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Monitoring physical and chemical changes during reactive processing
Reactive processing involves the production of a novel polymer as a result of chemical reactions that occur during the processing operation. These changes may be deliberate, as in functionalization, or inadvertent, as in chain scission due to undesired thermo- or mechano-chemistry. Section 1.4 gave the chemical changes to be expected when a thermoplastic polymer is subjected to elevated temperature for a period of minutes in the presence or absence of an oxidative atmosphere (Scott, 1993, Zweifel, 1998). For example, there will be the appearance of higher oxidation states of carbon such as in ether, alcohol, ketone and acid groups. These often accompany chain scission, which occurs during the free-radical-initiated oxidation chain reaction. In addition, there may be other chemical changes, such as grafting and functionalization, in which new chemical species are added to the polymer backbone in the course of the processing operation. The initiation of the oxidation, grafting or functionalization reactions will be through added initiator such as an organic peroxide and the novel chemistry will involve a monomer or other grafting agent, neither of which will necessarily be totally consumed during the reaction sequence. The measurement of the concentration profiles of these reagents as a function of time and, if possible, position in the reaction zone is crucial to the development of an understanding of the link between the chemical and rheological changes of the novel polymer system during processing.
Plastics are the most diverse materials in use in our society and the way that they are processed controls their structure and properties. The increasing reliance on plastics for high-value and high-performance applications necessitates the investment in new ways of manufacturing polymers. One way of achieving this is through reactive processing. However, the dynamics of reactive processes places new demands on characterization, monitoring the systems and controlling the complete manufacturing process.
This book provides an in-depth examination of reactive polymers and processing, firstly by examining the necessary fundamentals of polymer chemistry and physics. Polymer characterization tools related to reactive polymer systems are then presented in detail with emphasis on techniques that can be adapted to real-time process monitoring. The core of the book then focuses on understanding and modelling of the flow behaviour of reactive polymers (chemorheology). Chemorheology is complex because it involves the changing chemistry, rheology and physical properties of reactive polymers and the complex interplay among these properties. The final chapter then examines a range of industrial reactive polymer processes, and gives an insight into current chemorheological models and tools used to describe and control each process.
This book differs from many other texts on reactive polymers due to its
breadth across thermoset and reactive polymers in-depth consideration of fundamentals of polymer chemistry and physics focus on chemorheological characterization and modelling extension to practical industrial processes
The book has been aimed at chemists, chemical engineers and polymer process engineers at the advanced-undergraduate, post-graduate coursework and research levels as well as industrial practitioners wishing to move into reactive polymer systems.
This chapter highlights the importance of chemorheology in determining cure properties of reactive systems. A brief introduction to experimental rheology has been provided in Chapter 3 to provide a baseline knowledge of experimental rheology. In this chapter we examine a description of chemorheology in terms of basic chemorheology, chemoviscosity, gelation and vitrification transitions and ultimate properties. Finally, examples of chemorheological analysis will be discussed. (We will briefly summarize chemorheological data and models in this chapter, but only for reference to chemorheological testing. A more extensive examination of chemorheology and modelling of systems will be presented in Chapter 5.)
Chemorheology
The definition of chemorheology (in this text) is the study of the deformation properties of reactive polymer systems. Figure 4.1 shows a schematic representation of the structural development during thermoset cure.
Step (a) shows unreacted monomers, and cure proceeds to step (b), at which there is the formation of some branched molecules. By step (c) the cure has progressed to the gel point, such that an infinite network is formed across the whole structure. Further cure can occur to point (d), at which the material becomes fully cured and vitrification is reached.
The essential elements of a chemorheological study are
The purpose of this chapter is to provide the background principles from polymer physics and chemistry which are essential to understanding the role which chemorheology plays in guiding the design and production of novel thermoplastic polymers as well as the complex changes which occur during processing. The focus is on high-molar-mass synthetic polymers and their modification through chemical reaction and blending, as well as degradation reactions. While some consideration is given to the chemistry of multifunctional systems, Chapter 2 focuses on the physical changes and time—temperature-transformation properties of network polymers and thermosets that are formed by reactions during processing.
The attention paid to the polymer solid state is minimized in favour of the melt and in this chapter the static properties of the polymer are considered, i.e. properties in the absence of an external stress as is required for a consideration of the rheological properties. This is addressed in detail in Chapter 3. The treatment of the melt as the basic system for processing introduces a simplification both in the physics and in the chemistry of the system. In the treatment of melts, the polymer chain experiences a mean field of other nearby chains. This is not the situation in dilute or semi-dilute solutions, where density fluctuations in expanded chains must be addressed. In a similar way the chemical reactions which occur on processing in the melt may be treated through a set of homogeneous reactions, unlike the highly heterogeneous and diffusion-controlled chemical reactions in the solid state.
