26 August 2013 Optical and thermal properties of spinel with revised (increased) absorption at 4 to 5 μm wavelengths and comparison with sapphire
Author Affiliations +
Infrared absorption of high-quality, commercial, polycrystalline MgAl2O4 spinel is ∼40% greater in the range of 3.8 to 5.0 μm than the value predicted by the computer code OPTIMATR®, which has been used for window and dome design for more than 20 years. As a result, spinel and a -plane sapphire windows designed to support the same external pressure with the same probability of survival have approximately the same infrared absorptance in the range 3.8 to 5.0 μm. c -Plane sapphire has greater absorptance than spinel in the range 3.8 to 5.0 μm. Spinel has two weak absorption bands near 1.8 and 3.0 μm. At 1.064 μm, the laser calorimetric absorption coefficient of spinel is 10 to 50 times greater than that of sapphire. New measurements of specific heat capacity, thermal expansion, thermal conductivity, elastic constants, and refractive index (including dn/dT) of spinel are reported.



Sapphire, spinel, and aluminum oxynitride (ALON) are the most durable, commercially available midwave infrared (3 to 5 μm) window materials that are candidates for applications requiring environmental durability, such as sand and rain erosion resistance or the ability to operate at elevated temperature.1 All three materials transmit from about 5 μm in the infrared to at least as far as 0.3 μm in the ultraviolet. Wickersham and LaFever2 observed as early as 1960 that spinel has superior transmittance to that of sapphire near 5 μm. Figure 1 compares infrared transmittance of these materials, with the region 4 to 5 μm highlighted. The long wavelength cutoff between 5 and 6 μm increases in the order ALON<c-plane sapphire<a-plane sapphire<spinel.

Fig. 1

Midwave infrared transmittance spectra of ALON (2.86 mm thick polycrystalline material from Surmet, Burlington, MA), spinel (3.01 mm thick polycrystalline material from TA&T, Annapolis, MD), and sapphire (3.02 mm thick single crystal material from GT Advanced Technologies, formerly Crystal Systems, Salem, MA).


For applications requiring maximum transmittance or minimum optical emittance in the 4 to 5 μm region, it appears from Fig. 1 that spinel would be the best choice if it is the same thickness as sapphire and has sufficient mechanical strength. Sapphire is mechanically stronger than spinel,1 so a thinner sapphire window might be optically superior to a thicker spinel window and still meet mechanical requirements. Of the two commonly available crystal orientations of sapphire, a-plane material has less absorption than c-plane material.3 However, a-plane sapphire has a refractive index anisotropy of 0.001 in the plane of the window, whereas c-plane sapphire has an isotropic refractive index in the plane of the window. Optical anisotropy might be an issue for some applications.4 a-Plane sapphire is currently available in larger sizes than c-plane material, so the choice of crystal plane can be dictated by the required window size.

Careful transmittance measurements5,6 of these materials in the 1980s provided input to a computer code called OPTIMATR®, which was available in the 1990s,7,8 but is no longer commercially available. This computer code implements a multioscillator, multiphonon model for the complex refractive index of each material over a range of wavelengths and temperatures.9 The code was used to generate the optical constants n and k that are listed for ALON,10 spinel,11 and sapphire3 in Palik’s Handbook of Optical Constants of Solids. The code is validated in the region of intrinsic absorption by these materials, but is not meaningful in the transparent window region where absorption can be governed by impurities and defects.

We are interested in the relative merits of spinel and sapphire for large sensor windows with lateral dimensions >30cm that need high transmittance in the 4 to 5 μm region and must also withstand external pressure. We measured the absorption of some of the highest optical quality currently available spinel and sapphire near 5 μm by laser calorimetry to compare with absorption coefficients measured in the 1980s. Spinel was taken from large area blanks that could be used to make large windows. This paper presents the results of laser calorimetry, as well as new measurements of spectral transmittance, specific heat capacity, refractive index, thermal expansion, thermal conductivity, Young’s modulus, and Poisson’s ratio of spinel. The result is a revision to the OPTIMATR absorption coefficient of spinel in the 4 to 5 μm region. We discuss window design trade between optical absorption and mechanical reliability.



Polycrystalline spinel with a grain size of several hundred microns was provided by TA&T (Annapolis, MD) in the form of two polished blocks stated to represent high-optical-quality material. This material is representative of the quality and grain size commercially available today for large area windows with high optical quality. The blocks were cut from 35×40cm plates made by hot pressing followed by hot isostatic pressing. One polished block with a finished thickness of 5.98 mm was cut from a blank with a thickness of 7.4 mm. Another polished block with a finished thickness of 12.76 mm was cut from a blank with a thickness of 14.7 mm. Thermal, mechanical, and optical properties reported in this paper come from the TA&T material. For careful measurements of infrared transmittance, additional samples of polished spinel were provided by TA&T and by MER Corp. (Tucson, AZ).

a-Plane (±2deg) and c-plane (±2deg) sapphire were provided by GT Advanced Technology (Salem, MA) (formerly Crystal Systems) from their highest-quality, strain-free, single-crystal material grown by the heat-exchanger method. Boules were grown from aluminum oxide melt stock with a stated purity of 99.996%. Disks for calorimetry were machined and polished to a 10-5 scratch-dig surface finish by Crystal Systems.

