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| ISBN-13: | 9780854048397 |
|---|---|
| Publisher: | RSC |
| Publication date: | 01/22/2008 |
| Edition description: | Second Edition,New edition |
| Pages: | 276 |
| Product dimensions: | 6.30(w) x 9.30(h) x 0.80(d) |
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Rheology for Chemists
An Introduction
By Jim W Goodwin, Roy W Hughes
The Royal Society of Chemistry
Copyright © 2008 JW Goodwin and RW HughesAll rights reserved.
ISBN: 978-0-85404-839-7
CHAPTER 1
Introduction
The study of rheology is the study of the deformation of matter resulting from the application of a force. The type of deformation depends on the state of matter; for example, gases and liquids will flow when a force is applied, whilst solids will deform by a fixed amount and we expect them to regain their shape when the force is removed. In other words we are studying the "handling properties of materials'"'. This immediately reminds us that we must consider solutions and dispersions and not simply pure materials. In fact, the utility of many of the materials we make use of every day is due to their rheological behaviour and many chemists are formulating materials to have a particular range of textures, flow properties, etc. or are endeavouring to control transport properties in a manufacturing plant. Interest in the textures of materials, such as say a chocolate mousse or a shower gel, may be of professional interest to the chemist in addition to natural curiosity. How do we describe these quantitatively? What measurements should we make? What is the chemistry underlying the texture so that we may control it? All these questions make us focus on rheology.
The aim of this text is to enable the reader to gain an understanding of the physical origins of viscosity, elasticity, and viscoelasticity. The route that we shall follow will be to introduce the key concepts through physical ideas and analogues that are familiar to chemists and biologists. Ideas from chemical kinetics, infrared, and microwave spectroscopy are invariably covered in some depth in many science courses and so should aid the understanding of rheological processes. The mathematical content will be kept to the minimum necessary to give us a quantitative description of a process, and we have taken care to make any manipulations as transparent as possible.
There are two important underlying ideas that we shall return to throughout this work. Firstly, we should be aware that intermolecular forces control the way our materials behave. This is where the chemical nature is controlling the physical response. The second is the importance of the timescale of our observations, and here we may observe quite different physical responses when our experiments are carried out at different timescales. The link between the two arises through the structure that is the consequence of the forces and the timescale for changes by microstructural motion resulting from thermal or mechanical energy. What is so exciting about rheology is the insights that we gain into the origins of the behaviour of such a wide variety of systems in our everyday mechanical world.
1.1 DEFINITIONS
1.1.1 Stress and Strain
The stress is simply denned as the force divided by the area over which it is applied. Pressure is a compressive bulk stress. When we hang a weight on a wire, we are applying an extensional stress and, when we slide a piece of paper over a gummed surface to reach the correct position, we are applying a shear stress. We shall focus more strongly on this latter stress as most of our instruments are designed around this format. The units of stress are Pascals.
When a stress is applied to a material, a deformation will be the result. In order to make calculations tractable, we define the strain as the relative deformation, that is, the deformation per unit length. The length that we use is the one over which the deformation occurs. This is illustrated in Figures 1.1 and 1.2.
There are several features of note in Figures 1.1 and 1.2:
1. The elastic modulus is constant at small stresses and strains. This linearity gives us Hooke's law, which states that the stress is directly proportional to the strain.
2. The shear strain, produced by the application of a shear stress σ, is illustrated in Figure 1.2. The lower section of the figure shows the general case where there is no rotation of the principal axes of strain. These are simply the diagonals of the material element, one of which shortens whilst the other lengthens. We will see later how this leads to compressive and extensional forces on pairs of particles as they collide in a flowing system.
3. At high stresses and strains, nonlinearity is observed. Strain hardening (an increasing modulus with increasing strain up to fracture) is normally observed with polymeric networks. Strain softening is observed with some metals and colloids until yield is observed.
4. We should recognise that stress and strain are tensor quantities and not scalars. This will not present any difficulties in this text but we should bear it in mind as the consequences can be dramatic and can be useful. To illustrate the mathematical problem, we can think what happens when we apply a strain to an element of our material. The strain is made up of three orthogonal components that can be further subdivided into components, each of which are lined up with our axes. This is shown in Figure 1.3.
