Abstract
When the melt of a crystalline polymer is cooled to a temperature between the glass transition and the equilibrium melting point, the thermodynamic requirement for crystallization is fulfilled.
In a crystallizable miscible blend, however, the presence of an amorphous component, either thermoplastic or thermosetting, can either increase or decrease the tendency to crystallize depending on the effect of the composition of the blend on its glass transition and on the equilibrium melting point of the crystallizable component and also on the curing extent and conditions in case of thermosetting amorphous component. The type of segregation of the amorphous component, influenced by parameters such as crystallization conditions, chain microstructure, molecular weight, blend composition, and curing extent, determines to a large extent the crystalline morphology of a crystallizable binary blend. Separate crystallization, concurrent crystallization, or cocrystallization can occur in a blend of two crystallizable components. The spherulite growth of the crystallizable component in miscible blends is influenced by the type and molecular weight of the amorphous component, the former affecting the intermolecular interactions between both components and the latter the diffusion of the amorphous component. The blend composition, the crystallization conditions, the degree of miscibility and the mobility of both blend components, and the nucleation activity of the amorphous component are important factors with respect to the crystallization kinetics. The melting behavior of crystallizable miscible blends often reveals multiple DSC endotherms, which can be ascribed to recrystallization, secondary crystallization, or liquid-liquid phase separation. Complex crystallization behavior develops in miscible blends containing a crystallizable thermoplastic and a curable thermosetting component. That depends on the temperature and time of curing the thermosetting and also on whether crystallization is initiated before, during, or after the curing process.
For the discussion of the crystallization and melting behavior in immiscible polymer blends, a division into three main classes is proposed.
In blends with a crystallizable matrix and an amorphous dispersed phase, both the nucleation behavior and the spherulite growth rate of the matrix can be affected. Nucleation of the matrix always remains heterogeneous; however, the amount of nuclei can be altered due to migration of heterogeneous nuclei during melt-mixing. Blending can also influence the spherulite growth rate of the matrix. During their growth, the spherulites can have to reject, occlude, or deform the dispersed droplets. In general, the major influence of blending is a change in the spherulite size and semicrystalline morphology of the matrix.
A completely different behavior is reported for blends in which the crystallizable phase is dispersed. Fractionated crystallization of the dispersed droplets, associated with different degrees of undercooling and types of nuclei, is the rule. The most important reason is a lack of primary heterogeneous nuclei within each crystallizable droplet. An important consequence of fractionated crystallization may be a drastic reduction in the degree of crystallinity.
When two crystallizable components are blended, a more complex behavior due to the influence of both phases on each other is expected. In general, the discussion for matrix crystallization and droplet crystallization can be combined. However, crystallization of one of the phases can sometimes directly induce crystallization in the second phase. As a consequence, the discussion of blends of this type has been subdivided with respect to the physical state of the second phase during crystallization. The special case of “coincident crystallization,” in which the two phases crystallize at the same time, is discussed. Finally, the effect of compatibilization of crystalline/crystalline polymer blends is briefly reviewed.
A new section has been added, introduced to deal with crystallization phenomena in immiscible polymer blends containing nanoparticles. Recent reports, although few, discuss the effect of nanoparticles on crystallization and melting in immiscible polymer blends.
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Dedication and Acknowledgments
Professor Emeritus Dr. Gabriël Groeninckx would like to dedicate this chapter to all his former master and Ph.D. students, postdocs, and colleagues of the Laboratory for Macromolecular Structure Chemistry of the Catholic University of Leuven (KU Leuven, Heverlee, Belgium) for their valuable contribution in the field of polymer blends and related domains. He also would like to fully express his acknowledgments to the KU Leuven where he spent his scientific career from 1965 to 2010. And last but not least, he also has the great pleasure of dedicating this chapter 5 to his wife Anne-Marie and his children Christine, Filip, and Mark but also to his grandchildren Maartje, Nikolaas, Lineke, Noortje, and Luca. Each of them made him very happy in their own way.