Specific heat capacity (cp) at constant pressure (P) is the heat (H) required to raise the temperature of 1 g of substance by 1 K. Sapphire is a reference material for this measurement (ASTM E1269).12 Duplicate samples of spinel were measured by differential scanning calorimetry at the Thermophysical Properties Research Laboratory (TPRL), West Lafayette, Indiana. Two small compartments were heated electrically at 20K/min while temperature and electrical heat input were monitored. Samples were disks with a diameter of 5.8 mm and thickness of 1.5 mm with one smooth ground face for thermal contact. Spinel or a sapphire standard was placed in one compartment, while the reference compartment was empty. The differential power required to heat the sample or standard at the same rate as the blank reference pan was determined. From the mass of the standard or sample, the differential power required to heat each item, and the known specific heat capacity of the sapphire standard, the specific heat capacity of the sample was computed. Samples were measured in a PerkinElmer DSC 4 differential scanning calorimeter from 23 to 500°C under Ar and then in a Netzsch DSC 404 from 23 to 1000°C under Ar. Results from two samples, which had an average difference of 0.3 to 1% at each temperature, were averaged to obtain the specific heat capacity.

Thermal expansion of spinel was measured at the TRPL by ASTM standard testing procedure E228 with a dual push-rod dilatometer (Theta Dilatronics II). Test specimens were 51×6×6mm parallelepipeds with flat, parallel, ground ends. The differential expansion between a test specimen and a reference material was measured at 10-deg intervals from 20 to 1000°C during warming and then from 1000 to 200°C during cooling. Expansion of the test specimen was computed from this differential expansion and the known expansion of the standard. Six standards from the National Institute of Standards and Technology (NIST) included materials with low, moderate, and large expansions. For calibration and checkout, one standard was measured against another standard.

Thermal diffusivity of spinel was measured at the TRPL by the laser flash method (ASTM E1461). In this method, the front face of a disk is subjected to a short laser burst and the rear face temperature rise is recorded and analyzed. Ceramic disk samples with parallel, fine ground faces had a diameter of 12.7 mm and thickness of 2.54 mm. The apparatus consists of a Korad K2 1.064 μm Nd:YAG laser, a high-vacuum system including a bell jar with windows for viewing the sample, a tantalum or stainless steel tube heater surrounding a sample holding assembly, a thermocouple or infrared detector, and a digital data acquisition system capable of taking data at 40μs. Both surfaces of spinel were coated with a thin layer of black stove paint to absorb the laser energy.

Young’s modulus and Poisson’s ratio were measured at the University of Dayton Research Institute (Dayton, OH) at 21°C by impulse excitation of vibration (ASTM C 1259) with duplicate 38-mmdiameter×2-mmthick disks. Disk faces were optically polished and edges were ground. Measurements were made with a GrindoSonic Model MK3s (J. W. Lemmens, Leuven, Belgium) fitted with a microphone. Specimens supported on packing foam were excited by a steel ball bearing on a polymer rod. The flexural frequency was measured at the circumference of the disk after impact at the center. The torsional frequency was found by impacting the nodal circle whose diameter was 0.681 times the specimen diameter and measuring the vibration 90 deg away on the nodal circle. Testing was complete when five consecutive readings agreed within 1%. Young’s modulus (E) and Poisson’s ratio (ν) were calculated using the EMOD software supplied with the GrindoSonic.

Transmittance from 1.5 to 8 μm was measured with a nitrogen-purged PerkinElmer Spectrum GX Fourier transform infrared (FTIR) spectrophotometer at the Naval Air Warfare Center. The instrument uses a 1350 K wire coil source, a deuterated triglycine sulfate detector, and a KBr beamsplitter. Each spectrum is an average of 32 scans with 4cm1 resolution at a wavelength of 2.5 μm. Photometric accuracy is ±0.25%. The 100% transmittance was measured before each sample scan. A new background was collected if the 100% transmittance changed by more than ±0.25%. Transmittance from 0.25 to 2.5 μm was measured with a 150-mm diameter integrating sphere on a PerkinElmer Lambda 950 UV-Vis-NIR spectrophotometer with a photometric accuracy of ±0.25%T. The FTIR values matched the integrating sphere values to better than ±0.1% in the wavelength region of 1.5 to 2.5 μm where the two instruments overlap.

Total integrated infrared optical scatter in the forward and reverse hemispheres was measured at the Naval Air Warfare Center with a Coblentz sphere that captured light scattered between 2.5 and 70 deg from the direction of the incident laser beam.13 The light source was an optical parametric oscillator laser from JP Innovations (Monroe, WA) tunable from 3.46 to 4.41 μm. The idler output is 6mW. A 4-mm thick Ge window at the laser output blocks both the pump and signal radiation. Total integrated forward and back scatter of spinel from TA&T and MER were each in the range of 0.1 to 0.4% at 3.5 μm for samples with a thickness of 7 to 13 mm.