Chapters 3 and 4 presented chemical, physical and chemorheological techniques useful for characterizing various reactive polymer systems. This chapter will now focus on a review of chemorheological analyses for a variety of polymer systems, including detailed experimental findings and chemorheological modeling.
Chemoviscosity and chemorheological models
Chemorheology is defined as the study of the viscoelastic behaviour of reacting polymer systems. This involves examining the effects on chemoviscosity of chemical reactions (cure conversion, cure kinetics) and processing conditions (temperatures, shear rates), as well as gelation and vitrification. In Chapter 4 we briefly summarized chemoviscosity models that highlight effects of cure (ηc=ηc(Τ, α)), shear rate (ηsr=ηsr(γ, Τ)) and filler (ηf=ηf(F, Τ, t)) in Tables 4.4–4.6. This chapter will examine the development of chemorheology and chemorheological modelling in more detail by examining the chemorheology and chemoviscosity models of unfilled reactive systems, overviewing the effects of fillers on chemoviscosity and then presenting chemoviscosity data and models for filled systems. It is hoped that, by presenting the data and models in more depth, a better understanding of the chemorheology of systems will be obtained.
Neat systems
Chemorheological models for neat (unfilled) curing systems can be grouped into the following categories:
simple empirical models
Arrhenius models
structural and free-volume models
probability-based and molecular models
Simple empirical models
Malkin and Kulichikin (1991) initially reviewed the rheokinetics of cured polymers and highlighted the first empirical chemorheological models.
This chapter focusses on the physical properties and models of network and reactively modified polymers. Understanding changes in physical properties during curing, in tandem with changes in chemical properties (Chapter 1), and chemorheological properties (Chapter 4), is essential to fully characterizing network and reactively modified polymer systems. This chapter will first give a brief introduction to polymer physics and dynamics before focussing on redefining network and reactively modified polymer systems. Then it will focus on defining the key changes in physical properties during cure. Finally this chapter will focus on key experimental techniques for describing changes in physical properties during cure.
Polymer physics and dynamics
Chapter 1 has already introduced basic concepts of polymers relating to their physical nature, such as crystalline and amorphous regions, molar mass, glass transition and rubbery regions. This section will focus on developing further basic polymer-physics and polymer-dynamics concepts that will be pertinent to reactive polymer systems. Specifically we will be interested in examining the physics behind polymer dynamics — to understand how to characterize the dynamics and stress behaviour of polymers under deformation and flow. This will be essential background for the chemorheology of polymer systems.
Polymer physics and motion — early models
Polymer chains consist of large molecules (macromolecules), which are composed of multiple repetition of one or more species of atoms or groups of atoms that are interlinked.
Sm3+, Ce3+ codoped Al2O3–La2O3–SiO2 glasses were prepared and their luminescence properties were characterized. Blue-cyan to orange-red tunable luminescence was observed from these glasses with different excitation wavelengths ranging from 385 to 410 nm. White light emission with internal luminescence efficiency 42% has been observed using commercially available purple light-emitting-diode excitation. The energy transfer between Ce3+ and Sm3+ has also been investigated from fluorescence decay curves and spectral properties.
In this article, we briefly review a particular approach to fabricate light-emitting diode (LED) structures on the semipolar side facets of triangular GaN stripes grown by selective area epitaxy. This approach enables a significant reduction of the internal piezoelectric fields in the LED's active area, while still maintaining the well-established c-direction as the main epitaxial growth direction for GaN-based devices on large area substrates. For the latter, these internal fields are responsible for the lower efficiency of GaN-based LEDs in the longer (green) wavelength range. The reduced internal fields of such semipolar LEDs can be directly determined by photoluminescence (PL) investigations on pre-biased LED structures and further confirmed by time-resolved PL studies. The epitaxial growth behavior is strongly facet-dependent, leading to different surface flatnesses on different semipolar facets formed by this procedure and different – indium incorporation efficiencies. An increased indium uptake on semipolar {1101} facets as compared to conventional c-plane layers can help to shift the LED emission to longer wavelengths near 500 nm, despite the significantly reduced field-dependent Stark shift, which helps to reach the green wavelength range in polar LEDs.
