        3.73
                 528        2.35  1.76        1.70
                 531        2.61  0.94        0.83
                 533        2.44  0.10        0.10
 50/50           523        2.20  4.02        4.36
                 525        2.52  8.67        8.69
                 528        2.33  0.69        0.93
                 531        2.51  1.09        0.72
                 533        2.69  0.08        0.07

PPS/TLCP         Correlation       [DELTA]E X [10.sup.-3]
composition  coefficient (Fig. 9)    (KJ [mol.sup.-1])

100/00               0.9992                      108
 90/10               0.9992                       76
 80/20               0.9994                       10
 70/30               0.9961                       75
 60/40               0.9991                       61
 50/50               0.9994                       40

An Avrami exponent n with value close to three is attributed to three-dimensional crystal growth (spherical structure) resulting from instantaneous athermal nucleation process. On the other hand, an n value between two and three represents non three-dimensional truncated spherical structures resulting from instantaneous nucleation, controlled by diffusion process Diffusion process

A conception of the way a stock's price changes that assumes that the price takes on all intermediate values.
. The nonintegral n values indicate the presence of the combination of thermal and athermal mixed nucleation and mechanisms (63). In present case for pure PPS, it can be observed that the exponent n is found to range from 2.10 to 3.11 (Table 4) when the crystallization temperature increases from 523 to 525 K and from 525 to 528 K. This indicates to gradual growth of two-dimensional morphology to a spherical three-dimensional morphology with a combination of thermal and athermal nucleation. This is well understood, based on the fact that as the crystallization temperature decreases from 528 to 525 K and from 525 to 523 K, the athermal nucleation density in PPS increases (64) resulting in enhanced instantaneous nucleation mechanism, causing the Avrami exponent n to decrease. At such larger undercooling ([DELTA]]T = [T.sub.m.sup.0]--[T.sub.c]), the spherulitic truncation from impingement ultimately prevents the developing of fully grown three-dimensional morphology. Further with increasing crystallization temperatures to 531 and 533 K, the Avrami plots show a deviation from the linear trend, indicating the presence of secondary crystallization, consecutively occurring with primary crystallization for PPS. These two plots are characterized by slightly lower n values, around 2.61 and 2.73, respectively, and then the ones found for lower crystallization temperatures at 528 K. The lower values may be attributed to comparatively imperfect three-dimensional crystal growths, resulting out of early spherulite impingement in the later stage of crystallization process. Also, because of the overall low polymer chain mobility at lower crystallization temperatures, the diffusions of crystallizable polymer segments become difficult and selective. Only the nearest neighbors of polymer segments could associate with each other for intermolecular Adj. 1. intermolecular - existing or acting between molecules; "intermolecular forces"; "intermolecular condensation"  crystallization. In such cases, the presence of intermediate sheaf-like structures in PPS is possible as reported by Lopez and Wilkes (24).

The values of the Avrami exponents corresponding to PPS/TLCP blends crystallized from the melt at different crystallization temperatures [T.sub.c]s are presented in Table 4. In present case, we found that the blending of TLCP did change n values. This indicates that the addition of TLCP into PPS does affect the nucleation process followed by crystal growth. The analysis of crystallization kinetic parameters, n and K, of blends indicate that the values of these parameters vary with respect to both, the crystallization temperature as well as composite composition.

In the present case, the n values as a function of wt % TLCP, two different behaviors are observed, one at low [T.sub.c] at values 523 and 525 K and another at higher [T.sub.c] temperatures at 528, 531, and 533 K. At 523 K, the n values (n = 2.30-2.59) are increasing for 90/10 and 80/20 compositions: afterward it decreases with the increase of TLCP content (n = 2.20 for 50/50 composition), which is in both cases comparatively still little higher than pure PPS (n = 2.10). In the case of 525 K crystallization temperature, n values are increasing with increasing TLCP content in blends, up to a concentration of 30 wt % TLCP (2.80, 3.37, and 3.30). However, with further increasing wt % TLCP it reaches to same value of PPS (2.52). For both the [T.sub.c]s, the maximum value of n representing higher dimensionality is observed for 80/20 blend composition. Further as the [T.sub.c] temperature increases to 531 and 533 K, compared with pure PPS, n values decrease with increase in TLCP content except for 90/10 composition (n = 2.80 for [T.sub.c] = 531 K) and are in the range of 2.62-2.40. The maximum n values (2.92 and 2.64) are again obtained at a low TLCP concentration ([less than or equal to]wt% 20%) in blends.

The analysis clearly indicates that in general the introduction of TLCP into the PPS notably causes heterogeneous growth process from crystal growth to a combination of two-dimensional and three-dimensional spherulitic growths particularly depending on the crystallization temperatures. The nonintegral values and particularly values of n lower than 3 support crystal branching and/or two-stage crystal growth and/or mixed growth and nucleation mechanisms (62). The results suggest that introducing low concentrations of 10-20 wt% of TLCP into PPS induces the uniform heterogeneous nucleation. On the other hand, higher TLCP loading induced more steric steric /ste·ric/ (ster´ik) pertaining to the arrangement of atoms in space; pertaining to stereochemistry.

ster·ic or ster·i·cal
 hindrance hin·drance  
a. The act of hindering.

b. The condition of being hindered.