Refractive index of one TA&T spinel prism was measured at the Air Force Research Laboratory by the method of minimum deviation.14,15 The prism had a 10×10mm base and rectangular 10×13mm faces. The apex angle was 45.1075±0.0014deg, where the uncertainty is the standard deviation of 10 measurements made with an autocollimator. Five measurements of the angle of minimum deviation were made on a Moller-Wedel divided circle spectrometer at each wavelength and the average was used to calculate the refractive index. For thermo-optic coefficient measurements, the advantage of the method is that it allows for direct measurement of dn/dT (change in refractive index n with respect to temperature T) without having to subtract the contribution of the thermal expansion coefficient from the overall change in optical path, which is measured interferometrically.16,17 Refractive indices of standards were within 0.0001 of NIST measurements.18,19 The estimated error in the refractive index is 0.0001 and the error in the thermo-optic coefficients, dn/dT, is ±10%.

Laser calorimetry was conducted at the University of Central Florida College of Optics and Photonics.20 The experiment consists of thermally equilibrating a suspended test sample in the calorimeter, then exposing it to a laser while measuring the temperature rise of the specimen, and then continuing to monitor sample temperature after halting the laser exposure. Prior to calorimetry, specimens were cleaned with acetone and a cotton bud, washed with methanol, and wiped with lens paper. An insulated box enclosed the experiment to thermally isolate the sample at ambient temperature (295±1K) in the air. Laser light entered and exited the box through holes surrounded by insulating material to reduce convective heat transfer to the atmosphere.

Calorimetry samples were optically polished disks with a diameter of 10 mm and nominal thicknesses of 1.0, 2.0, and 3.0 mm. One edge was ground flat over a length of 2 to 3 mm for gluing a monofilament nylon fishing line to suspend the specimen in the path of the laser beam. The fishing line was attached to a thermally isolated frame mounted with 3 degrees of translational and rotational movement. A precision temperature measurement system by GEC Instruments (model S4TC) allowed the simultaneous reading of four temperatures with precision better than 10 mK over a broad range. Three 0.2-mm diameter thermocouples were glued to the edge of each sample. Care was taken to prevent scattered laser light from striking the temperature sensors. The sensitivity of the calorimeter was 10mK.

Lasers emitting at 1.064 μm (Nd:YAG, 3W output), 2.94 μm (Er:YAG, 100mW), 3.41μm (cascade diode laser from Maxion Technologies, College Park, MD, 15mW), and 4.85μm (cascade diode laser from Maxion, 90mW) were used to irradiate the samples in the calorimeter via beam-directing mirrors. Laser power was measured as it entered the calorimeter using two calibrated power meters to check for consistency. If a laser beam was too large in diameter, or was divergent, a lens was used to focus the beam to <3mm. Power was measured after the lens. The 4.85-μm laser radiated over the range of 4.79 to 4.94 μm, with half of the intensity on either side of 4.85 μm.

Finite element analysis was carried out at the Naval Air Warfare Center with NX 7.5 finite element analysis software (Seimens PLM Software, Munich, Germany). A rectangular window was divided into 8-node cubic elements, with 51,300 elements in one plane and five planes through the thickness of the window. A static load of 13.79 kPa (2lb/in.2) was applied to the upper surface of the window. The analysis identifies in-plane stresses on the upper and lower surfaces of the window and computes the maximum principal stress in each surface element. For a simply supported window, nodes along both lower long edges and one of the lower short edges were fixed in the vertical (z) direction, but were free to rotate and to move in the x and y directions. The row of nodes on the other short, lower edge of the window was constrained in all six degrees of freedom. The model therefore has one edge restrained and three simply supported. Tensile stress adjacent to the constrained edge on the tensile face was neglected in computing the probability of survival of the window, so as to approximate a fully simply supported window. The one condition that was modeled was a window with dimensions of 48.26×68.58×1.27cm, with the length of each finite element being 0.254 cm. For other pressures and window thicknesses, stresses were scaled in proportion to p/b2, where p is the uniform pressure on the upper surface of the window and b is the thickness of the window. For example, if the applied pressure was doubled, stresses were doubled. If the window thickness was doubled, stresses were decreased by a factor of 4.


Thermal and Elastic Properties of Spinel


Specific Heat Capacity

The specific heat capacity of spinel was fit by the equation


with a0=0.12274, a1=4.9036×103, a2=7.1846×106, a3=4.8981×109, and a4=1.2606×1012. The residual standard deviation in cp is 7.5×104J/(g·K). Extrapolating the measured curve by 1 K gave a value of cp=0.815J/(g·K) at 295 K, which is 2% below the value of 0.833J/(g·K) reported by Klemme and Ahrens.21 For sapphire at 295 K, cp=0.768J/(g·K).12


Thermal Expansion

Thermal expansion of spinel was fit to the polynomial


where L0 is the initial length at T0=293K and ΔL is the increase in length at temperature T (K). The constants are b0=1.1699×103, b1=2.2478×106, b2=6.6441×109, and b3=2.0465×1012. The residual standard deviation in ΔL/L0 is 2.7×105. Our values of ΔL/L0 are generally within 2% of the values reported by Koenig,22 whose data are fit by a cubic polynomial with b0=2.0110×103, b1=5.8103×106, b2=2.0489×109, and b3=0.1339×1012 for T=293 to 1900 K. The differential coefficient of thermal expansion (CTE) derived from Eq. (2) is





The density of spinel (3.576g/mL) at 293 K was calculated from the cubic unit cell lattice dimension of 0.8085 nm and eight formula masses (142.266g/mol) per unit cell.21,23 At elevated temperature T, the density ρT decreases from thermal expansion.


where ρ0 is the density at T0=293K, and ΔL/L0 is computed with Eq. (2).