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Glossary
- AN
-
Acrylonitrile
- aPMMA
-
Atactic poly(methyl methacrylate)
- aPS
-
Atactic polystyrene
- BR
-
Butyl rubber
- CPE
-
Chlorinated polyethylene
- DDS
-
4,4′-diaminodiphenylsulfone
- DGEBA
-
Diglycidyl ether of bisphenol A
- DHDPE
-
Deuterated high-density polyethylene
- EBA
-
Ethylene butylacrylate
- EEA
-
Elastomeric copolymer from ethylene and ethyl acrylate
- EGMA
-
Ethylene glycidyl methacrylate
- EPDM
-
Elastomeric terpolymer from ethylene, propylene, and a non-conjugated diene
- EPR
-
Elastomeric ethylene-propylene copolymer
- EPR-g-SA
-
Elastomeric ethylene-propylene copolymer grafted with styrene acrylonitrile
- ER
-
Epoxy resin
- EVAc
-
Poly(ethylene-co-vinyl acetate) (random)
- FVA
-
Poly(vinyl acetate-co-di-n-tetradecyl fumarate) (alternating)
- GMA
-
Glycidyl methacrylate copolymer
- HDPE
-
High-density polyethylene
- iP(p-Me-S)
-
Isotactic copolymer of styrene and p-methyl styrene
- iPEMA
-
Isotactic poly(ethyl methacrylate)
- iPMMA
-
Isotactic poly(methyl methacrylate)
- iPS
-
Isotactic polystyrene
- LDPE
-
Low-density polyethylene
- LLDPE
-
Linear low-density polyethylene
- MA or MAH
-
Maleic anhydride
- MCDEA
-
4,4′-methylenebis(3-chloro-2,6-diethylaniline
- P(4-Me-pentene)
-
Poly(4-methyl pentene)
- P(E)0.43(K)0.57
-
Random copolymer of phenyl ether and phenyl ketone
- P(iPr-vinyl ether)
-
Poly(isopropyl-vinyl ether)
- P(sec-But-vinyl ether)
-
Poly(sec-butyl vinyl ether)
- PA-11
-
Polyamide 11
- PA-12
-
Polyamide 12
- PA-6
-
Polyamide 6
- PA-66
-
Polyamide 66
- PAr
-
Polyarylate
- PBA
-
Poly(1,4.butylene adipate)
- PBT
-
Polybutyleneterephthalate
- PC
-
Bisphenol-A polycarbonate
- PCDS
-
Poly(1,4-cyclohexane-dimethylene succinate)
- PCL
-
Poly-e-caprolactone
- PDPA
-
Poly(2,2-dimethyl-1,3-propylene adipate)
- PDPS
-
Poly(2,2-dimethyl-1,3-propylene succinate)
- PE
-
Polyethylene
- PEA
-
Poly(ethylene adipate)
- PECH
-
Poly(epichlorohydrin)
- PED
-
n-Dodecyl ester terminated poly(ethylene glycol)
- PEE
-
Poly(ester-ether) segmented block copolymers
- PEEEK
-
Poly(ether ether ether ketone)
- PEEK
-
Poly(ether ether ketone)
- PEEKK
-
Poly(ether ether ketone ketone)
- PEG
-
Polyethylene glycol (also PEO)
- PEI
-
Poly(ether imide)
- PEK
-
Poly(ether ketone)
- PEKK
-
Poly(ether ketone ketone)
- PEMA
-
Polyethylmethacrylate
- Penton
-
Poly[3,3-bis(chloromethyl)oxetane]
- PET
-
Polyethyleneterephthalate
- PET-b-PS
-
Block copolymer of PET and PS segments
- Phenoxy
-
Poly(hydroxy ether of bisphenol A)
- PI
-
Di-n-octadecyl ester of itaconic acid
- PI
-
Polyisoprene
- PIB
-
Polyisobutene
- PMMA
-
Polymethylmethacrylate
- POM
-
Polyoxymethylene
- PP
-
Isotactic polypropylene
- PPE, PPO
-
Poly(2,6-dimethyl 1,4-phenylene ether), GE Co. trade name
- PPG
-
Poly(propylene glycol)
- PPS
-
Poly(phenylene sulfide)
- PS
-
Atactic polystyrene
- PSMA
-
Poly(styrene-co-maleic anhydride)
- PVAc
-
Poly(vinyl acetate)
- PVC
-
Polyvinyl chloride
- PVDF
-
Poly(vinylidene fluoride) (sometimes expressed as PVF2)
- PVF
-
Poly(vinyl fluoride)
- PVME
-
Polyvinylmethylether
- RIPS
-
Reaction-induced phase separation
- SAN
-
Poly(styrene-co-acrylonitrile)
- SARAN
-
P(VCl2-VC), P(VCl2-VA), or P(VCl2-AN) random copolymers of vinylidene chloride (VCl2) with vinyl chloride (VC), vinyl acetate (VA), and acrylonitrile (AN), respectively
- SBS
-
Elastomeric styrene-butadiene-styrene triblock polymer (also TR)
- SD
-
Spinodal decomposition
- SEBS
-
Styrene-ethylene/butylene-styrene triblock polymer
- SMA
-
Poly(styrene-co-maleic anhydride)
- sPMMA
-
Syndiotactic poly(methyl methacrylate)
- sPS
-
Syndiotactic polystyrene
- TR
-
Thermoplastic rubber (also SBS)
- UHMWPE
-
Ultra-high-molecular-weight polyethylene
- VDF-HFA
-
Copolymer of vinylidene fluoride and hexafluoro acetone
- VDF-TFE
-
Copolymer of vinylidene fluoride and tetrafluoro ethylene
- VLDPE
-
Very low-density polyethylene
- compat.
-
Compatibilization, compatibilized, etc.
