Sticker shock for optomechanical hardware designed for advanced optical DEMVAL systems can lead to program loss.
In optomechanical design it is important to manage this risk through easily manufacturable and inexpensive hardware to
meet demands of lower budget programs. The optical and optomechanical design teams must work closely to optimize
system design for ease of manufacture, and assembly, while at the same time minimizing the impacts to system
performance. Effective teaming often results in unique/creative design solutions which enable future system
development. Outlined are some novel optomechanical structure concepts, with 5 degrees of freedom (DOF), used to
design a low cost DEMVAL optical system. The concepts discussed include inexpensive repeatable magnetic kinematic
mounts, flexure rings for lens preloading, simplistic drop-in lens housing designs, and adjustable tooling ball metering
rods which accommodate alignment in 5 DOF.
Niobium doped Lead Zirconate Titanate (PZT) with a Zr/Ti ratio of 95/5 (i.e., PZT 95/5-2Nb) is a ferroelectric
with a rhombohedral structure at room temperature. A crystal (or a subdomain within a crystal) exhibits a
spontaneous polarization in any one of eight crystallographically equivalent directions. Such a material becomes
polarized when subjected to a large electric field. When the electric field is removed, a remanent polarization
remains and a bound charge is stored. A displacive phase transition from a rhombohedral ferroelectric phase to
an orthorhombic anti-ferroelectric phase can be induced with the application of a mechanical load. When this
occurs, the material becomes depoled and the bound charge is released. The polycrystalline character of PZT
95/5-2Nb leads to highly non-uniform fields at the grain scale. These local fields lead to very complex material
behavior during mechanical depoling that has important implications to device design and performance.
This paper presents a microstructurally based numerical model that describes the 3D non-linear behavior of
ferroelectric ceramics. The model resolves the structure of polycrystals directly in the topology of the problem
domain and uses the extended finite element method (X-FEM) to solve the governing equations of electromechanics.
The material response is computed from anisotropic single crystal constants and the volume fractions of the
various polarization variants (i.e., three variants for rhombohedral anti-ferroelectric and eight for rhomobohedral
ferroelectric ceramic). Evolution of the variant volume fractions is governed by the minimization of internally
stored energy and accounts for ferroelectric and ferroelastic domain switching and phase transitions in response
to the applied loads. The developed model is used to examine hydrostatic depoling in PZT 95/5-2Nb.
The shape control of flexible mirrors has been studied mainly for edge-supported thin-plate configurations. For applications such as optical reflectors, corner-supported configurations, which allow for paraboloidal geometries, prove more applicable. Moreover, the use of corner supports enables more flexibility and larger achievable deflections than with edge supports. This paper discusses a corner-supported thin rectangular plate actuated by a two-dimensional array of segmented piezoelectric laminated actuators. First, a model determining the deflected shape of a laminate for a given distribution of voltages over the actuator array is derived. Second, the results of the model are shown to agree well with a finite element simulation of the structure. Finally, paraboloidal deflection of a rectangular PVDF laminate is investigated.
This paper presents an experimental and analytical investigation into the mechanical behavior of PZT-5H piezoelectric ceramic. The materia is subjected to cyclic uniaxial compressive stress at a constant electric field bias. The damping characteristics such as fraction of energy absorbed and elastic modulus are evaluated as a function of bias electric field. Increasing the positive electric field increases the specific damping and decreases the elastic modulus. The trend is reversed when the electric field becomes sufficiently high to inhibit the domain wall motion by the mechanical stresses. Measured specific damping values vary form 0.18 to 0.46 depending on the stress amplitude and bias electric field. The corresponding secant modulus varies from 79 to 24 Gpz. The optimum electric field values increase as the stress amplitude increases because the positive electric field and the compressive stress counteract each other in terms of domain wall motion. An analytical model shows that the material's response is proportional to the volume fraction of the domains available for switching and the domain wall pressure difference between positive electric field and compressive stress.
This paper presents an experimental investigation into the damping characteristics of piezoelectric ceramic PZT-5H. The material is subjected to cyclic uniaxial compressive stress (up to 200 MPa) at a constant electric field bias (from 0 to 2 MV/m). The experiments are conducted at 25 degree(s)C, 0 degree(s)C, and 50 degree(s)C. Fraction of energy absorbed (a specific damping capacity_ and elastic modulus are evaluated as a function of bias electric field. For investigated stress amplitudes, the specific damping capacity increases with increasing bias field, reaches a maximum (28-33%) at the optimum field level, and then decreases. The optimum electric field values increase as the stress amplitude increases because the positive electric field and the compressive stress counteract each other in terms of domain wall motion. The damping properties are stable in the investigated temperature range. The piezoceramic is found to have superior damping properties compared to common structural methods.
An ongoing investigation into understanding the nature and mechanics of damage in piezoelectric material under combined cyclic electrical and static mechanical loads is described. The piezoelectric is subjected to large field excursions that are sufficient to cause polarization switching at least around internal anomalies, as well as mechanical stresses with values well below ultimate strength of the material. Experimental work is conducted on PZT-5H with macroscopically engineered dissimilar (180°) domain structures. All samples contain a seed notch to introduce a stress concentration at a specified location and eliminate questions associated with electrode attachment. Results indicate that for specimens undergoing significant domain wall motion the crack initiation occurs after only 20 - 100 cycles while for specimens undergoing small domain wall motion cracks initiate after 800,000 cycles. Compressive mechanical loads are found to retard damage growth. Experimental results are explained with data obtained from a finite element model. The principal conclusion is that domain wall motion on both micro and macro levels is responsible for crack initiation and degradation of the material during cycling loading.
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