2. One that hinders; an impediment. See Synonyms at obstacle.
 resulting in reduced PPS chain transportation ability during crystallization process, it seems, which is minimum at 525-528 K crystallization temperatures. Moreover, the calculated values of n (Table 4) for PPS/TLCP composites are in general consistent with a spherulitic growth of PPS initiated by athermal nucleation. This is well supported when combined with the observations under POM (Fig. 4B), where the PPS still shows spherulitic structures, however, depending on the TLCP content in composites.

The TLCP content in the PPS/TLCP composites can influence the crystallization rate parameter by providing nucleating sites and reduce the melt viscosity of PPS. As aforementioned, in present case the lowering of the [T.sub.g] of PPS (Table 1) indicates that the TLCP content in these composites may be acting as a diluent in the crystallization of PPS. Thus with lower TLCP content when the nucleation effect dominates, the result expected is a higher crystallization rate. However, the increased TLCP content will result in a lower crystallization rate as now the diluent effect becomes dominant. The data in present case reflect the results of the competition between these two effects.

The values of [t.sub.0.5] and K(T) of PPS and PPS/TLCP blends determined from Eq. 4 are listed in Tables 3 and 4, respectively. It can be deduced from the Table 4 that K(T) is affected by crystallization temperatures as well as by the blend compositions. It is observed that in the 90/10 composition, the PPS crystallization is faster than in pure PPS at 523 K crystallization temperature, which slows down on further addition of TLCP in blends. The value of [t.sub.0.5] is smaller than that of pure PPS. With further increase in the crystallization temperatures to 525 and 528 K, the rate is now faster for blends with increasing TLCP content upto 30 wt%. However, [t.sub.0.5] values remain almost unchanged for these blends but slightly higher than pure PPS at 525 K crystallization temperature, whereas at 528 K, compared with pure PPS the [t.sub.0.5] shows lower time values at all blend compositions except for 50/50 composition. This faster crystallization can be attributed to the increased nucleation density due to presence of TLCP on the crystallization of PPS. However, when TLCP content is increased more than 30 wt%, the K(T) as well as [t.sub.0.5] variations are irregular. This may be due to the competitive affect of nucleation effect of TLCP and the temperature induced morphological restrictions caused by TLCP itself on the diffusion of crystallizing PPS macromolecules Macromolecules
A large molecule composed of thousands of atoms.

Mentioned in: Gene Therapy

. It should be noted that the K(T) contains contribution from both nucleation and growth rates. At a high crystallization temperature, 531 K, the K(T) slightly increases with marginally improvement in [t.sub.0.5] value for all the blend compositions except for 90/10 composition. However, with further increase in crystallization temperature to 533 K the K(T) remains almost unchanged with very high [t.sub.0.5] values compared with pure PPS for all the compositions, again except for 90/10 composition. Such a lower crystallization rate at high crystallization temperatures can be attributed to the lower nucleation density and reduced melt viscosity, ultimately resulting in slower spherulitic growth (62), which is well consistent with hypothesis that the crystallization kinetics in the particularly higher [T.sub.c] range is dominated by the thermodynamic driving forces of crystallization.

Activation Energy activation energy, in chemistry, minimum energy needed to cause a chemical reaction. A chemical reaction between two substances occurs only when an atom, ion, or molecule of one collides with an atom, ion, or molecule of the other.  of Crystallization

Assuming crystallization process of the neat PPS and PPS/TLCP composites is thermally activated the crystallization rate parameter (K) can be approximately described by the following Arrehenius form of equation (65).

[K.sup.1/n] = [K.sub.0] exp( - [DELTA]E/[RT.sub.c] (6)

1/n in K = ln([K.sub.0] - [DELTA]E/[RT.sub.c] (7)

where [K.sub.0] is the temperature independent pre-exponential factor, [DELTA]E is the crystallization activation energy which consists of both, the transport molecular segments across the phase boundary to the crystallization surface and the free energy required for the formation of the critical size crystal nuclei at crystallization temperature, [T.sub.c]. R is the universal gas constant universal gas constant: see gas laws. . The crystallization activation energy [DELTA]E, was determined by the slope coefficient of Arrehenius plots of 1/n In K vs. 1/[T.sub.c] in Eq. 7 (plots are not shown here). The value of [DELTA]E is considered negative heat quantity as it is energy released when the polymer melt transformed into crystalline state. In this study, the [DELTA]E values for neat PPS and PPS/TLCP in primary crystallization are reported in Table 4. The results indicated that activation energy is remarkably dependent on the content of the TLCP in composites, which ultimately comparatively governs the overall nucleation density and the TLCP total droplet external surface area in composites. Although the increasing TLCP content may increase the nucleation density, however, the overall effective external surface area decreases with increasing TLCP content due to larger droplets morphology (see Fig. 1). In present case, the crystallization activation energy decreases upto 30 wt% of TLCP content which, however, increases for 40 and 50 wt% of TLCP content in composites. It seems that initially TLCP droplets increase the mobility of the molecular chains of PPS to crystallize and accelerate crystallization rates. Also the large external surface of TLCP droplets contributes to enhanced nuclear density. Both contribute in overall decreasing activation energy. Further with increasing TLCP content (> 30 wt%), it increases due to now restricted mobility of PPS chains as well as total lower available droplet surface area. However, still the value is lower compared with neat PPS. This clearly indicates that the addition of higher content of TLCP induces ultimately more heterogeneous nucleation density which dominates over the effect of reduced polymer chain transportation ability.

