International Journal of Spectroscopy

Volume 2010 (2010), Article ID 206362, 13 pages

http://dx.doi.org/10.1155/2010/206362

## High Temperature Resonant Ultrasound Spectroscopy: A Review

Department of Physics and Astronomy, National Center for Physical Acoustics, The University of Mississippi, MS 38677, USA

Received 6 August 2010; Accepted 24 November 2010

Academic Editor: Jaan Laane

Copyright © 2010 G. Li and J. R. Gladden. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

#### Abstract

The measurement of elastic constants plays an important role in condensed matter physics and materials characterization. This paper presents the resonant ultrasound spectroscopy (RUS) method for the determination of elastic constants in a single crystal or amorphous solid. In RUS, the measured resonance spectrum of a properly prepared sample and other information such as geometry, density, and initial estimated elastic constants are used to determine the elastic constants of the material. We briefly present the theoretical background and applications to specific materials; however, the focus of this review is on the technical applications of RUS, especially those for high-temperature measurements.

#### 1. Introduction: Elastic Constants and Measurement Methods

The elastic response of a solid is determined by the full set of independent elastic constants, which are a measure of the material’s interatomic forces and, specifically, the curvature of the potentials around the equilibrium spacing. Elastic constants are a sensitive probe into the atomic environment of a crystal lattice, and changes in elastic constants are a useful tool for investigating critical phenomenon. Elastic constants are involved in many fundamental phenomena in solid-state physics: they are important parameters in equations of state, lattice dynamics, and phonon spectra; they are also linked to other quantities in thermodynamics such as coefficient of thermal expansion, Debye temperature, Grüneisen parameter, and so on. The measurement of elastic constants is of interest not only to engineers and materials scientists, but also to researchers in many areas of fundamental and applied physics.

Numerous theoretical and experimental methods are available for evaluating elastic constants. If the equation for the interatomic potential is known, the elastic constant can be calculated from first principles. The results from *ab initio* calculations for some crystalline solids with known atomic structures and potentials are usually in reasonable agreement with the experimental data. For simple, accurate and efficient determination of elastic properties of materials, various ultrasonic and nonultrasonic experimental techniques are often preferred.

Many experimental techniques [1–3] have been developed and employed for measuring the elastic constants of different types of materials. The selection of technique depends on factors such as the composition, structural characteristic and size of the sample, desired accuracy of measurement, and, of course, the availability of equipment and expertise. Various common techniques can be roughly categorized according to the major parameters that are evaluated or the primary equipment that are used (Table 1). The accuracy of a given experimental method depends on many factors other than the fundamental nature of the method itself. However, frequencies are one of the easiest quantities to measure, and resonance methods typically depend on many more frequency measurements than variables being determined. For these reasons, RUS has emerged as one of the most accurate methods for elastic constant measurements.

In principle, elastic constants can be readily computed from the stress and strain, which are related by the generalized Hooke's law throughout the elastic range. Samples of relatively large sizes are either pulled, compressed, bent, or twisted by known stresses, and the strains are measured by a variety of techniques such displacement measurement by a strain gauge. When a sample can be conveniently put into some kind of vibration, a quasistatic method is often preferred over the static method in strain and stress measurements. In the quasistatic method, the sample is subject to a small, harmonic external force, and frequency of the external force is much lower than the natural resonance frequencies of the sample itself. Both static and quasi-static stress-strain methods are widely used for characterizing materials for engineering applications. It is important to note that because the time scales of static and quasi-static methods are typically long compared to thermal time scales, the sample has time to come to thermal equilibrium in response to the stress, and thus the moduli obtained are *isothermal* moduli. This is in contrast to the much shorter time scales in ultrasonic measurements which produce *adiabtic* moduli.

New and exotic materials of crystal forms are often small, and the number of independent elastic constants increases as crystalline symmetry decreases. Due to their high efficiency and accuracy, ultrasonic methods are better suited to evaluating elastic properties of these materials. Ultrasonically, an elastic constant can be measured in two ways: one is by measuring the speed of sound, which is related to the relevant elastic constant component; the other is by measuring the free vibration frequencies, which depend on sample density, dimensions, and elastic constants. Elastic constants can be determined from the ultrasonic wave velocities in various directions in a crystal [4]. In the linear regime, the general relationship between the speed of sound in a crystal, the material density, and its elastic constants is governed by the following equation: where is the speed of sound, is the component of the elastic constants relevant to (i.e., for a shear wave, would be the relevant constant), and is the material density. The pulse-echo method is the most commonly used method of measuring speed of sound in homogeneous and anisotropic materials [4, 5]. In the pulse-echo method, good acoustic coupling or even bonding between the sample and transducer is required. To obtain all the elastic constants of a crystal, the same sample must be repeatedly cut along different principal axes of the crystal lattice and bonded to the transducer, or multiple samples are needed. This is rather labor intensive, especially for low-symmetry crystals. The lack of suitable high-temperature piezoelectric transducers or stable high-temperature couplants prevents the pulse-echo method from being a robust method for elastic constant measurement in such extreme environments.