Figures 1.2 and 1.3 show how if we apply a simple shear strain, γ, in our rheometer this is formally made up of two equal components, γxy and γxy. By restricting ourselves to simple and well-defined deformations and flows, i.e. simple viscometric flows, most algebraic difficulties will be avoided but the exciting consequences will still be seen.
1.1.2 Rate of Strain and Flow
When a fluid system is studied by the application of a stress, motion is produced until the stress is removed. Consider two surfaces separated by a small gap containing a liquid as illustrated in Figure 1.4. A constant shear stress must be maintained on the upper surface for it to move at a constant velocity, u. If we can assume that there is no slip between the surface and the liquid, there is a continuous change in velocity across the small gap to zero at the lower surface. Now, in each second the displacement produced is x and the strain is:
γ = x/z (1.1)
and as u = dx/dt, we can write the rate of strain as:
dγ/dt = u/z (1.2)
The terms rate of strain, velocity gradient, shear rate are all used synonymously and Newton's dot is normally used to indicate the differential operator with respect to time. For large gaps the rate of strain will vary across the gap and so we should write:
[??] = du/dz (1.3)
When the plot of shear stress versus shear rate is linear, the liquid behaviour is simple and the liquid is Newtonian with the coefficient of viscosity, η, being the proportionality constant.
When a flow is used that causes an extension of a liquid, the resistance to this motion arises from the extensional viscosity, ηε, and the extension rate is [??]. Extensional flows require an acceleration of the fluid as it thins and so steady flows are never achieved and this means that the microstructural time-scale is particularly important. Many practical applications involve extensional flows, frequently with a shear component. For example, spraying, spreading, and roller coating are common ways to apply products from the food, pharmaceutical, paint and printing industries. Although the analysis may be carried out as if the materials are continua with uniform properties, the control comes from an understanding of the role of molecular architecture and forces.
1.2 SIMPLE CONSTITUTIVE EQUATIONS
1.2.1 Linear and Nonlinear Behaviour
It is a simple matter to write down an algebraic relationship that describes the simpler forms of rheological behaviour. For example: for a Hookean solid
σ = Gγ (1.4)
and a Newtonian liquid
σ = η[??] (1.5)
These equations should fully describe the stress-strain-time relationship for the materials over the full range of response. However, the range over which such linear behaviour is observed is invariably limited. Usually large stresses and strains or short times bring deviations from eqns (1.4) or (1.5).
As the behaviour becomes more complicated more parameters are required to fit the experimental curves. To illustrate this, consider two common equations used to describe shear-thinning behaviour observed in viscometers. Figure 1.5 shows these two responses.
Figure 1.5(a) shows a steady shear-thinning response and the experimental points can be fitted to a simple equation:
σ = Ac[??]n (1.6)
where the two fitting parameters are Ac the "consistency", and n, the "power-law index". This equation is often presented in its viscosity form:
η = Ac[??]n-1 (1.7)
Figure 1.5(b) shows the behaviour of a "Bingham plastic" and the fitting equation is:
σ = ηp[??] + σB (1.8)
Here, the fitting parameters are the slope of the line, (the plastic viscosity, ηp) and the Bingham or dynamic yield stress, (the intercept, σB). Other constitutive equations will be introduced later in this volume as appropriate.
1.2.2 Using Constitutive Equations
The first use that we can make of our constitutive equations is to fit and smooth our data and so enable us to discuss experimental errors. However, in doing this we have the material parameters from the model. Of course it is these that we need to record on our data sheets as they will enable us to reproduce the experimental curves and we will be able to compare the values from batch to batch of a product or reformulation. This ability to collapse more or less complicated curves down to a few numbers is of great value whether we are engaged in production of, the application of, or research into materials.
The corollary is that we should always keep in mind the experimental range. Extrapolation outside that range is unwise. This will become particularly clear when we discuss the yield phenomenon – an area of wide interest in many practical situations. Whatever the origins claimed for these models, they all really stem from the phenomenological study of our materials and so our choice of which one to use should be based on the maximum utility and simplicity for the job in hand.