Thermal Conductivity

Thermal diffusivity (D) is a measure of the rate at which temperature diffuses through a substance when there is a spatial gradient of temperature. Thermal conductivity, k, is computed from the measured diffusivity by the equation


where ρ is the density in Eq. (4), cp is the specific heat capacity in Eq. (1), and D is the thermal diffusivity. Our data in Fig. 2 are fit by the equation


where A=443174, B=1.8692, c=7.3970, and T=296 to 1273 K, and the residual standard deviation of the curve fit is 0.15W/(m·K). Figure 2 also shows previously reported values of the thermal conductivity of spinel.22,24,25

Fig. 2

Thermal conductivity of spinel (open circles) from Eq. (5). Solid line is curve fit by Eq. (6). Filled triangle, diamonds, and square are literature data.22,24,25 Filled circles are laser flash measurements by Raytheon in 2008 of legacy Raytheon spinel from the 1980s.



Elastic Moduli and Poisson’s Ratio

Young’s modulus (E) and Poisson’s ratio (ν) measured from vibrational frequencies of test specimens were used to compute the shear modulus (G) and bulk modulus (K). Results are E=272GPa, ν=0.27, G=106GPa, and K=197GPa for T=294K. Our value of Young’s modulus can be compared with values of 277,26 275,27 266 to 270,28 268,29 and 25830,31 GPa in previous reports.


Laser Calorimetry


Treatment of Laser Calorimetry Data

Laser calorimetry is recommended for measuring the low absorptance of optical components and window materials.3233.34.35 In this technique, a small disk is irradiated with a laser while the temperature of the disk is measured by thermocouples attached to the edge. After irradiation, the temperature falls back to ambient in an exponential manner. The graph of temperature versus time in Fig. 3 can be used to extract the absorptance (a) of the material, which is the fraction of incident radiant power (P0) absorbed.


Power absorbed=aP0.
Knowing the mass of the sample and its specific heat capacity, we can calculate how much energy was absorbed from the laser to create the observed temperature rise.

Fig. 3

Temperature rise of 2-mm-thick disks of c-plane sapphire (0.628 g sample, 73 mW laser power), a-plane sapphire (0.634 g, 70 mW), and spinel (0.527 g, 61 mW) in laser calorimetry at 4.85 μm. The sample is exposed to the laser from time tstart to time tstop. A linear temperature correction for baseline drift was applied to the data prior to display.


Advantages of laser calorimetry include the simplicity of the apparatus and ease of absolute calibration. Surface and bulk absorptance can be distinguished by studying samples with different thicknesses. If the surfaces are identical, then a plot of measured absorptance versus sample thickness extrapolated to zero thickness reveals the surface absorptance. The slope of the graph gives the bulk absorptance.

If the laser calorimetry test specimen were not losing heat during laser irradiation, and if the thermal conductivity of the sample is high enough that its temperature (T) is uniform, the rate at which its temperature would rise is equal to the power absorbed divided by the thermal mass (mass×specific heat capacity) of the disk.


Heating rate=dTdt=aP0mcp,
where t is time and m is the mass of the sample. The numerator on the right side of Eq. (8) is the power absorbed by the sample. The denominator is the energy required to raise the sample temperature by 1 K. In the absence of heating, the rate at which the sample cools is proportional to the difference in temperature between the sample and its surroundings (ΔT).


Cooling rate=dTdt=γΔT,
where γ is an empirical heat loss coefficient accounting for radiative and conductive heat losses.

At any time during the calorimetry experiment, the rate of change of temperature is the sum of Eqs. (8) and (9).


Rate of change of temperature in laser calorimetry=dTdt=aP0mcpγΔT.

Integration of Eq. (10) gives the temperature rise of the sample versus time.


Duration irradiation:ΔT=aP0γmcp[1eγ(ttstart)].


After irradiation:ΔT=aP0γmcp[eγ(ttstop)eγ(ttstart)],
where tstart is the time at which the sample is exposed to the laser and tstop is the time at which exposure ends (Fig. 3). Absorptance (a) and heat loss coefficient (γ) can be extracted from the temperature versus time data in Fig. 3 by least-squares curve fitting.

Internal transmittance is the fraction of radiant power that has entered a specimen, which reaches the opposite side after traversing a path length b through the specimen. The relation between internal transmittance and absorption coefficient (α) is


Internal transmittance=eαb.
Internal transmittance is independent of surface losses by reflection, absorption, and scatter.

For perpendicular incidence of a laser beam on a sample with parallel surfaces, negligible optical scatter, and negligible surface absorption, the absorption coefficient is related to absorptance by Eq. (14),35 which is derived in the appendix.


where τ is the single-surface Fresnel transmittance and R is the single-surface Fresnel reflectance. (We use τ for transmittance to avoid confusing transmittance with temperature, T.) If there is negligible absorption and scatter at the surface, then τ=1R. In the absence of strong absorption, the single-surface Fresnel reflectance and transmittance depend only on the real part (n) of the refractive index of the disk.




where the refractive index of air is 1. For specimens and wavelengths used in the present study, scatter and absorption are low enough for Eqs. (15) and (16) to be good approximations.