Resonance methods have been useful tools for measuring elastic properties of solid materials for many years. An elastic body resonates when the frequency of the external force matches one of the natural frequencies of the body. The response of the body during resonance is amplified by roughly the quality factor (, where is the peak width at half magnitude) and can be easily detected by piezoelectric transducers. Several lower normal modes for a particular parallelepiped sample are demonstrated in Figure 1. These free-vibration frequencies, along with dimensions and mass of the sample, can be used to infer the elastic properties of the material. This is the so-called “inverse” problem—inferring elastic constants from measured free-vibration frequencies. The solution of the inverse problem relies on solving the “forward” problem first, that is, to compute its normal modes from the known characteristics of an elastic body. Early resonance techniques were largely confined to large-sized samples with regular geometries such as a sphere for which analytical solutions for the associated forward resonance problems were available [6–8]. The lack of exact solutions to the problem of the free vibrations of an elastic solid of general shape and crystallographic symmetry greatly limited the scope of resonance methods until high-speed computers became common.

Early researchers [9, 10] attempted to use the Rayleigh-Ritz variational technique [11] to calculate the natural vibration frequencies of parallelepipeds. Demarest [12] developed a more accurate method called “cube resonance” for solving the forward problem using the Rayleigh-Ritz method, and this method was used for elastic constant determination with limited success. The cube resonance method was further extended by Ohno [13] to the determination of elastic constants of single crystals. Ohno called his method “rectangular parallelepiped resonance” and it is abbreviated as RPR. Subsequently, researchers advanced the RPR method and applied it to the determination of elastic constants of solids [14–25].

When Migliori and Maynard examined the history of the modern resonant ultrasound spectroscopy (RUS) method [26], they found that a milestone in RUS was the identification of a simple set of basis functions—the products of powers of the Cartesian coordinates by Visscher et al. [27]. This set of basis functions can be applied to many geometries and general anisotropic materials with great accuracy and flexibility. With this breakthrough in solving the forward problem and the wide availability of computing resources, RUS was soon accepted as a useful technique for determining elastic constants of materials, particularly small crystalline solids [2, 28]. RUS methods have been refined and extended over the past several decades to include measurements in extremely low and high temperatures, high pressures, high magnetic fields, as well as heterogeneous samples composed of thin films deposited on a substrate [13, 18, 26, 28–32].

#### 2. Theoretical Method

Two problems, a “forward” and an “inverse” problem, are involved in computing (estimating to be exact) the elastic constants of a solid from the measured spectrum. The forward problem involves computing the spectrum from known parameters of dimensions, density, and initial estimated values for elastic constants; the so-called inverse problem involves determining all independent elastic constants from the experimentally obtained spectrum. The forward problem is presented first.

##### 2.1. Linear Elasticity Theory Primer

The linear theory of elasticity has been well treated in detail in many classical textbooks [33–36]. When the body of a solid material is deformed under external forces, a point (with components ) in the undistorted body moves to a new location (with components ). The displacement of this point due to the deformation is then given by the vector , which we shall denote by The is called the displacement vector. Since the vector is itself a function of , this implies that a small deformation of an elastic body can be written as where the second subscript denotes a partial derivative has been performed with respect to the direction indicated (i.e., ). Rewrite (3) into symmetrical and antisymmetric components where the Einstein summation convention (summation over repeated indices) is used here. The second term represents a solid body rotation, which is independent of any elastic deformation so it can be dropped. We define the strain as where it is assumed that the strains are small so that second-order terms may be neglected. A strain tensor represents the distortion produced in the body by the applied forces. Note that the strain tensor is symmetric so there are only six independent components. The stress is a measure of the intensity of total internal forces when the body of a solid material is deformed. The components of the forces applied to an imaginary surface inside a solid can be written as are the components of the forces acting on the small surface of ; is the stress tensor having units of force per unit area. The components of stress tensor acting on a small element are demonstrated in Figure 2. For a solid in static equilibrium, the net torque acting upon the body is zero, requiring the stress tensor to be symmetrical, that is, Similar to the strain tensor, there are only six independent components in the stress tensor.