1.3 DIMENSIONLESS GROUPS
An everyday task in our laboratories is to make measurements of some property as a function of one or more parameters and express our data graphically, or more compactly as an algebraic equation. To understand the relationships that we are exploring, it is useful to express our data as quantities that do not change when the units of measurement change. This immediately enables us to "scale" the response. Let us take as an example the effect of temperature on reaction rate. The well-known Arrhenius equation gives us the variation:
kr = A exp(-Ea/RT) (1.9)
Here kr is the rate of a reaction measured at temperature T. Ea is the activation energy and R is the gas constant. Now RT is the value of thermal energy and so the magnitude of the dimensionless group, (Ea/RT), immediately gives us a feel as to the importance of the activation process. For example, if Ea [much less than] RT, then the activation process will not slow the reaction rate significantly from the fastest possible rate A. On the other hand, if Ea [much greater than] RT, then the reaction rate will be very much slower than A. Mechanistically this reminds us of the Boltzmann energy distribution and stochastic processes. The dimension-less group, {Ea/RT is known as the "Arrhenius group".
Another example from chemical kinetics can be seen in the rate equation for first-order reactions. Here, the equation relating the concentration of a species A at time t, [A] (t) to the reaction time and the initial concentration, [A](0) is:
[A](t) = [A](0) exp (-krt) (1.10)
The rate coefficient, kr, has units of t-1 and so can equally well be thought of in terms of the characteristic time for the reaction to take place. Hence if krt [much greater than] 1, the reaction will be a long way towards completion, whereas if kr t [much less than] 1, very little change will have occurred. Equation (1.10) describes the decay of radioactive elements and 1/kr could be considered as the characteristic time for the relaxation of the element from its active to its nonactive state.
1.3.1 The Deborah Number
Maxwell introduced the idea of viscous flow being the manifestation of the decay of elastically stored energy. If we follow this concept through we will see how a dimensionless group, the Deborah number, De, arises naturally. Let us consider a piece of matter in which all the molecules or particles (either small or large, it makes no difference) have had time to diffuse to some low energy state. Now, if we instantaneously strain (deform) the material, we will store energy because the structure is perturbed and the molecules are in a higher-energy state. As we hold the matter in this new shape, we find it becomes easier as the molecules diffuse until an equivalent low-energy state to the initial one has been achieved although the original shape has been lost, i.e. viscous flow has occurred. We can define the characteristic time for this process to occur as the stress relaxation time, τ of the material. Now the Deborah number is:
De = τ/t (1.11)
The relaxation of the stress resulting from a step strain can be observed experimentally and we see that it is the result of diffusive motion of the microstructural elements. Although we can have a mechanistic picture, what does this mean in terms of our measurements? We have the very striking result that our material classification must depend on the time t, i.e. the experimental or observation time. Hence, we can usefully classify material behaviour into three categories:
De [much greater than] 1 solid-like
De ~ O(1) viscoelastic
De [much less than] 1 liquid-like
The most frequently quoted example to illustrate this behaviour is the children's toy "Silly Putty" which is a poly(dimethyl siloxane) polymer. Pulled rapidly it shows brittle fracture like any solid and if pulled slowly it flows as a liquid. The relaxation time for this material is ~ 1 s. After t = 5τ the stress will have fallen to 0.7% of its initial value so the material will have effectively "forgotten" its original shape. That is one could describe it as having a "memory" of around 5 s (about that of a mackerel!). Many other materials in common use have relaxation times within an order of magnitude or so of 1 s. Thickened detergents, personal care products and latex paints provide examples. It is of course no coincidence and this timescale is frequently deliberately chosen by formulation adjustments. The reason is that it is in the middle of our, the human, timescale. Our nervous system responds over the timescale of ~ 1 ms to ~ 1 ks and so, if a material has relaxation time within that region, we will observe an "interesting" or useful texture. Reiner pointed out that our observation time could be quite long with some material, set concrete for example, and so ultimately our definition of solid-like can become one of practical rather than philosophic origin.