High-quality SrAl12O19:Pr3+ nanodisks and nanoplates were fabricated via a new processing technique based on a modified polymer steric entrapment method. Serious agglomeration and large particle size distribution of final products, which usually occurred in the conventional method, were eliminated completely. The effects of new synthetic processes on the morphology, crystallization, and yield of products and the relevant mechanisms were discussed. As far as we know, SrAl12O19:Pr3+ nanodisks with mean diameter ∼60 nm and thickness between 5 and 10 nm were successfully synthesized for the first time by this low-cost technique. The new synthetic method may provide a general route to synthesize other refractory mixed-oxide nanocrystals. Photon cascade emission involving transitions 1S0–1I6 followed by 3P0–3H4 in SrAl12O19:1% Pr3+ nanodisks was investigated. Size-effect-induced blue shift of the 4f5d states of Pr3+ was observed in SrAl12O19:1% Pr3+ nanodisks, in which the quantum efficiency was preserved, as in the bulk counterparts.
Many clay-bearing sedimentary stones such as Portland Brownstone will swell when exposed to water, and this can generate damaging stresses as differential strains evolve during a wetting cycle. Current swelling inhibitors, consisting of α,ω-diaminoalkanes, can reduce swelling in Portland Brownstone up to 50%. In this study, through x-ray diffraction and swelling strain experiments, we demonstrate that the α,ω-diaminoalkanes inhibit swelling by substituting for interlayer cations and partially hydrophobicizing the interlayer, then rehydrating on subsequent wetting cycles. We also introduce the copper (II) ethylenediamine complex as a potential treatment for swelling inhibition.
We report on a novel biocompatible hierarchical TiO2 porous coating on the surface of Ti, processed via anodic oxidation. The coating consists of large (∼1–20 μm) pores on the microscale and nanotubes (∼50 nm diameter) on the nanoscale. This structure is exciting because of its potential application as a bioactive coating for Ti bone implants. Surface characterization of the coating showed nanotubes of relatively uniform diameter. The interface between TiO2 nanotubes and Ti, studied by transmission electron microscopy, was incoherent. The tubes were also somewhat interconnected.
Erbium dihydride Er(H,D,T)2 is a fluorite structure rare-earth dihydride useful for the storage of hydrogen isotopes in the solid state. However, thermodynamic predictions indicate that erbium oxide formation will proceed readily during processing, which may detrimentally contaminate Er(H,D,T)2 films. In this work, transmission electron microscopy (TEM) techniques including energy-dispersive x-ray spectroscopy, energy-filtered TEM, selected area electron diffraction, and high-resolution TEM are used to examine the manifestation of oxygen contamination in ErD2 thin films. An oxide layer ∼30–130 nm thick was found on top of the underlying ErD2 film, and showed a cube-on-cube epitaxial orientation to the underlying ErD2. Electron diffraction confirmed the oxide layer to be Er2O3. While the majority of the film was observed to have the expected fluorite structure for ErD2, secondary diffraction spots suggested the possibility of either nanoscale oxide inclusions or hydrogen ordering. In situ heating experiments combined with electron diffraction ruled out the possibility of hydrogen ordering, so epitaxial oxide nanoinclusions within the ErD2 matrix are hypothesized. TEM techniques were applied to examine this oxide nanoinclusion hypothesis.
Alloying effects of iridium on the glass formability (GFA) of the Zr–Ir–Cu–Al system have been investigated, and several new bulk metallic glasses (BMGs) with high GFA have been successfully developed. Additions of Ir in the Zr–Cu–Al system can yield a beneficial distribution in atomic sizes, but the strong chemical interaction of the Zr–Ir atomic pair limits the maximum addable Ir contents and the resultant GFA. Our analyses indicate that the optimum composition for alloying elements is determined by not only topological but also chemical factors. Phase competition upon solidification, rather than effects from individual affecting factors, dictates the GFA of BMG systems.
The structural phase stability and electronic properties of the Ti–Al intermetallic compounds were investigated by means of density-functional theory (DFT) calculations in a generalized gradient approximation. Through comparison of the calculated formation energies of the parent and product phases, an in-depth theoretical understanding of the deformation-induced γ ↔ α2 phase transitions observed previously in TiAl alloys was achieved. The formation energy plays an important role in evaluating the feasibility of these phase transformations during plastic deformation of TiAl alloys. In addition, the density of states (DOS) was also calculated and used to analyze the stability of Ti–Al intermetallic compounds. The reasons for the absence of the deformation-induced (DI)-α2 and DI-γ (L12) phases in underformed TiAl alloys were analyzed.