In linear elasticity theory, each stress component can be expressed as a linear combination of the strain components. The stress and the strain are related by the generalized Hooke's law where are components of the elastic stiffness tensor. The symmetries in the strain and the stress reduce 81 different entries in the elastic tensor 36 independent elements. In the linear regime, the potential energy must be quadratic in the strain. This reduces the number of independent elements to 21. This number can be further reduced by the crystallographic symmetries imposed by the material itself. In the literature, the elastic constants are often written in the reduced index form. Voigt notation is the standard mapping for tensor indexes (; ; ; ; ; ). The cubic system is the simplest anisotropic system, there are only three independent elastic constants (, , and ). Note we use a lowercase when denoting the full fourth rank stiffness tensor and capital when discussing the reduced notation form. Isotropic materials have only two independent elastic constants, which are usually expressed as the first-order elastic moduli: Young's modulus (E) and Poisson's ratio (). However, the alternative elastic constants bulk modulus (K) and/or shear modulus (G) can also be used. Table 2 lists the arrays of reduced elastic constants for various crystal symmetries.

##### 2.2. Computation of Resonance Frequencies

The calculation of vibration modes of elastic objects with free boundaries is a classic problem in mechanics. Unfortunately, exact analytical solutions exist for only a few cases such as an isotropic sphere and certain modes of a parallelepiped [7]. In most cases, approximation methods such as finite element method (FEM) or Rayleigh-Ritz method must be used for estimating the eigenfrequencies of normal modes. FEM allows the determination of eigenfrequencies for an arbitrary shape of sample made of heterogeneous, anisotropic materials such as layered composite materials. FEM is more general and usually requires more computing time [37]. The Rayleigh-Ritz method [11] is a widely used, classic method for calculating the approximate natural vibration frequencies of a system. The application of the Rayleigh-Ritz method in RUS calculation is based on the Hamilton's principle of least action that the Lagrangian of a system is stationary with respect to small perturbations in the eigenfunctions. The potential and kinetic energy can be expressed in terms of a displacement field . The potential energy density is and the kinetic energy density for a normal mode is where an exp() time dependence has been assumed and first derivatives with respect to time have been performed (). The Lagrangian is defined as . According to the Hamilton's principle, the time integral of the Lagrangian is a constant of motion, that is The displacement field can be approximated by an expansion of some suitable set of basis functions: where is a set of nonnegative integers. Substituting the expression above into the Lagrangian, we get

Writing the above compactly in the matrix format: where both and are matrices, and have elements, respectively,

The requirement that Lagrangian is stationary, that is, the variations of Lagrangian with respect to (any combination of ) is zero, allows us to cast the problem in the matrix eigenvalue form: The components of the vector are the expansion coefficients, and the eigenvalues correspond to the square of the angular frequencies of normal modes.

The central part of RUS calculation consists of solving (18) (finding the set of which minimizes the Lagrangian ) and then using the computed eigenvalues to “correct” the set of input parameters so as to iterate toward a match between the computed and measured frequencies (eigenvalues). There are standard computer routines for solving such eigenvalue problems. Any computation involving large matrix (typically in RUS) is always time consuming. The symmetries in the sample geometry and elastic constant matrix can be exploited to split large matrices through block diagonalization into smaller ones, and each can be solved independently with significant savings in computation time [13]. A good set of basis functions to approximate the displacement field is important for the RUS calculation. Choice of basis functions and estimation of elastic constants are briefly addressed in the following two sections.

##### 2.3. Choice of Basis Functions

Many functions such as trigonometric functions and Legendre polynomials have been exploited as the basis functions. They are simple, orthogonal, and complete functions but they lack the flexibility to handle a large number of sample shapes. Polynomials are good candidates for basis functions because a simple standard analytical solution exists for the integrals and derivatives of the polynomials, and high-order polynomials can approximate many shapes.

Visscher et al. proposed a simple set of basis functions in a paper published in 1991 [27]: the simple powers of the Cartesian coordinates,
where () are a set of positive integers indexed by *α* with the maximum power set by . This is known as the XYZ algorithm, and it is applicable to various irregular-shaped and anisotropic materials. A typical number of 10 for is numerically adequate to approximate the actual functions and very flexible and convenient to implement for a variety of shapes. The larger the , of course, the more accurately the basis functions mimic the actual normal mode displacements. However, a higher power of does not necessarily yield a better solution. The increased demand in computing power and the digital precision of the computer processors must be considered. Typically, is the limit for a 32-bit computer. A further benefit of an expansion of this form is that integrals and derivatives of this function have the same functional form, only changing the coefficients and powers in a simple way.