1.3.2 The Péclet Number
Although a mechanism for stress relaxation was described in Section 1.3.1, the Deborah number is purely based on experimental measurements, i.e. an observation of a bulk material behaviour. The Péclet number, Pe, though is determined by the diffusivity of the microstructural elements, and is the dimensionless group given by the timescale for diffusive motion relative to that for convective or flow. The diffusion coefficient, D, is given by the Stokes-Einstein equation:
D = kB T/6πη0a (1.12)
where kB is the Boltzmann constant, η0 is the viscosity of the liquid medium, and a is the radius of the diffusing moiety, whether a molecule or a particle. This has dimensions of m2s-1 We can use eqn (1.12) to estimate the time taken for the diffusing moiety to move a characteristic distance. It makes sense to choose the radius as this distance and this gives us the Einstein-Smoluchowski equation:
[MATHEMATICAL EXPRESSION NOT REPRODUCIBLE IN ASCII]
and so
[MATHEMATICAL EXPRESSION NOT REPRODUCIBLE IN ASCII] (1.13)
Now the characteristic time for shear flow is the reciprocal of the shear rate. This is the time taken for a cubic element of material to be transformed to a parallelogram with angles of 45° (i.e. the time for unit strain to be applied) as shown in Figure 1.6. The Péclet number can now be written:
[MATHEMATICAL EXPRESSION NOT REPRODUCIBLE IN ASCII] (1.14)
Now, an interesting problem arises when we consider solutions or colloidal sols where the diffusing component is much larger in size than the solute molecules. In dilute systems eqn (1.14) would give an adequate value of the Péclet number but not so when the system becomes concentrated, i.e. the system itself becomes a condensed phase. The interactions between the diffusing components slow the motion and, as we shall see in detail in Chapter 3, increase the viscosity. The appropriate dimensionless group should use the system viscosity and not that of the medium and now becomes:
Pe = 6πa3σ/kBT (1.15)
where the shear stress, σ = η[??, has been used to make a clear distinction from eqn (1.14). Of course for a simple system, such as cyclohexane in decane for example, eqns (1.14) and (1.15) would give the same result as the intermolecular interactions between the species are similar, and the viscosity of a mixture of the two is similar to that of the two components.
However, we shall use eqn (1.15) throughout this work as the use of the stress indicates the importance of the interactions and gives a useful approximation to the change in diffusivity of the components of the material.
1.3.3 The Reduced Stress
The reduced stress, σr was introduced by Krieger from a dimensional analysis and has the form:
σr =a3σ/kBT (1.16)
(Continues...)
Excerpted from Rheology for Chemists by Jim W Goodwin, Roy W Hughes. Copyright © 2008 JW Goodwin and RW Hughes. Excerpted by permission of The Royal Society of Chemistry.
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Table of Contents
Contents: Chapter 1: Introduction; 1.1 Definitions; 1.1.1 Stress and Strain; 1.1.2 Rate of Strain and Flow; 1.2 Simple Constitutive Equations; 1.2.1 Linear and Non-linear Behaviour; 1.2.2 Using Constitutive Equations; 1.3 Dimensionless Groups; 1.3.1 The Deborah Number; 1.3.2 The PÚclet Number; 1.3.3 The Reduced Stress; 1.3.4 The Taylor Number, NTa; 1.3.5 The Reynolds Number, NRe; 1.4 Macromolecular and Colloidal Systems; 1.5 References; Chapter 2: Elasticity: High Deborah Number Measurements; 2.1 Introduction; 2.2 The Liquid-Solid Transition; 2.2.1 Bulk Elasticity; 2.2.2 Wave Propagation; 2.3 Crystalline Solids At Large Strains; 2.3.1 Lattice Defects; 2.4 Macromolecular Solids; 2.4.1 Polymers - An Introduction; 2.4.2 Chain Conformation; 2.4.3 Polymer Crystallinity; 2.4.4 Crosslinked Elastomers; 2.4.5 Self-associating Polymers; 