Regime Kinetics and Chain Folding Mechanism

Thermodynamic parameters concerning the crystallization process can be determined from the calorimetric cal·o·rim·e·ter  
1. An apparatus for measuring the heat generated by a chemical reaction, change of state, or formation of a solution.

 kinetic data obtained in isothermal conditions. In bulk crystallization, the crystal growth is strictly a process controlled by the secondary nucleation and thus the overall isokinetic isokinetic /iso·ki·net·ic/ (-ki-net´ik) maintaining constant torque or tension as muscles shorten or lengthen; see isokinetic exercise, under exercise.  crystallization rates are not as simple to be interpreted as only spherulitic radial growth, which is in fact a combination of nucleation and growth phenomena (15). According to Lauritzen-Hoffman (L-H) model of kinetic theory of polymer crystallization, the temperature dependence of the linear growth rate (G) of a chain-folded polymer crystal is given by the following biexponential relationship (15), (17):

G = [G.sub.0] exp ([-U*]/[R([T.sub.c] - [T.sub.[infinity]]])) exp (-[k.sub.g]/f[T.sub.c][DELTA]T). (8)

In L-H relation, the first term in parenthesis represents a contribution due to polymeric polymeric /poly·mer·ic/ (pol?i-mer´ik) exhibiting the characteristics of a polymer.

1. Having the properties of a polymer.

 segments, whereas the second term represents the thermodynamic driving force. In Eq. 8, [G.sub.0] is a pre-exponential factor that includes all temperature-independent terms, U* is the activation energy (WLF WLF Washington Legal Foundation
WLF Wallis and Futuna (ISO Country code)
WLF Waist Level Finder (camera viewfinder type)
WLF Viva La Figa (MotoGP motorcycle races) 
 energy term) for the transport of crystallizable segments at liquid--solid interface and is universal constant typically taken as 6.280 J [mol.sup.-1], [T.sub.[infinity]] the hypothetical temperature (WLF-temperature) below which all motion associated with viscous viscous /vis·cous/ (vis´kus) sticky or gummy; having a high degree of viscosity.

1. Having relatively high resistance to flow.

2. Viscid.
 flow or reptation ceases, and usually assumed to be equal to ([T.sub.g] - 30)K, the term [florin] = 2[T.sub.c]/([T.sub.m.sup.0] + [T.sub.c]), a correlation factor The ratio of a ground dose rate reading to a reading taken at approximately the same time at survey height over the same point on the ground.  that is closed to unity at high temperatures and introduced to account for the temperature dependence change of enthalpy of fusion of the perfect crystal ([DELTA][H.sub.f]). The factor [K.sub.g] understood as a nucleating constant is important as it contains the variable n that reflects the regime behavior. The second exponential term in L-H relation is a highly dependent function of crystallization temperature [T.sub.c] and undercooling [DELTA]T (where [DELTA]T = [T.sub.m.sup.0] - [T.sub.c]) and is measured from the thermodynamic melting point [T.sub.m.sup.0] of samples. The factor [K.sub.g], a (secondary) nucleation constant that controls crystal growth and reflects the regime behavior, and thus contains contributions from the surface free energies of the lamellar crystals, is expressed by,

[k.sub.g] = m[b.sub.0][sigma][[sigma].sub.e][T.sub.m.sup.0]/kd[DELTA][H.sub.f.sup.0] (9)

where [b.sub.0] is the thickness of a single molecular layer (stem) in the crystal and generally taken to be the prependicular separations of two adjacent fold planes. In PPS, the chain folding for nucleation takes place along the (020) crystal plane and the [b.sub.0] value has been taken as the perpendicular separation of growth crystal plane. [sigma] and [[sigma].sub.e] are the free energy of formation per unit area of the lateral (side surface) and folding surfaces, respectively, d is the density of perfect crystalline phase (1.35 X [10.sup.3] kg [m.sup.-3] for fully crystalline PPS) (65), (66), and k is the Boltzmann constant Boltzmann constant

Ratio of the universal gas constant (see gas laws) to Avogadro's number. It has a value of 1.380662 × 10−23 joules per kelvin.
. According to the L-H (15), (67), the value of m in Eq. 9 depends on the crystallization regime.

Instead of the spherulitic radial growth, however, the use of the overall growth rate is supported by the literature (68), (69). Thus, assuming that the three-dimensional crystal growth is linear with crystallization time; the overall kinetic constant K can be expressed as:

K = (4[pi]/3) [G.sup.3]N (10)

where N is the nucleation density.

By combining Eqs. 6 and 8, the following relationship can be obtained:

1/3lnK = [C.sub.0] - U*/R([T.sub.c] - [T.sub.[infinity]]) - [k.sub.g]/[florin][T.sub.c][DELTA]T). (11)

where [C.sub.0] = In [G.sub.0 - 1/3 In (3/4[pi]N).