##### 2.4. Estimation of Elastic Moduli

The determination of the elastic constants from the measured resonance frequencies is the inverse of the forward problem. The forward calculation described above cannot be mathematically inverted. But, the forward calculation and nonlinear fitting can be used to “invert” the problem. Given a set of measured and estimated parameters, a forward calculation is performed to generate a set of resonance frequencies, which are then compared to the measured values. Parameters are adjusted during each iteration to minimize the error function, which is defined as the sum of the squares of the differences between the calculated and measured frequencies.

The minimization of the error function is a nonlinear least-squares problem. The Levenberg-Marquart (LM) method is a classic algorithm for nonlinear least-squares problems and is typically employed in RUS analysis. The LM algorithm is used to find the set of adjustable parameters which minimizes the sum of squares of the differences between the calculated and measured frequencies where are the measured frequencies, and are the calculated ones. are the weights that reflect the confidence in the measured frequencies. These weights can be any value between 0 and 1 but they are usually all set to one except for the fundamental (lowest frequency) mode. The fundamental frequency consistently does not fit very well. The reason for this is not fully understood; however, there is evidence that it is due to an increased sensitivity to loading effects by the transducers [31]. In nonlinear fitting, appropriate starting values are important for the estimation of the model parameters. In addition to elastic constants, other parameters such as two out of the three dimensions (subject to a constant volume condition) or even Euler angles defining the crystal orientation relative to the sample geometry can be adjustable.

Inverse problems are typically ill-posed. Estimating elastic constants from the measured frequencies is no exception. A computer code was developed by Migliori et al. to handle the inverse problem in RUS [2]. One or more resonance modes may be missed during measurement if the pickup transducer touches the node of a mode, or if the transducer is insensitive to the direction a mode moves. If this occurs, one can identify the missing modes by comparing the measured and calculated frequencies after a few iterations of code. Errors for modes higher than the missing mode tend to be the same sign, either positive or negative. Inserting a missing mode or a place holder in the input file may quickly reduce the error. It is a good practice to start with the first few modes and add more mode(s) gradually. For a geometrically precise (errors in parallelism and perpendicularity of a few parts in 10^{3}), high-Q (a few thousands or higher) sample, the overall RMS error between the calculated and measured frequencies is typically in the range of 0.1–0.3%. Table 3 shows the first 20 modes in a typical “good fit” in RUS calculation for an -type silicon-germanium (SiGe) sample near 500°C.

#### 3. Experimental Methods

##### 3.1. Introduction

RUS involves the study of resonances of a properly prepared sample. A carefully polished sample, often a rectangular parallelepiped, is placed between a pair of acoustic transducers, one drives the sample in a swept-frequency continuous wave (CW) mode, the other detects the sample response. When the drive frequency matches a natural vibration frequency of the sample, the surface displacement amplitudes increase. The amount of increase depends on the quality factor () of the resonance, which is associated with the internal friction at that particular resonance frequency. RUS offers the advantages of point contact or loose coupling over the pulse-echo method, and can obtain all elastic constants in one measurement. The sample peaks in the frequency domain are fit with a Lorentzian line shape to extract the center frequencies and quality factors. A complete vibration spectrum comprises the ordered list of these measured vibration frequencies of the sample. The measured spectrum is then compared to a spectrum computed from known parameters of dimensions, density, and initial values for elastic constants, which are adjusted in a least-squares sense to best fit the measured data. A block diagram of RUS is given in Figure 3.

The RUS code treats a variety of sample geometries but parallelepipeds remain as the most common ones. Raw materials of any geometry can be cut into parallelepiped shape using, low-speed diamond saw. The parallelepiped specimens are polished using a lapping machine. The detailed procedures for sample preparation can be found in the literature[31, 38, 39].

The piezoelectric effect of crystals and composite materials finds useful applications in the production and detection of sound. Although electromagnetic [40, 41], laser optical [42–46], and other types of transducers [47] have been used for high-temperature RUS measurements, piezoelectric materials are good choices due to their advantages such as efficiency, simplicity, and low design cost.

