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The platforms described in the previous chapter access a range of states via a number of thermodynamic loading paths taken by a material as it deforms. Some load to the elastic limit, some up to the finis extremis where electronic bonding changes its nature, and some beyond that. What follows will concern loading from the elastic limit to the point at which ambient descriptions of strength cease to apply. A few of the loading paths necessary to define an equation of state for a material are shown in the schematic of Figure 4.1. There are a range of outputs which may be sensed to give insight into the response of materials under load. Experiments should aim to map their states beyond the yield point statically and dynamically. In the first case they induce an ideal stress state to define operating mechanisms represented in suitable models, which are later tested against other loading down more complex paths. Thus shock experiments map out Hugoniot curves but can also yield information that allows one to deduce compression isotherms and isentropes. Isotherms are generally measured using static compression experiments at some fixed temperature in the diamond anvil cell (DAC). To briefly recap, the isentrope generally lies between the isotherm and Hugoniot curves and is in fact tangent to the Hugoniot at the common starting state. Although shock experiments generally yield only a final P–V state on the Hugoniot, an ideal isentropic compression experiment (ICE) yields a continuous locus of points along a different loading path. Although not precisely following the isentrope, it is certainly possible to load more slowly and avoid the adiabatic conditions of shock, and so this is better dubbed shockless loading. To record this data demands sensors capable of acquiring pressure, density and temperature as a function of time, which requires sub-nanosecond data collection under the fastest loadings. To measure deviatoric quantities entails measures of the stress state in the target which is itself directional. Thus a series of accurate, time-resolved sensors has been developed to make such measurements in these experiments. Another means of recording the data is to use a quantitative imaging technique (such as X-rays) to deduce state parameters from the flow. Imaging itself allows the visualisation of geometries changing under load whist offering non-invasive measurements of flow parameters.
In the text a range of problems encountered by materials under extreme conditions has been described. To understand them, knowledge of the response of structure at the microscale is necessary and this has been assembled in the ambient state by materials science. Chemical reaction is possible in some substances in the condensed phase, and these are described as energetic, but in general physical deformation precedes chemistry in loaded materials. A fundamental focus for this field will be to try and understand the nature of the strength of solids. It will become clear that this is a difficult objective since complex behaviour results from the two classes of process that define strain: that in which length or volume changes with constant shape and one in which the shape changes at constant volume.
In what follows the response of these will be followed through from the microstructure at the atomic level to their form at the continuum. The various materials classes – metals, brittle materials, polymers and composites of all three – will be looked at to highlight particular features of their behaviour which go towards defining how the macroscopic boundary conditions of the loading excite response from the individual atomic architectures. The framework to describe observations is materials physics and this will be summarised below to aid the reader. It is by no means complete and much more rigorous texts exist for the student of materials science; however, it serves to allow a reader from an alternative background access to the necessary concepts to make the comments elsewhere in the text more tractable.
To obtain high strength often suggests inorganic and non-metallic materials where hardness provides resistance against high thermal or mechanical loads. In a book concerned with dynamic extremes, these stimuli include materials propelled to impact at high velocity. The design paradigm requires a material to deliver an easily formed structural component capable of resisting impulsive loads of high amplitude and arbitrary duration. At the present time the reality is that these aspirations are only partially met. The response of these materials to idealised one-dimensional loading under shock is not yet understood in full detail and fully three-dimensional loading is only described empirically. Nevertheless the response of glasses and ceramics to dynamic loading has been investigated by the impact community over the past 30 years so that at least a library of data exists. In that time much has been learnt but vital questions remain unresolved, particularly understanding contact, penetration, fragmentation, inelastic behaviour and failure that are encountered in the response of a brittle material to impulsive loading.
Even the qualitative understanding of the response of brittle materials to dynamic loading has not been reflected in advances in constitutive models for them. This results from an incomplete knowledge of operating mechanisms that are consequently not reflected in global models. Further, there is a wide range of microstructures represented in this grouping, ranging from amorphous silicate glasses to polycrystalline ceramics containing both crystalline and amorphous phases. Clearly to construct adequate models for such heterogeneous materials to work on numerical platforms requires a macroscale description of behaviour, yet at present even subscale approaches have not described the processes operating in these heterogeneous media where the phases interact at the mesoscale. It is scale that remains the key frontier that bridges the continuum to microscale behaviour, and it is the mesoscale where the defects that control failure in the bulk are found.
The man-made and the natural environment surrounds man with a wide array of plastics and polymers both natural and man-made. A polymer is a molecule which contains repeated units of a particular chemical base segment, and there are many types found across organic chemistry. A plastic is a term that covers a wide range of mostly synthetic but also some natural organic products that can be moulded or extruded. Thus while all plastics are organic polymers, not all polymers are plastics and in general may need to be modified with other additives to form useful materials. In everyday parlance plastic and polymer are terms often used interchangeably but in fact there are many other types of molecules, both biological and inorganic, that are also polymeric.
The word polymer has ancient Greek roots, compounded from poly (meaning many) and meros (meaning parts or units), whilst plastic has a root that indicates a solid that is malleable being easily shaped or moulded. Natural plastics may originate in biological systems such as tar and shellac, tortoise shell and horns, as well as tree saps that produce amber and latex. These plastics may be processed with heat and pressure into a host of different products. If natural polymers are chemically modified then other plastics result and during the 1800s these processes produced such materials as vulcanised rubber and celluloid. In 1909 a semi-synthetic polymer was produced called Bakelite, soon followed by fibres such as rayon (1911). The ability to work and particularly to cast or mould them to component shapes made plastics increasingly dominant for manufacturing. However, restrictions on supply of natural materials during the Second World War led to the modern predominance of synthetic plastics. This time period saw development of nylon, acrylic, neoprene, polyethylene and many more to replace the natural products that could no longer be imported. Post-war the plastics business has developed into one of the fastest growing industries in the world.