Next the regime analysis of the L-H model was performed to treat the growth rate data. For the kinetic analysis of crystallization rate, the transport term in Eq. 9 can be considered constant as the investigated [T.sub.c] range (523-533 K) is very narrow. Using U* = 1.400 kcal [mol.sup.-1], [T.sub.[infinity]] = ([T.sub.g] - 30) K, where [T.sub.g] = 367 K, and f = 2[T.sub.c]/([T.sub.m.sup.0] + [T.sub.c]), where [T.sub.m.sup.0] values derived using linear H-W extrapolation (mathematics, algorithm) extrapolation - A mathematical procedure which estimates values of a function for certain desired inputs given values for known inputs.

If the desired input is outside the range of the known values this is called extrapolation, if it is inside then
, [DELTA] [H.sub.m.sup.0] = 80 X [10.sup.-3] J [kg.sup.-1], and the other values of [t.sub.0.5] and n from Avrami analysis. The values of kinetic parameters, calculated from the growth rate data are listed in Table 5. In the present case, the Eq. 11 is used with In 2/[t.sub.0.5.sup.n] in place of K, as both of these two crystallization rate parameters are well related to the primary nucleation rate and there after crystal growth rate (15). Figure 10 shows plots of 1/3 In K + [U*/R([T - [T.sub.[infinity]) vs. 1/f[T.sub.c] [DELTA]T for pure PPS and PPS/TLCP composites, which provide the values of [K.sub.g] (slope) for regime II (discussed latter in this section characterized by m = 2) and [G.sub.0] (intercept) which describe the nucleation constants and absolute linear growth rates respectively. In fact, the nature of the transport of chain segments and its effect on the growth front are embodied in the [G.sub.0], which measure the effect on the growth rate of reptational diffusion as the molecular chain, is drawn onto the crystal substrate by the force of crystallization. The optimal fit in Fig. 10 is reflected in the correlation coefficients which are close to 1, except for the 70/30 PPS/TLCP composite. The [G.sub.0] and [K.sub.g] values thus obtained are presented in Table 6. It can be observed that the presence of TLCP in PPS lead to composition dependent [K.sub.g] and [G.sub.0] values. These data indicate that PPS/TLCP composites have significant values of nucleation constant [K.sub.g] and [G.sub.0] depending on the TLCP content in composites. The values [G.sub.0] of 90/10 composite is higher compared with pure PPS, suggesting that the introduction of low content of 10 wt% TLCP into PPS mainly plasticize plas·ti·cize  
tr. & intr.v. plas·ti·cized, plas·ti·ciz·ing, plas·ti·ciz·es
To make or become plastic.

 the PPS and therefore resulting in faster nucleation chain motion, leading to higher rate constant [G.sub.0]. However, it is necessary to point out that the morphology of the PPS/TLCP composites indicated the formation of larger TLCP droplets with further increase in TLCP content (70), causing more gradual restriction of polymer transportation which is expected to lower the [G.sub.0] and [K.sub.g] values for 20 and 30 wt% of TLCP. On the other hand, the results indicate that, the addition of more TLCP, also induces the effective heterogeneous nucleation of PPS which probably now dominates over low transportation ability of PPS--molecular chains. As a consequence, the resultant values of [G.sub.0] and [K.sub.g] of composites increase with increasing TLCP contents to 40 and 50 wt%.

TABLE 5. Values of kinetic parameters calculated from Lauritzen-Hoffman
analysis for isothermal crystallization of PPS and PPS/TLCP composites
(U* = 1.400 kcal [mol.sup.-1]).

PPS/TLCP  [T.sub.m.sup.0]  [T.sub.c] (K)    (1/3) In K =
                (K)                        (1/3) In (In 2/

 100/00           578           523             -2.4104
                                525             -2.7560
                                528             -4.1567
                                531             -3.6986
                                533             -4.3996
  90/10           580           523             -2.4345
                                525             -3.0884
                                528             -4.0557
                                531             -4.0874
                                533             -3.6668
  80/20           582           523             -3.0585
                                525             -3.7821
                                528             -3.6628
                                531             -3.6683
                                533             -4.4453
  70/30           579           523             -2.3325
                                525             -3.7061
                                528             -3.7918
                                531             -3.4522
                                533             -4.0425
  60/40           586           523             -2.4977
                                525             -3.0411
                                528             -3.0311
                                531             -3.6242
                                533             -4.1118
  50/50           578           523             -2.5114
                                525             -2.7186
                                528             -3.2058
                                531             -3.5337
                                533             -4.5403

PPS/TLCP     (1/3) In K +      f = 2[T.sub.c]/    {1/([T.sub.c]
                  U*/         ([T.sub.m.sup.0]  ([T.sub.m.sup.0] -
            (R([T.sub.c]-       + [T.sub.c])        [T.sub.c])
          [T.sub.[infinity])                      f X [10.sup.5]

100/00          1.4413             0.9500             3.6592
                0.9918             0.9519             3.7753
               -0.4678             0.9548             3.9672
               -0.0668             0.9576             4.1842
               -0.8048             0.9595             4.3453
 90/10          1.4499             0.9483             3.5373
                0.9772             0.9502             3.6446
               -0.2526             0.9531             3.8215
               -0.4556             0.9559             4.0207
               -0.0720             0.9578             4.1679
 80/20          0.7295             0.9470             3.4513
               -0.0343             0.9489             3.5527
                0.0261             0.9518             3.7194
               -0.0364             0.9546             3.9065
               -0.8505             0.9565             4.0444
 70/30          1.4556             0.9496             3.6279
                0.0417             0.9515             3.7417
               -0.1029             0.9544             3.9297
                0.1796             0.9572             4.1420
               -0.4477             0.9591             4.2995
 60/40          1.2904             0.9432             3.2178
                0.7067             0.9451             3.3040
                0.6578             0.9479             3.4448
                0.0076             0.9508             3.6014
               -0.5170             0.9526             3.7160
 50/50          1.2766             0.9500             3.6592
                1.0291             0.9519             3.7753
                0.4831             0.9548             3.9672
                0.0981             0.9576             4.1842
               -0.9455             0.9595             4.3453