In a RUS measurement, the absolute amplitude of a resonance depends on many factors such as the amplitude of driving signal and the loading (contact force between the sample and the transducers) to the sample. Although the amplitude information is unreliable and not used in RUS calculation, it is desired that transducers have a wide, flat frequency response in the frequency range of operation. An ultrasonic transducer for RUS measurement differs fundamentally from conventional ultrasonic transducers in which resonances of the transducer itself should be small compared to sample resonances, and if possible, should be kept out of frequency range of operation [48, 49]. Various transduction systems have been used to accommodate samples of various types and sizes in RUS measurement. We present readers a few samples.

Novel and exotic materials in crystal form usually come in small quantities and sizes, and are often quite expensive to synthesize. RUS excels at handling sub-mm-sized small samples. In an ideal RUS measurement, the drive transducer and pickup transducer are in contact with the two diagonally opposite corners of a parallelepiped sample so all resonance modes can be detected. The sharp corners of a mm-sized sample can be easily damaged if held by transducers with hard faces. PVDF film is a flexible, lightweight, and tough plastic material that can be electrically polarized for piezoelectric applications. PVDF film transducers offer advantages of wide frequency and dynamic range over other traditional ceramic transducers, and are particularly suited for handling small crystals with sharp corners. Maynard designed a small transducer cell using PVDF film transducers [28]. When a parallelepiped sample is mounted in this transducer cell, the two diagonally opposite corners of the sample are held between the two flexible transducers. A small transducer cell similar to Maynard's cell has been constructed at the National Center for Physical Acoustics (NCPA). The photograph of the cell is shown in Figure 4. The tension between the sample and transducers can be finely adjusted by advancing the sliding block to adjust the separation between the transducer strips. Due to the close distance between the two parallel PVDF transducers, electrical crosstalk can be troublesome when sample resonances are weak. A piece of grounded copper shield, with a center hole slightly larger than the sample, is placed between the two transducers. This small sample RUS apparatus is also useful for making measurements of heterogeneous samples composed of a substrate and thin film[31, 32, 50].

##### 3.2. High-Temperature Resonant Ultrasound Spectroscopy

RUS is commonly used for characterizing elastic properties of a wide variety of materials at room and low temperatures. Applications at elevated temperatures, however, are relatively rare [51] and have mostly been concentrated in the geophysics community. Some added technical difficulties in high-temperature measurements are (i) sensitivity of most piezoelectric transducers decreases, if not rapidly, with increasing temperature, thus making them unusable above certain temperatures, (ii) strength of the acoustic resonance of most materials becomes weak at high temperatures, and the broadened sample resonances due to increased attenuation and internal friction in materials can make it difficult to separate sample modes; (iii) technical challenges posed by electrical connections, transducer housing, and other related issues need to be considered.

Despite early successes of RUS applications in extreme environments such as high temperatures [15–17, 19, 51–53], recent applications reported in the literature are scarce. Refractory materials such as corundum (Al_{2}O_{3}) and periclase (MgO) can be placed in an open furnace for high-temperature studies. For oxidation-sensitive materials, a sealed system with minimum trace oxygen is required. In order to study high-temperature materials of weak resonances, a specialty transducer system was also developed at NCPA. The system has been used successfully up to 600°C. For higher-temperature measurements, a buffer-rod system was used at temperatures up to 1000°C of the furnace temperature limit.

###### 3.2.1. Inert Gas Flushing System

In high-temperature RUS measurement of oxidation-sensitive materials, a full temperature run can take dozens of hours. To minimize sample exposure to oxygen at high temperatures, an inert gas flushing system is employed at NCPA to maintain a low-oxygen environment during measurement. This system consists of (a) a compressed inert gas source (typically argon), (b) a gas regulator, (c) an oxygen trap, (d) an oxygen trace analyzer, and (e) a copper cooling coil. During measurement, the sample and transducer cell are placed inside the quartz tube, which snuggly runs through the high-temperature tube furnace, and gas flow is maintained at about 1 liter per minute. The schematic diagram of the gas flushing system is given in Figure 5.

###### 3.2.2. Transducer Systems for High-Temperature RUS Measurement

The upper operating temperature of a piezoelectric transducer can be limited by several factors: (i) most materials that exhibit good piezoelectric properties at room or low temperatures lose the piezoelectric effect quickly with increasing temperature; (ii) the operating temperatures in crystals with high Curie temperatures are usually well below their Curie temperatures due to impurities in their crystalline structures; (iii) the upper temperature limit may also be restricted by transducer components such as backing and supporting materials, bonding materials, and electrical connections.