When the product of the absorption coefficient and the sample thickness is small (αb1), a first-order expansion of Eq. (14) gives



If there is surface absorption, a term accounting for both surfaces can be added to Eq. (17).



In the present work, surface absorption was negligible relative to the precision of the measurement of bulk absorption. Equation (17) is typically accurate enough for laser calorimetry measurements of weakly absorbing specimens. However, Eq. (14) was required for sapphire and spinel at 4.85 μm, where there is significant absorption.


Laser Calorimetry Results

Figures 4 and 5 show the absorptance of sapphire and spinel at 4.85 μm and the absorptance of spinel at 3.41, 2.94, and 1.064 μm. Error bars on the data points are estimated standard deviations from several measurements. Straight lines through the origin were drawn through the spinel data for 3.41, 2.94, and 1.064 μm in Fig. 5. The slope is the absorption coefficient in Eq. (17).

Fig. 4

Absorptance of c-plane sapphire (circles) and a-plane sapphire (triangles) at 4.85 μm measured by laser calorimetry as a function of sample thickness. Curves are least-squares fit of Eq. (14) to the data with absorption coefficient as the one unknown parameter.


Fig. 5

Absorptance of spinel measured by laser calorimetry as a function of sample thickness. Data at 4.85 μm are fit to Eq. (14) using the method of least squares. Straight lines through the origin, Eq. (17), were fit to the points for 1.064, 2.94, and 3.41 μm.


The absorptance of spinel and sapphire at 4.85 μm is too high to use Eq. (17), which produces values of absorption coefficient that are 3 to 9% low. Therefore, absorptance was fit to Eq. (14), with the single-surface Fresnel reflectance and transmittance calculated from the literature refractive index3637.38 with Eqs. (15) and (16). The only adjustable parameter in the curve fit is absorptance. Curve fitting was done with Microsoft Excel Solver® as described by Harris.39 The standard uncertainty in absorptance from the curve fit was computed with Billo’s Excel macro Solvstat.40 The 95% confidence interval for absorptance was obtained by multiplying the standard uncertainty by Student’s t for n-p degrees of freedom, where n=3 is the number of data points on each curve and p=1 is the number of adjustable parameters.

Resulting absorption coefficients are listed in Table 1, where comparison is made with previously reported laser calorimetry measurements at several shorter wavelengths.4142.43.44 The absorption coefficients of sapphire and spinel at 4.85 μm are thought to represent intrinsic properties of the materials. Absorption coefficients at 1.064, 2.94, and 3.41 μm are thought to arise from extrinsic factors such as OH impurities. It is noteworthy that the spinel we measured has >50 times as much absorption as sapphire at 1.064 μm, and substantial absorption in the OH stretching region at 2.94 and 3.41 μm.

Table 1

Absorption coefficients measured by laser calorimetry.

MaterialAbsorption coefficient, α (cm−1)
Present work
1.064 μm2.94 μm3.41 μm4.85 μm
c-Plane sapphire0.0004±0.0001**0.58±0.17
a-Plane sapphire0.0003±0.0001**0.42±0.13
Literature data
1.3 μm2.7 μm3.8 μm
c-Plane sapphire0.0008,a,b 0.00005c0.00127,a 0.003d0.024,b,d 0.0285a,b

Note: Uncertainty is 95% confidence interval. The absorption coefficient for sapphire at 2.94 and 3.41 μm was too small to measure with the laser power available.


Reference 41.


Reference 43.


Reference 44.


Reference 42.

Figure 6 superimposes our results from laser calorimetry with previous optical transmittance measurements made with laser diodes at discrete wavelengths or by FTIR spectrometry.5,6,45 Our calorimetry results are represented by three large open symbols at 4.85 μm. Dashed lines are from OPTIMATR. Solid circles are reported points for c-plane sapphire. Solid squares are reported points for a-plane sapphire. Solid triangles are reported points for spinel. Two superimposed open symbols near the origin at 3.8 μm are laser calorimetry points for c-plane sapphire from the literature listed in Table 1.42,43

Fig. 6

Comparison of laser calorimetry (open symbols at 4.85 μm) to OPTIMATR absorption coefficient (dashed curves) and previously reported discrete values for absorption coefficient of c-plane sapphire (solid circles), a-plane sapphire (solid squares), and spinel (solid triangles). The solid curve is the absorption coefficient of spinel derived from transmittance of two thicknesses of spinel in the present work.