TABLE 6. Results of the Lauritzen--Hoffman analysis: value of nucleation
constant and parameters for isothermal crystallization of PPS and
PPS/TLCP composites in regime II ([sigma] = 16.8 x [10.sup.-3] J

PPS/TLCP     Nucleation   [G.sub.0]     Correlation
composites    constant   [10.sup.4])  (X coefficient
            ([k.sub.g])  [10.sup.4])     (Fig. 10)

100/00         303357       26.0          0.9888
 90/10         353926       92.0          0.9690
 80/20         266500        2.1          0.9999
 70/30         276395        7.5          0.8403
 60/40         361360       44.0          0.9860
 50/50         329265       68.0          0.9900

PPS/TLCP       Fold surface     Lateral surface free      Work of
composites     free energy         energy [[sigma]     chain folding
            [[sigma].sub.e] X     [sigma].sub.e] X       (q) (kcal
               [10.sup.-3]     [10.sup.-6] ([J.sup.2]   [mol.sup.-1])
              (J [m.sup.-2])         [m.sup.-4])

100/00            41.11                690.61                5.8
 90/10            47.80                802.95                6.8
 80/20            35.90                603.05                5.1
 70/30            37.42                628.68                5.3
 60/40            48.30                811.42                6.8
 50/50            44.62                749.59                6.3

At this point, it is important to mention here that the growth rates measured for PPS/TLCP by DSC and POM in this study do not agree absolutely. The discrepancies may be due to the fact that the overall crystallization data of polymer composites are much more complex involving primary and secondary crystallizations. Moreover, DSC is a macroscopic method in which the overall rate of the phenomenon is measured, whereas in POM, which is a rather microscopic method, the spherulite growth rate is measured directly that too in the constrained environment (68), (71). In the DSC data analysis, the entire secondary phenomenon that can occur during the overall crystallization are left out. Also, the assumption that the growth rate in the L-H equation can be replaced by the inverse half crystallization time has not been tested thoroughly. The validity of such a assumption influence the growth rate values, calculated from DSC data.

Most extensive set of melt crystallization growth data over the [T.sub.c] range from 383 to 553 K for pure PPS ([M.sub.w] = 15,000) has been reported by Lovinger et al. (22). They reported a regime II [right arrow] III transition centered at 481 K. They also predicted temperature of the regime I [right arrow] II transition between 524 and 536 K which is at the high temperature end of growth. Silverstre et al. (28) observed a possible regime II [right arrow] III break at 523 K for pure PPS ([M.sub.w] = 12,000). The higher value of regime transition temperature in latter case may be due to the difference in molecular mass of the PPS and the thermal treatments.

Figure 10 plots confirm that the present data is consistent with linear relationships over a present range of isothermal crystallization temperatures 523--533 K. No clear regime transition break is observed in this study. In this report, the isothermal crystallization data have been collected above 523 K, which lies at higher temperature end when compared with Lovinger's [T.sub.c] range (22). Additionally, the reasonable estimates of surface free energies and the work of chain folding for the PPS/TLCP composites indicate that regime II nucleation kinetics described by Lauritzen and Hoffman may be still followed at present crystallization temperatures in the PPS even after TLCP blending.

To further confirm the regime II crystallization kinetics, we employed Lauritzen treatment known as a Z-test (72). The isothermal crystallization of polymers is believed to proceed through the growth of lamellae which provide substrate for further growth. The test shows the dependence of lamellar growth rate (G) upon the mean length of the substrate (L) in the crystallographic crys·tal·log·ra·phy  
The science of crystal structure and phenomena.

 register. The surface nucleation rate of new growth layers per unit length per unit time (i), the velocity with which the growth layer covers the substrate (g), and the thickness of the growth layer (b).

At high [T.sub.c]s (low [DELTA]T), the adsorbed molecules can spread rapidly along the width of the lamellar substrate prior to the next molecular nucleation event. This results in relatively smooth growth surface over the length, L, and [G.sub.i] = ibL where i is the nucleation rate. This temperature region is defined as regime I and m = 4 in Eq. 7. At lower [T.sub.c]s (medium [DELTA]T), the rate of nucleation is so high that adsorbed molecular strips have no place to spread laterally resulting in ultimately crystallization through accumulating nucleation events. Under such conditions (regime III) m is again equal to 4 ([G.sub.III] [varies] i). At intermediate temperatures, nucleation occurs at high rates compared the regime I so multiple nuclei form on the substrate at a rate, i, and spread slowly at a velocity g. In this case, during crystallization, the adjacent nucleus has to compete in spreading laterally on the crystal substrate ultimately resulting in multiple nucleation events commencing before previous ones have finishes. At molecular level the formed substrate surface is rough and uneven. Now the crystal growth is proportional to the square root, ([G.sub.II] = b[(2ig).sup.1/2]. In this regime II, m is now equal to 2.