Most common piezoelectric materials such as lead zirconate titanate (PZT) ceramics are not suited for high-temperature applications. Many piezoelectric materials have been investigated for scientific and industrial uses at high-temperatures [54–56]. Several issues need to be considered when applying a piezoelectric material for high temperature applications [54]: the operating temperature of a material is often well below its Curie transition temperature, at which the material loses piezoelectric property; many piezoelectric materials are also pyroelectric, temperature variations may induce charges; dramatically increased electrical conductivity may result in charge drift and partial loss of signal, the conductivity problem is often aggravated in low-oxygen environment. Potential candidates for high-temperature (600°C and above) piezoelectric applications include tourmaline, bismuth titanate (Bi_{4}Ti_{3}O_{12}), gallium orthophosphate (GaPO_{4}), aluminum nitride (AlN), lithium niobate (LiNbO_{3}), lanthanum gallium silicate (langasite, LGS), and lanthanum gallium tantalate (langatate, LGT) [57]. The high Curie temperature of LiNbO_{3}, above 1200°C, along with its wide availability from commercial suppliers, makes it a good candidate for high-temperature RUS applications [58]. Pure LiNbO_{3} crystals with stoichiometric compositions are reported to exhibit remarkable piezoelectric properties even at 900°C [59, 60]; however, typical upper temperature limits for lithium niobate transducers are about 550°C (see below). Single y/36°-cut crystals with chrome/gold deposited on both sides were chosen as the piezoelectric elements for vibration excitation and detection. The mineral-insulated (MI) signal transmission cables made by ThermoCoax provide electrical connections to the piezoelectric elements. These coaxial cables are designed for high-temperature environment (above 1000°C). A silver-filled conductive epoxy (Epo-Tek E2101) is a good conductor at high temperatures and can provide good bonds between the electrode of piezoelectric element and MI cable.

The schematic of this direct-contact transducer probe can be found in Figure 6. The direct-contact scheme has advantages over the buffer-rod system: much improved signal-to-noise ratio (SNR); clean sample resonance signals without additional problematic resonances from the buffer rods. Unfortunately, the piezoelectric lithium niobate loses sensitivity beginning ~600°C. The lithium niobate acoustic transducers were reported be able to operate at temperatures close to the Curie temperature [16, 17]. However, there is no further reported use of LiNbO_{3} for similar resonance measurement at such high temperatures. Many recent evidences in the literature, however, show that the typical upper operating temperature of LiNbO_{3} is about 650°C, which is far below the material's theoretical Curie temperature of above 1200°C [56, 58]. It has been discussed in the literature [56] that this signal deterioration is caused by oxygen loss, and it might have been exacerbated in low-oxygen environment. Other factors such as impurities and crystal stoichiometry may also have some effect [59, 60]. The presence of defects in the crystal lattice can significantly affect the material's piezoelectric properties at high temperatures. The silver-filled epoxy can provide electrical connection and mechanical bond up to 800–900°C range. With new piezoelectric materials of higher operating temperatures, upper operating temperature of a transducer probe with similar design can be pushed to 900°C.

The current restrictions by the piezoelectric elements in the direct-contact transducer system can be overcome using buffer-rod systems [61, 62]. Acoustic buffer rods have long been used for making high-temperature ultrasonic measurement including elasticity measurements [63, 64]. The conventional buffer-rod system makes RUS measurement possible at extremely high temperatures, and such applications have been reported in the literature [19, 51, 52]. The buffer rods, usually made out of materials of low acoustic loss such as metals, ceramics, or fused quartz, serve as waveguides for ultrasound transmission.

A buffer-rod transducer system was constructed at NCPA for high-temperature RUS measurement. In the buffer-rod probe, the piezoelectric element is cemented to one end of a 0.318 cm diameter buffer rod; the other end of the buffer rod is in direct contact with the test sample placed in the high-temperature environment. In operation, the transducer is exposed to a temperature that is significantly lower than that of the sample. A pair of buffer-rod probes are needed for RUS measurement: one to drive the sample, the other to detect the sample resonance. A cage consists of alumina ceramic disks and rods provides structural support for the two buffer-rod probes and the thermocouple wire. The disks and rods are cemented together using high-temperature chemical set cement (Omegabond OB-700). The cage can withstand repeated high temperatures and retain rigidity in the whole operating temperature range up to 1000°C. The resonances of the cage are weak, and this feature is highly desired in RUS measurement. When the whole apparatus is loaded into the tube furnace, flexible high-temperature (rated up to 200°C) coaxial cables are used to connect the piezoelectric elements to coaxial feedthroughs. The flexible cable allows the upper transducer probe to move up and down freely in the cage so no extra force in addition to the weight of the upper transducer probe is exerted on the test sample. The schematic for the buffer-rod system is shown in Figure 6.