We obtained the solid curve in Fig. 6 by measuring the transmittance of spinel with thicknesses of 0.598 and 1.276 cm. If surface absorption and surface scatter from the two specimens are the same, the bulk extinction coefficient (β=αabsorption+αbulk scatter), arising from bulk absorption plus bulk scatter, is given by


β=αabsorption+αbulk scatter=ln(T1/T2)b2b1,
where Ti is the transmittance of each sample and bi is the thickness. Equation (19) ignores multiple reflections within the sample. Total integrated optical scatter provides an estimate of bulk scatter in spinel. The sum of the forward and reverse scatter averaged from measurements at 3.5, 4.0, and 4.4 μm is 0.346% for a 0.598-cm thick specimen and 0.418% for a 1.276-cm thick specimen. (The total integrated scatter from the two samples of spinel did not vary with wavelength in the interval of 3.5 to 4.4 μm.) If surface scatter of both specimens is equal, the difference in bulk scatter is 0.4180.346=0.072% for a thickness difference of 1.2760.598=0.678cm. The bulk scatter coefficient is therefore αbulk scatter=0.072%/0.678cm=0.0011cm1. This negligible scatter coefficient was subtracted from the extinction coefficient β in Eq. (19) to obtain the absorption coefficient αabsorption shown by the solid line in Fig. 6.


Revised Spectral Absorption Coefficient of Spinel

In Fig. 6, experimental data points for the absorption coefficient of spinel (solid triangles) and our measurement from two thicknesses of spinel [solid line computed with Eq. (19)] are superimposed, but do not agree with the dotted line for spinel computed with OPTIMATR. By contrast, experimental data points for c-plane sapphire (solid circles) and a-plane sapphire (solid squares) are in good agreement with the dashed curves computed by OPTIMATR. Our laser calorimetry measurement for a-plane sapphire at 4.85 μm (open square) lies on the OPTIMATR curve. Our laser calorimetry measurement for c-plane sapphire (open circle) lies 12% below the OPTIMATR curve, but within the estimated uncertainty of the calorimetry measurement. For spinel, our laser calorimetry measurement (open triangle) lies between the dashed and solid curves for spinel, but within experimental uncertainty of both. In summary, experimental data points are in good agreement with the OPTIMATR curves for sapphire, but experimental points for spinel do not lie on the OPTIMATR curve in the region from 4.2 to 5.2 μm. OPTIMATR underestimates the absorptance of spinel in the 4.2 to 5.2 μm region.

We therefore made spectroscopic measurements of the absorption coefficient of additional samples of spinel to see if the solid curve in Fig. 6 is reproducible. Figure 7 shows that spectroscopic data from new samples of spinel from TA&amp;T and from MER Corp. lie near the solid curve from Fig. 6 and not near the OPTIMATR curve. Table 2 lists the average absorption coefficient of spinel from measurements of three pairs of thick and thin specimens. We found other spinel samples that gave higher extinction coefficients than those shown in Table 2. We assume that these materials had higher optical scatter and deliberately used samples that gave the lowest extinction coefficients so as not to overestimate the absorption of spinel.

Fig. 7

Absorption coefficients of spinel manufactured by four companies three decades apart all lie above the OPTIMATR curve (solid line) in the region of 4.2 to 5.2 μm. Dashed lines are obtained from two pairs of TA&T spinel plates and one pair of MER spinel plate made in the 2010 to 2012 period. Small corrections for bulk scatter at 3.5 μm have been subtracted from the bulk extinction coefficient. Open circles were measured by diode laser absorption of Raytheon spinel in the 1980s.5 Open triangles were measured by diode laser absorption of Coors spinel in the 1980s.5 Open square is laser calorimetry value from the present work.


Table 2

Mean absorption coefficient of spinel from transmittance of three pairs of thin and thick specimens.

Wavenumber (cm−1)Absorption coefficient (α, cm−1)Wavenumber (cm−1)Absorption coefficient (α, cm−1)

Note: A polynomial fitting absorption coefficient as a function of wave number (ν˜, cm−1) from 2600 to 1875  cm−1 is α (cm−1)=5.51852179        ×        10−18ν˜6            −            8.88520838            ×            10−14ν˜5            +            5.85969325        ×10−10ν˜4−2.03475841×10−6ν˜3+3.93709258×10−3ν˜2−4.03652837ν˜+1717.85263. Full nine-digit coefficients are required to reproduce α with three decimal precision.

The pair of spinel samples that gave the lowest absorption coefficient in the 4 to 5 μm region was used to calculate the extinction coefficient at shorter wavelengths. Figure 8 shows two weak absorption features near 1.8 and 2.8 μm, which are evident in all samples of spinel that are thick enough to see the absorption. Note that the absorption coefficients from laser calorimetry for spinel in Table 1 are roughly twice as great as the values in Fig. 8. The values in Fig. 8 could therefore be an underestimate.

Fig. 8

Extinction coefficient of MER spinel showing absorptions in the 1.5 to 3.2 μm region seen in MER and TA&T spinel. No correction for bulk optical scatter has been applied to the data.


For comparison of the absorption of sapphire and spinel in Sec. 7 of this paper, we calculated the absorptance (a) of a 1-cm-thick slab of each material from the absorption coefficient by using Eq. (14), where τ=1R is the single-surface transmittance. We then computed the average absorptance over the wave number range ν˜=2000to2632cm1 (3.8 to 5.0 μm) with Eq. (20).


Average absorptance=12632200020002632av˜dv˜.

Results are shown in Table 3, which also includes the average absorptance for the range 3.0 to 5.0 μm using the absorption coefficient for spinel from Fig. 8. The average absorptance of spinel (0.134) in the 3.8 to 5.0 μm region is 92% as great as that of a-plane sapphire (0.145) and 71% as great as that of c-plane sapphire (0.189). OPTIMATR predicts significantly lower average absorptance for spinel (0.094). The average absorptance of spinel (0.073) in the wider range of 3.0 to 5.0 μm is slightly greater than that of a-plane sapphire (0.071) because spinel has absorption in the 3.0 to 3.8 μm region (Fig. 8) and sapphire does not. OPTIMATR does not model any spinel absorption below 3.8 μm.