In regime II crystallization, during the layer growth process, if the [bar.n] is the ensemble average In statistical mechanics, the ensemble average is defined as the mean of a quantity that is a function of the micro-state of a system (the ensemble of possible states), according to the distribution of the system on its micro-states in this ensemble.  of the number of nuclei for each completed growth layer then (1/[bar.n]) will be the fraction of nuclei initiating growth layers resulting in iL/[bar.n] number of growth layers per lamella lamella /la·mel·la/ (lah-mel´ah) pl. lamel´lae   [L.]
1. a thin leaf or plate, as of bone.

2. a medicated disk or wafer to be inserted under the eyelid.
 per unit time, formed out of average number of nuclei, iL, per unit time. The growth rate (G) is now given by G = (biL/[bar.n]), Here,[bar.n] is a dimensionless number dimensionless number  

A number representing a property of a physical system, but not measured on a scale of physical units (as of time, mass, or distance). Drag coefficients and stress, for example, are measured as dimensionless numbers.
 and depends on the finite possible numbers i, L, and g. Thus [bar.n] is a function of possible geometrical dimensionless arrangement, i[L.sup.2]/g. One define Z = i[L.sup.2]/4g (60), using the following approximated relations for the nucleation rate (i) and the velocity (g).

i = [beta]/[alpha] exp ([-4b[sigma][[sigma].sub.e]]/[kT[DELTA]f] - 2ab[[sigma].sub.e]/kT)) (12)


g = [alpha][beta] exp (-2ab[[sigma].sub.e]/kT)) (13)

The Lauritzen approximated Z-test equation for regime II is defined as

z [approximately equal to] [10.sup.3] [(L/2a).sup.2] exp (-X/T[DELTA]T) (14)

where for regime II, X = 2[K.sub.g] and Z [greater than or equal to] 1. The value of [k.sub.g] is determined from the slope of the plot shown in Fig. 10. With this approach, it follows that to be in regime II,

L [approximately equal to] 2a [[10.sup.-3] exp(2[k.sub.g]/[T.sub.c][DELTA]T)).sup.1/2]. (15)

The possible values of L in regime I and II for pure PPS and PPS/TLCP composites were calculated. It is generally observed that any one regime will produce reasonable values of L whereas other will give unrealistic values. In this case for regime I, L was determined to be very low values than that of regime II, ranging from 10.00 to 52.00 [Angstrom angstrom (ăng`strəm), abbr. Å, unit of length equal to 10−10 meter (0.0000000001 meter); it is used to measure the wavelengths of visible light and of other forms of electromagnetic radiation, such as ultraviolet ], which are unreasonable substrate lengths compared with latter. This appears to rule out crystallization in regime I. It is therefore possible to conclude that this secondary crystallization in pure PPS as well as PPS in PPS/TLCP composites growth occurs according to regime II kinetics where large numbers of surface nuclei form on the substrate with multiple nucleation acts. This occurs comparatively at faster rates and thus facilitates adjacent nuclei spreading laterally on the crystal substrate resulting in growth of chain folded PPS-crystallites following secondary crystallization process on the already existing crystalline substrate with the rate of secondary nucleation comparative with the rate of substrate completion rate. Thus, assuming that the PPS crystallization in PPS/TLCP composites occurs in regime II the calculated possible values of L in regime II are presented in Table 7. As the stringency of the Eq. 15 depends on the isothermal crystallization temperature it is observed that the L values for pure PPS as well as for particular PPS/TLCP composite increase with increasing [T.sub.c]. However for particular [T.sub.c] the trend in development in substrate length (L) in composites is complex which in comparison to pure PPS increases for 90/10 than which further reduces for 80/20 and 70/30 compositions. However, it increases for 60/40 and 50/50 PPS/TLCP composites. It is to be noted here that in regime II, the substrate of length L will suffer multiple nucleation and therefore be quite rough. Consequently, growth rates are now associated with both the parameters i and g [[G.sub.II] = [(i[b.sub.0]g).sup.1/2]. However, the critical factor in this regime is the niche separation between two neighboring neigh·bor  
1. One who lives near or next to another.

2. A person, place, or thing adjacent to or located near another.

3. A fellow human.

4. Used as a form of familiar address.

 nuclei. As the nucleation rate decreases with increasing [T.sub.c], the niche separation is continuously increased which now can accommodate number of stem width [a.sub.0]. This ultimately results in large substrate length.
TABLE 7. Maximum substrate length (L in [micro]m) required for
the crystallization to fall in regime II, using Lauritzen Z test.