The added temperature range afforded by the buffer rod system comes at a cost, however. The acoustic signal transmitted through the long buffer rod loses some strength, and this is particularly detrimental to the measurement of weak resonance signals. Radial resonances of buffer rods can be excited and mixed in with sample peaks, making the identification of sample peaks difficult and time consuming. Lastly, the extra weight of the buffer rod (~7 g) causes a slight upshifting of resonances which is mode dependent, but typically not more than 0.1%. The spectra shown in Figure 6 illustrates these issues.

#### 4. Applications

##### 4.1. Elastic Constant Measurement of Small and Low-Symmetry Crystals

As a versatile tool for charactering elastic properties of solid materials, RUS has found applications in a variety of fields. Materials scientists are interested in mechanical properties of their newly developed and modified materials that are often available in small quantities and sizes. RUS measures mm-sized samples handily [28, 31]. The use of a small sample of a material is more likely to guarantee homogeneity. Thin film materials have been the subject of intense research in recent years, and RUS analysis has been extended to handle heterogeneous samples such as a thin film deposited on a substrate. The knowledge of elastic properties of thin film materials are required for a variety of applications. RUS has been used to study colossal magnetoresistance (CMR) and silicon carbide thin (200–1600 nm) films deposited on a substrate [31, 50].

##### 4.2. Elastic Constant Measurements at High Temperatures

Knowledge of the mechanical properties of materials intended for use in high-temperature environments is required for understanding the fundamental physics of these materials [65] and is crucial information for proper mechanical design. Applications of resonance techniques at elevated temperatures have been reported in the literature [15–17, 19, 51–53, 66]. Early high-temperature RUS applications were mostly limited to the geophysical studies of the Earth. Geophysicists are particularly interested in the elastic behaviors of constituent phases in Earth's mantle at temperatures beyond their Debye temperatures [67]. The high-temperature data of geophysically important minerals is needed for studying the thermal equation of state, the structure, and the composition in the Earth's interior.

Two main transducer systems were used in these high-temperature studies of geophysical materials. An apparatus with piezoelectric transducers was used by Sumino et al. to evaluate the temperature variations of elastic constants of single-crystal forsterite (Mg_{2}SiO_{4}) up to about 400°C [15]. In this apparatus, the sample is in direct contact with the two acoustic transducers, and the load on the sample is kept at minimum using a microbalance. The transducer and sample assembly in a vacuum chamber are heated by an electric furnace. A similar apparatus was reported to obtain the elastic constants of a single crystal forsterite (Mg_{2}SiO_{4}) from room temperature to about 927°C [17], and the elastic constants of a single crystal periclase (MgO) up to 1027°C [16]. In the direct-contact setup, both the sample and transducers experience the same high temperature, so the upper operating temperature is often limited by the piezoelectric elements. For higher-temperature measurement, the transducers need to be placed outside of the extremely high-temperature environment. A buffer-rod RUS apparatus was used for measuring elastic constants of single crystals up to 1552°C in this system [19]. The single crystal corundum (Al_{2}O_{3}) parallelepiped was held between two long, thin alumina buffer rods, which separate the BaTiO_{3} transducers attached at the other ends of buffer rods from the harsh high-temperature environment. The load of the upper buffer rod on the sample was fine adjusted using a beam balance. The buffer-rod system was also used to obtain the elastic constants of single-crystal forsterite (Mg_{2}SiO_{4}) up to 1427°C [21] and periclase (MgO) up to 1527°C [20].

##### 4.3. Temperature-Induced Phase Transition Studies

Elastic constants are a measure of the curvature of the bonding energy within a crystal structure near the minimum and are sensitive probes to any changes in the atomic environment. Subtle changes often missed by other experimental methods can be observed in RUS measurements. Such phase transitions can come in many forms-structural, superconducting, magnetic, charge ordering, glass, and so forth. The measurement of elasticity of a solid as a function of temperature has been a traditional and useful technique for studying temperature-induced phase transitions. The exact nature of the temperature trends of elastic constants near the critical temperature depends on the specifics of the transition. However, they generally are exhibited as either a discontinuous shift in the values of the elastic constants themselves or in the derivative with respect to temperature. Frequency measurements can be as precise as several parts per million in a RUS experiment, making it an extremely *precise* method of determining elastic constants of crystalline and noncrystalline materials. The high precision makes RUS a sensitive and powerful tool for studying various phase transitions [2, 22, 23, 68]. RUS is complementary to other conventional techniques such as X-ray and neutron techniques for phase transition studies.