Table 3

Average absorptance of spinel and sapphire.

Data sourceWavelength rangeWave number rangeAverage absorptance for 1 cm thickness, Eq. (20)
c-Plane sapphirea-Plane sapphireSpinel
OPTIMATR (295 K)3.8 to 5.0 μm2632 to 20000.1890.1450.094
Present work3.8 to 5.0 μm2632 to 2000aa0.134
OPTIMATR (295 K)3.0 to 5.0 μm3333 to 20000.0920.0710.045
Present work3.0 to 5.0 μm3333 to 2000aa0.073


Spectral transmittance of sapphire was not measured in the current work. Laser calorimetry and measurements of sapphire conform to OPTIMATR.


Refractive Index of Spinel

Published2,46,47 and unpublished measurements of the refractive index (n) of spinel at room temperature from 0.35 to 5.5 μm were summarized in 1995 by the Sellmeier equation. 38


where wavelength (λ) is expressed in μm. Spinel samples included natural minerals and synthetic material from the 1980s and earlier.

We measured the refractive index of a single prism of commercial polycrystalline spinel manufactured in 2010. Measurements near 295 K were made at 60 wavelengths between 0.4 and 5.0 μm. An additional 93 measurements were made near 350, 400, and 450 K at selected wavelengths. The entire data set was fit to the following Sellmeier equation by the Levenberg-Marquart algorithm with the Excel macro Optimiz.48


where λ is the wavelength in the range of 0.4 to 5 μm, T is the temperature in the range of 295 to 450 K, T0=295.15K, and the least-squares parameters are A=1.893592, B=5.904×108, C=0.097911, D=4.437×109, E=4.617875, and F=19.0165. The root-mean-square error in fitting the refractive index is 0.00014. The root-mean-square difference between Eqs. (21) and (22) at 295 K is 0.0009, with the value of n from Eq. (22) being higher than the value from Eq. (21). A 2 mol% increase in the Al2O3MgO ratio would increase the refractive index by 0.0009.

The refractive index increases linearly in the range of 25 to 175°C, with a slope dn/dT1.4×105K1. For comparison, Lang and Duncan49 found n=1.6837+1.30(±0.04)×105T3.6×109T2 (T=°C) at 0.633 μm in the range of 25 to 525°C. The average slope of this function from 25 to 175°C is 1.2×105K1. Vadem et al.47 reported dn/dT=0.90×105K1 at 0.589 μm for the range of 25 to 700°C.


Trading Optical Absorption and Mechanical Strength

The question that motivated our study of sapphire and spinel is which of these infrared window materials can provide the least midwave infrared absorption while meeting the mechanical requirements for a window? From Fig. 1, the long held conventional wisdom has been that increased infrared transmittance in the 4 to 5 μm range is provided in the order c-plane sapphire<a-plane sapphire<spinel. However, careful measurements in Fig. 6 show that the absorption coefficients of spinel and a-plane sapphire are almost equal in the range of 3.8 to 4.8 μm and diverge only at longer wavelengths. Sapphire is mechanically stronger than spinel, so a thin sapphire window could possibly be used instead of a thicker spinel window, resulting in lower absorption by the thin sapphire than by the thicker spinel. Our goal is to make quantitative comparisons to select the material that has the least infrared absorption, while meeting mechanical requirements.

One way to design a window plus its frame employs finite element analysis to calculate the stress distribution in the window under a given load and to use Weibull statistics to estimate the probability of survival of the window. If the desired probability of survival cannot be achieved with a practical thickness of material, a proof test on a finished window could be used to demonstrate that a particular window survives required loads. Another approach to window design is to measure slow crack growth rate of the window material (ASTM C1368) and then design the window to last for a chosen lifetime under operational stresses.29,50

Consider a simply supported rectangular window subjected to a uniform pressure on one face. Maximum tensile stress (σmax) on the tensile face of the window is proportional to the applied pressure (p) and decreases as the inverse square of window thickness (b).51


Stress also depends on Poisson’s ratio, which is the same (0.27) for sapphire and spinel.

To compare strengths of materials, we employ the characteristic strength (sc) defined by Klein as the effective mean strength of a 1cm2 area under tension in a mechanical test.5253.54 The strength of an optical ceramic is a highly variable, extrinsic property that depends on flaws such as scratches, subsurface damage, weak grain boundaries, large grains, inclusions, pore nests, and voids. The distribution of flaw sizes determines the distribution of strength, which is characterized by the Weibull modulus, m. The smaller the Weibull modulus, the broader is the distribution of strength.