                         Isothermal crystallization
                               temperature (K)

PPS/TLCP composition   523   525   528    531    533

100/00                2.08  2.97   5.97  10.40  17.00
 90/10                0.17  0.23   0.35   0.56   0.80
 80/20                0.33  0.44   0.69   1.13   4.88
 70/30                0.75  1.03   1.74   3.15   4.88
 60/40                1.24  1.65   2.64   4.47   6.55
 50/50                5.13  7.55  14.30  29.40  50.20

Once it is established that the crystallization occurs in regime II across a present range of [T.sub.c], the growth rate data is used to estimate [[sigma][sigma].sub.e]. The value of [sigma], the lateral surface energy, was calculated by the following Thomas-Stavely empirical relation (15):

[sigma] = [alpha]([DELTA][H.sub.f.sup.0])[([a.sub.0][b.sub.0]).sup.1/2] (16)

where d is a constant generally ranging from 0.1 to 0.3. As the value of [alpha] for organic molecules is closer to 0.30, a value of [alpha] = 0.25 has been chosen for estimation the lateral surface free energy ([sigma]) in present case. For calculations taking (020) growth substrate plane, the molecular width ([a.sub.0]) is 4.33 [angstrom] and the molecular thickness ([b.sub.0]) is 5.66 A. Here, Eq. 16 has yielded [sigma] = 1680 x [10.sup.-2] J [m.sup.-2]. Using experimentally observed [T.sub.m.sup.0] and [K.sub.g] values for neat PPS and PPS/TLCP composites listed in Tables 2 and 6, respectively, and the density of fully crystalline PPS equal to 1.35 x [10.sup.3] kg [m.sup.-3] (57), (58), the fold surface free energy values ([[sigma].sub.e]) can be obtained using Eq. 9. The calculated values of [[sigma].sub.e] are presented in Table 6. It can be seen that [[sigma].sub.e] found to be a function of TLCP content in composites.

In present case, for pure PPS, the value of [[sigma].sub.e] = 41.10 X [10.sup.-3] J [m.sup.-2] has been obtained, which is almost similar to the ones reported in the literature (73). The [[sigma].sub.e] value for PPS/TLCP composite with 10 wt% TLCP is 47.80 X [10.sup.-3] J [m.sup.-2] which is higher than that of pure PPS. With further increase of TLCP content to 20 and 30 wt% it is observed that there is a tendency of [[sigma].sub.e] to decrease (even much lower than that of pure PPS) which, however, shows a reverse trend as TLCP content increase to 40 and 50 wt% in composites. These results clearly indicate that the fold surface interfacial energies of PPS in composites are modified. This change can be understood in terms of the possible competitive compromise between the nucleation effect and the hindrance of TLCP particles on the mobilities of PPS chains. As [[sigma].sub.e] is strongly correlated with the work of chain folding, which is further understood in terms of bending of polymer chain back upon itself, the initial higher [[sigma].sub.e] value in composite indicates that there exist constraints on the mobility of the PPS chains in the interspherulitic regions due to the presence of TLCP. However the further increasing TLCP content in composites increases multiple nucleation which now dominates over restricted chain mobilities. Also, this increased nucleation density leads to more complex molecular architecture of PPS, ultimately resulting in formation of loops and the tie molecules and dangling chain ends, which contributes to hindrance in chain folding. Such morphology eventually decreases the end surface free energy ([[sigma].sub.e]) required for crystallization. As mentioned earlier, much higher loading of TLCP (> 30 wt%), now increases the size of TLCP particle domains as well as the number of domains, which could cause more effective restrictions on the mobility of PPS segments and slow down the PPS crystallization (72). At such a situation, we believe that to crystallize PPS-chain molecules in composites require overcoming a higher nucleation barrier during crystal growth.

The work of chain folding (q), which has been found to be the one parameter most closely correlated with molecular structure and contribution to its relative magnitude is from inherent stiffness of the chain itself (15). In fact, the large amount of the work of chain folding q may be attributed to the fact that few certain segments with fold may be in elevated intramolecular in·tra·mo·lec·u·lar  
Within a molecule.

 rotational energy This article is about the rotation of an object around a single axis (a one-dimensional rotation). See rigid rotor for the kinetic energy of an object that rotates in three dimensions.  levels. According to L-H (74), the work of chain folding permolecular fold can be obtained from:

[[sigma].sub.e] = [[sigma].sub.eo] + q/(2[a.sub.0][b.sub.0]) [approximately equal to][sigma] + q/(2[a.sub.0][b.sub.0]) (17)

where [[sigma].sub.eo] is the value equal to [[sigma].sub.e] when no work is required to bend the polymer chain back upon itself considering the conformational constraints on the fold imposed by the crystal structure. As a first approximation, it is assumed that the [[sigma].sub.eo] may be taken equal to the lateral surface interfacial energy [sigma]. Thus, it is expected that [[sigma].sub.eo] will be significantly less than q/(2[a.sub.0][b.sub.0]i) and ultimately may be set equal to zero. The Eq. 17, therefore, is usually written in the following form:

q = 2[a.sub.0][b.sub.0][[sigma].sub.e] (18)

For a polymer, [[sigma].sub.e] is considered to be inversely proportional to the chain area, and considering q/2 as a proportionality constant, and thus Eq. 18 allows to determine the q values
For other definitions, see Q value

Q values are the difference of energies of the parent nuclides to the daughter nuclides.
 in present case. The values of q are illustrated in Table 6. As can be seen for neat PPS, q is estimated to be 5.8 kcal [mol.sup.-1], which is some what lower than reported value for 6-7 kcal [mol.sup.-1] (22) and in present case, however, still indicates the moderately stiffer chains for PPS. Nevertheless, from the values of [[sigma].sub.e] and [sigma] from Table 6, it seems that the major contributions to [[sigma].sub.e] arise from the work of chain folding q, over the population of restricted folds, ultimately leading to orthorhombic or·tho·rhom·bic  
Of or relating to a crystalline structure of three mutually perpendicular axes of different length.