- conc.
-
Concentration
- cryst.
-
Crystallization, crystalline, crystallize
- cte
-
Constant
- DSC
-
Differential scanning calorimetry
- etc.
-
Et cetera
- exp.
-
Exponent
- HM
-
High molecular weight
- LCST
-
Lower critical solution temperature
- O. M.
-
Optical microscopy (also OM)
- phr.
-
Parts per hundred
- [(polymer)]
-
Amount/concentration of the cited polymer
- SALS
-
Small-angle light scattering (also SALLS)
- SAXS
-
Small-angle X-ray scattering
- SEM
-
Scanning electron microscopy
- temp.
-
Temperature
- UCST
-
Upper critical solution temperature
- WAXS
-
Wide-angle X-ray scattering
- WLF
-
Williams, Landel, and Ferry
- C 1, C 2, C 3
-
WLF constants
- C-2
-
Carbon chain with 2 C-atoms; i.e., ethylene
- C-3
-
Carbon chain with 3 C-atoms; i.e., propylene
- C p
-
Heat capacity under constant pressure
- E 1
-
Energy dissipated for rejection of droplets during spherulite growth
- E 2
-
Energy to overcome the inertia of droplets during spherulite growth
- E 3
-
Energy required to form new interfaces when droplets are engulfed
- E 4
-
Energy dissipated for deformation of occluded particles during spherulite growth
- F 12
-
Spreading coefficient
- f z (1)
-
Fraction of dispersed droplets of volume VD that contain z heterogeneities of type 1
- G
-
Isothermal spherulite growth rate
- G o
-
Theoretical spherulite growth rate
- G 1
-
Undisturbed spherulite growth rate of the homopolymer described by the Turnbull-Fisher equation
- M (1)
-
Concentration of heterogeneities of type 1
- MW
-
Molecular weight
- n
-
Avrami exponent
- N
-
Nucleation density
- N/S
-
Nucleation density normalized per unit area
- K
-
Overall crystallization rate
- t 0.5
-
Halftime of crystallization at a fixed T c,iso
- T c
-
Bulk crystallization temperature upon cooling from the melt
- T c o
-
Crystallization temperature of the bulk homopolymer
- T c,cold
-
Cold crystallization temperature
- T c,hom
-
Homogeneous crystallization temperature
- T c,i
-
Crystallization temperature at which heterogeneities of type i become active
- T c,iso
-
Isothermal crystallization temperature
- T c,max
-
Optimal isothermal crystallization temperature which yields the highest overall crystallization
- T g
-
Glass-transition temperature
- T m
-
Measured melting temperature of the crystalline phase
- T m o
-
Theoretical melting temperature for crystalline lamellae of infinite thickness
- T m ′
-
Observed melting temperature of the crystalline phase in blends
- T melt
-
Premelting temperature
- t melt
-
Time the polymer is kept in the melt
- V D
-
Average volume of dispersed polymer droplets
- Vol%
-
Volume percentage
- wt%
-
Weight percentage
- X c
-
Total degree of crystallinity
- y p (m, c)
-
Lateral surface free energy between the crystal and its own melt
- y pn (m)
-
Interfacial energy between the nucleating species and the polymer melt
- y pn (c)
-
Interfacial energy between the nucleating species and the polymer crystal
- z
-
Number of heterogeneities of type 1, inducing crystallization in the bulk polymer at T c o
- ΔE
-
Activation free energy for the transport of chains through the liquid–solid interface
- ΔF
-
Difference of interfacial energies; driving force for rejection, engulfing, and/or deformation of dispersed droplets during spherulite growth
- ΔF *
-
Free energy for the formation of a nucleus of critical size
- ΔH m
-
Total melting enthalpy of the crystalline polymer fraction
- ΔT c,hom
-
Degree of undercooling required for homogeneous crystallization
- ΔT c,i
-
Degree of undercooling required before a heterogeneity of type i can become active
- Δy i
-
Specific interfacial energy difference between a nucleating species of type i and the polymer
- Δy pn
-
Specific interfacial energy difference between a nucleating species and the polymer
- γ PS
-
Interfacial free energy between the crystallizing solid and the inclusions
- γ PL
-
Interfacial free energy between the liquid polymer melt and the inclusions
- σ ο
-
Surface free energy of folding
- σ 1,2
-
Interfacial free energy between two phases of a blend in the melt
- σ i,1
-
Interfacial free energy of an impurity with respect to melt phase 1
- σ i,2
-
Interfacial free energy of an impurity with respect to melt phase 2
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Groeninckx, G., Harrats, C., Vanneste, M., Everaert, V. (2014). Crystallization, Micro- and Nano-structure, and Melting Behavior of Polymer Blends. In: Utracki, L., Wilkie, C. (eds) Polymer Blends Handbook. Springer, Dordrecht. https://doi.org/10.1007/978-94-007-6064-6_5
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