Migliori et al. successfully studied the elastic behavior of La_{1.86}Sr_{0.14}CuO_{4} near superconducting transition temperature (about 220 K) [23]. A giant softening in accompanied the tetragonal-orthorhombic (TO) structural phase transition (SPT). In addition, they also applied RUS to SPT studies in SrTiO_{3} and La_{2}CuO_{4} [2]. McGuire et al. experimentally investigated phase transitions in superconductor LaFeAsO using various techniques including RUS [69]. An obvious gradual softening in the elastic moduli was observed, and the transition temperature was determined using the temperature derivative of the elastic moduli. Ohno et al. studied the well-known transition in quartz near 573°C using a buffer-rod system [53]. The complete set of elastic constants of *α*- and *β*-quartz were determined as function of temperature, and the softening of elastic constants near the transition temperature was clearly observed.

##### 4.4. Nanostructured Doped Silicon Germanium

Our group has recently concluded a study of doped nanostructured silicon germanium (SiGe) which has potential applications as a high-temperature thermoelectric material [70]. We measured the elastic moduli of both phosphorous doped (-type) and boron-doped (-type) silicon germanium which was fabricated using a hot press technique at the Jet Propulsion Laboratory. The resulting material was polycrystalline with crystallite sizes of about 70 nm, much smaller than an acoustic wavelength (~1.0 mm), so that an isotropic elastic model could accurately be used. The final sample compositions were Si_{0.784}Ge_{0.196}P_{0.020} for the -type samples and Si_{0.787}Ge_{0.197}B_{0.016} for the -type samples. We found a rather dramatic difference in the temperature dependence of the moduli between the - and -type SiGe which is shown in Figure 7. The -type samples show a smooth softening with a slight negative curvature over the entire temperature range with no hysteresis observed upon heating/cooling cycles. The -type sample, however, shows a rather sharp stiffening near 650 K followed by a more pronounced softening beginning at about 800 K during the initial heating. Upon cooling, the moduli smoothly stiffen and ultimately end slightly stiffer after the thermal cycle is complete. If the sample is reheated, the moduli follow the previous cooling trend, the stiffening feature is not repeated.

We attributed the stiffening in the -type sample to precipitation of the phosphorous atoms in Si-Ge matrix. Phosphorous in silicon germanium exhibits a retrograde solubility limit in the range of 600–1273 K [71]. As the phosphorous atoms precipitate out of the Si-Ge, the ratio of Si/Ge-P to Si/Ge-Si/Ge bonds drops as more P atoms are bonded to other P atoms rather than the host matrix, and the Si-Ge to Si/Ge potentials have a sharper curvature than the Si/Ge—P potentials resulting in an overall stiffer material. The precipitation is not reversible in the sense that when the material cools, much of the phosphorous remains precipitated out, and the material is stiffer at room temperature after thermal cycling. This hypothesis was tested by heating the samples to 1275 K for 30 minutes and then air quenching them to room temperature. At this temperature, the solubility is maximum, and the phosphorous redissolves into the Si/Ge matrix. When this heat-treated sample was remeasured using RUS, the temperature dependence of the moduli was precisely repeated—the stiffening was observed on heating and was not observed on cooling. Further evidence for our conclusion comes from electrical resistivity and Seebeck coefficient measurements which show similar anomalies at 650 K and hysteresis in the -type samples but not the -type. This particular application of RUS exemplifies the wealth of information which can be derived from elastic constant measurements. The original goal of the project was simply to characterize the thermomechanical properties of these materials to help design thermoelectric devices and understand thermal stresses imposed by the temperature gradients. While that goal was achieved, more fundamental physics was also learned.

#### 5. Conclusions

We have presented here a review of the experimental method of resonant ultrasound spectroscopy to measure the elastic tensor of a material. We have focused on high-temperature methods which are becoming increasingly important as new energy related materials with operating environments well above room temperature are being actively researched. Since its development as an experimental technique in the early 1990's, RUS has become the preferred method for elastic constant measurements, and the community of practitioners is expanding.

#### Acknowledgment

J. R. Gladden acknowledges the Department of Energy, EPSCoR Award no. DE-FG02-04ER46121, NASA Award no. NM0710850, and the University of Mississippi for support of this project as well as P. Smith for fruitful discussions.

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