2.4.6 Non-interactive Fillers; 2.4.7 Interactive Fillers; 2.4.8 Summary of Polymeric Systems; 2.5 Colloidal Gels; 2.5.1 Interactions Between Colloidal Particles; 2.5.2 London - van der Waals' Interactions; 2.5.3 Depletion Interactions; 2.5.4 Electrostatic Repulsion; 2.5.5 Steric Repulsion; 2.5.6 Electrosteric Interactions; 2.6 References; Chapter 3: Viscosity: Low Deborah Number Measurements; 3.1 Initial Considerations; 3.2 Viscometric Measurement; 3.2.1 The Cone and Plate; 3.2.2 The Couette or Concentric Cylinder; 3.3 The Molecular Origins on Viscosity; 3.3.1 The Flow of Gases; 3.3.2 The Flow of Liquids; 3.3.3 Density and Phase Changes; 3.3.4 Free Volume Model of Liquid Flow; 3.3.5 Activation energy Models; 3.4 Superfluids; 3.5 Macromolecular Fluids; 3.5.1 Colloidal Dispersions; 3.5.2 Dilute Dispersions of Spheres; 3.5.3 Concentrated Dispersions of Spheres; 3.5.4 Shear Thickening Behaviour in Dense Suspensions; 3.5.5 Charge Stabilised Dispersions; 3.5.6 Dilute Polymer Solutions; 3.5.7 Surfactant Solutions; 3.6 References; Chapter 4: Linear Viscoelasticity I Phenomenological Approach; 4.1 Viscoelasticity; 4.2 Length and Timescales; 4.3 Mechanical Spectroscopy; 4.4 Linear Viscoelasticity; 4.4.1 Mechanical Analogues; 4.4.2 Relaxation Derived as an Analogue to 1 st Order Chemical Kinetics; 4.4.1 Oscillation Response; 4.4.2 Multiple Processes; 4.4.3 A Spectral Approach To Linear Viscoelastic Theory; 4.5 Linear Viscoelastic Experiments; 4.4.1 Relaxation; 4.4.2 Stress Growth; 4.4.3 Antthixotropic Response; 4.4.4 Creep and Recovery; 4.4.5 Strain Oscillation; 4.4.6 Stress Oscillation; 4.6 Interrelationships Between the Measurements and the Spectra; 4.6.1 The Relationship Between Compliance and Modulus; 4.6.1 Retardation and Relaxation Spectrum; 4.6.2 The Relaxation Function and the Storage and Loss Moduli; 4.6.3 Creep and Relaxation Interrelations; 4.7 Applications to the Models; 4.8 Microstructural Influences on the Kernel; 4.8.1 The Extended Exponential; 4.8.2 Power law or the Gel Equation; 4.8.3 Exact Inversions from the Relaxation or Retardation Spectrum; 4.9 Non-shearing Fields and Extension; 4.10 References; Chapter 5: Linear Viscoelasticity II. Microstructural Approach; 5.1 Intermediate Deborah Numbers; 5.2 Hard Spheres and Atomic Fluids; 5.3 Quasi-hard Spheres; 5.3.1 Quasi-hard Sphere Phase Diagrams; 5.3.2 Quasi-hard Sphere Viscoelasticity and Viscosity; 5.4 Weakly Attractive Systems; 5.5 Charge Repulsion Systems; 5.6 Simple Homopolymer systems; 5.6.1 Phase Behaviour and the Chain Overlap in Good Solvents; 5.6.2 Dilute Solution Polymers; 5.6.3 Undiluted and Concentrated Non-entangled Polymers; 5.6.4 Entanglement coupling; 5.6.5 Reptation and Linear Viscoelasticity; 5.7 Polymer Network Structure; 5.7.1 The Formation of Gels; 5.7.2 Chemical Networks; 5.7.3 Physical Networks; 5.8 References; Chapter 6: Non-Linear Responses; 6.1 Introduction; 6.2 The Phenomenological Approach; 6.2.1 Flow Curve4s; Definitions and Equations; 6.2.2 Time Dependence in Flow and The Boltzmann Superposition Principle; 6.2.3 Yield Stress Sedimentation and Linearity; 6.3 The Microstructural Approach - Particles; 6.2.1 Flow in Hard Sphere Systems; 6.2.2 The Addition of a Surface Layer; 6.2.3 Aggregation and Dispersion in Shear; 6.2.4 Weakly Flocculated Dispersions; 6.2.5 Strongly Aggregated and Coagulated Systems; 6.2.6 Long Range Repulsive Systems; 6.2.7 Rod-like Particles; 6.4 The Microstructural Approach - Polymers; 6.4.1 The Role of Entanglements in Non-linear Viscoelasticity; 6.4.2 Entanglements of Solution Homopolymers; 6.4.3 The Reptation Approach; 6.5 Novel Applications; 6.5.1 Extension and Complex Flows; 6.5.2 Uniaxial Compression Modulus; 6.5.3 Deformable Particles; 6.5 References; Subject Index;What People are Saying About This
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