 PPS crystal state. In the case of PPS/TLCP composites, the changes in the magnitude of q (5.1-6.8 kcal [mol.sup.-1]) could be attributed to the overall TLCP concentrations dependent modified PPS chain mobility. It seems, therefore, that this difference between two, fold energies can be taken as evidence for the modification in structured folds of PPS in PPS/TLCP composites.


It is evident from this study that the crystallization kinetics in semicrystalline polymer/TLCP composites are a complex phenomena and undoubtedly are highly dependent on the composite composition and the chemical structures of polymeric components. Importantly, the results are very much dependent on the thermal history imposed on the systems. The crystallization rate or crystalline morphology does not show increasing or decreasing linear relationship with simply increasing TLCP content. The data reflect the results of competition between the effect of difference in the nucleation densities of the sized TLCP nematic domains or to an increase or decrease in the mobility of the polymer chains because of the TLCP phase (or both).

In this investigation, the contrasting effects of the presence of TLCP as a second immiscible component in PPS/ TLCP composites on the melting and the isothermal crystallization behavior of PPS were investigated. From the results, it can be concluded that the melting and the crystallization of PPS in PPS/TLCP composites are affected by addition of TLCP and observed to be highly sensitive Adj. 1. highly sensitive - readily affected by various agents; "a highly sensitive explosive is easily exploded by a shock"; "a sensitive colloid is readily coagulated"  both to the crystallization temperature as well as to the TLCP content in the composites. The observation of melting endotherms of the composites after isothermal crystallization at the particular crystallization temperature (in the temperature range of 523-533 K) exhibits double melting peaks of PPS in composites. These multiple endotherms are due to the TLCP induced melting of the different PPS crystal perfections and their recognizing during thermal scan. At larger undercooling (523-528 K) the PPS crystals are imperfect due to rapid nucleation out of additional contribution from TLCP-induced state of low mobility. At lower undercooling (531-533 K) both the endotherms marginally shift toward higher temperatures indicating PPS-crystals are now much perfect. However, crystal structure and morphology are still in the reorganization domain in the present temperature range. [T.sub.m.sup.0] values are found to increase with TLCP content in composites.

The most important conclusive observation for the kinetic data is the observed relationship between the crystallization temperature and the composite compositions. Avrami analysis showed that the addition of TLCP into PPS does affect the nucleation process through heterogeneous nucleation followed by a combination of two-dimensional and three-dimensional spherulitic crystal growths depending on the [T.sub.c]. The crystallization rate of PPS in PPS/TLCP composites decreases with increasing TLCP loading in composites. However, for a particular composite it increases with increasing [T.sub.c]. This suggest that in addition to the composite composition, the [T.sub.c] induced mobility is important factor governing the extend of modification of the PPS crystallization behavior in composites. The crystallization activation energy is initially reduced as the TLCP content increases upto 30 wt%, which further decreases with increasing TLCP content in composites. The result clearly indicates that TLCP behaves as a nucleating agent for the crystallization process for PPS.

The fold interfacial free energy and the regime kinetic analysis of the crystallization data obtained for PPS/TLCP composites show that the crystallization occurs in regime II on the large substrates, across the [T.sub.c] range covered in this study. As the fold surface free energy [[sigma][sigma].sub.e] is strongly correlated with the work of chain folding the results suggest that in general the higher TLCP loading is more of a hindrance to folding of PPS chains which is again affected by the [T.sub.c].


The authors express their appreciation to Dr.(Mrs.) Jyoti P. Jog of NCL NCL Norwegian Cruise Line
NCL New Caledonia (ISO Country code)
NCL National Consumers League (Washington, DC)
NCL Neuronal Ceroid Lipofuscinosis (adult type) 
, Pune, India, for providing polarizing optical microscope optical microscope

See under microscope.


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A. K. Kalkar, V. D. Deshpande, M. J. Kulkarni

Department of Physics, Institute of Chemical Technology, University of Mumbai Most of the colleges in the city of Mumbai (Bombay) and the districts of Thane, Raigad, Ratnagiri and Sindhudurg are affiliated to the University of Mumbai. The University of Mumbai offers Bachelors, Masters and Doctoral degrees to students. , Matunga, Mumbai 400 019, India

Correspondence to: A.K. Kalkar; e-mail;

Contract grant sponsor: All India Council for Technical Education The All India Council for Technical Education (AICTE), is the statutory body established for proper planning and co-ordinated development of the technical education system in India. It was established in November, 1945.  (AICTE AICTE All India Council Technical Education ), Govt. of India, New Delhi New Delhi (dĕl`ē), city (1991 pop. 294,149), capital of India and of Delhi state, N central India, on the right bank of the Yamuna River. ; contract grant number: NO.F. 8017/RDII/BOR/95/Rec.586/TAPTEC/1997.

DOI (Digital Object Identifier) A method of applying a persistent name to documents, publications and other resources on the Internet rather than using a URL, which can change over time.  10.1002/pen.21263

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Title Annotation:thermotropic liquid crystalline copolyester
Author:Kalkar, A.K.; Deshpande, V.D.; Kulkarni, M.J.
Publication:Polymer Engineering and Science
Article Type:Technical report
Date:Feb 1, 2009
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