For window design consideration, we choose the parameters sc and m in columns 2 and 3 of Table 4, which approximately represent particular lots of real specimens. Three sets of Weibull parameters for spinel in Table 4 encompass the behavior of large-grain, commercial material for which we have data. Weibull parameters for sapphire are roughly representative of several widely varying reports.52,5556.57 Sapphire and spinel could have widely different characteristics from those listed in the table. For example, experimental coupons of spinel with a grain size of 2 μm had a characteristic strength of 425MPa and a Weibull modulus of 6.9.58 In our experience, Table 4 approximately represents the range of strength and Weibull modulus of high optical quality spinel that can be currently purchased in the form of large windows with lateral dimensions >30cm. The characteristic strength of sapphire in Table 4 might appear high in comparison to strengths listed in some manufacturer’s bulletins. The reason is that the characteristic strength sc applies to 1cm2 area under load. When scaled for area with a Weibull modulus of 4, the strength of sapphire would look more familiar. For example, for an area of 20cm2 instead of 1cm2, the strength of c-plane sapphire is predicted to be (900MPa)(1cm2/20cm2)1/4=426MPa

Table 4

Applied pressure and window thickness that give Ps=0.999 for spinel and sapphire windows with different strength distributions.

Materialsc (MPa)mApplied pressure p (kPa)Thickness b (cm)Max stress in window (MPa)Mean absorptance 3.8 to 5.0 μmRelative absorptance 3.8 to 5.0 μm
Spinel 1100839.51.2721.00.1641.00
Spinel 2150639.51.3817.70.1751.07
Spinel 3200639.51.2023.60.1560.95

Note: Simply supported window (48.26×68.58×b  cm thick) with pressure p applied to one surface.

For each element of area on the tensile surface of a window in a finite element model, the probability of survival (Ps) is given by the Weibull distribution, which we choose to write as suggested by Klein.5253.54


where A is the surface area of the finite element, A0=1cm2, Γ is the gamma function of the argument (1+1/m), and σ is the maximum principal tensile stress in the finite element. The overall probability of survival of the window is the product of Ps for all the elements of the tensile surface. The probability of failure for the window is Pf=1Ps.

Finite element analysis was conducted for a simply supported rectangular window with dimensions 48.26×68.58×bcm with a uniform pressure p applied to one face. The thickness (b) of the window was varied to produce a probability of survival of 0.999 for each set of Weibull parameters. In Table 4, for spinel 1 with sc=100MPa and m=8, a thickness of b=1.27cm and applied pressure p=39.5kPa give a probability of survival of 0.999. The maximum stress at the center of the tensile face is 21.0 MPa. For c-plane sapphire with sc=900MPa and m=4, the same applied pressure of 39.5 kPa yields a probability of survival of 0.999 if the thickness is 1.02 cm. The stress at the center of the tensile face is 32.4 MPa. Three cases for spinel and two cases for sapphire are listed in Table 4.

From the thickness of the window required to produce a survival probability of 0.999, the mean absorptance for the wavelength range of 3.8 to 5.0 μm was computed by solving Eq. (14) for absorptance at each wavenumber and then integrating Eq. (20). Absorptance is shown in the next-to-last column of Table 4 and relative absorptance is shown in the last column. We find that a-plane sapphire has equivalent absorptance to spinel 2 whose characteristic strength is 150 MPa and whose Weibull modulus is 6. Spinel 1 with a higher Weibull modulus and spinel 3 with a higher strength have slightly less absorptance than a-plane sapphire. The absorptance of c-plane sapphire is 9 to 23% greater than that of the three types of spinel.

The conclusion of this analysis is that spinel and a-plane sapphire have similar mean absorptance in the 3.8 to 5.0 μm region. When designed to bear the same load, either material could be better than the other, depending on their Weibull parameters. This conclusion contradicts the common belief that a spinel window will have less midwave infrared absorptance than a sapphire window. Spinel does have less absorptance than c-plane sapphire, but does not have a clear advantage over a-plane sapphire.



Careful measurements of infrared absorption of high-quality, commercial, polycrystalline MgAl2O4 spinel show that the absorptance is 43% greater in the range of 3.8 to 5.0 μm than the value predicted by the computer code OPTIMATR®, which has been used for window and dome design for more than 20 years. The average absorptance of spinel in the wavelength range of 3.8 to 5.0 μm is 92% as great as that of a-plane sapphire and 71% as great as that of c-plane sapphire. Spinel also exhibits weak absorptance in the range of 1.4 to 3.4 μm. As a result, the average absorptance of spinel in the range of 3.0 to 5.0 μm is 103% as great as that of a-plane sapphire and 79% as great as that of c-plane sapphire. The spinel that we examined has >50 times as much optical absorption as sapphire at 1.064 μm. Specific heat capacity, thermal expansion, thermal conductivity, elastic constants, and refractive index of spinel are also reported. We examined the relative infrared absorptance of sapphire and spinel windows designed to provide the same probability of survival under an applied load. The conclusion is that spinel and a-plane sapphire have similar mean absorptance in the 3.8 to 5.0 μm region. The absorptance of c-plane sapphire is greater than that of spinel.


We thank Larry Fehrenbacher of TA&T and Juan Sepulveda of MER Corp. for providing spinel and sharing data on spinel. We are grateful to GT Advanced Technologies (formerly Crystal Systems) for providing sapphire. Raytheon thermal conductivity data were kindly provided by Howard Poisl.



Derivation of Eq. (14) Relating Absorption Coefficient to Absorptance

Absorptance can occur in the bulk material and at both surfaces. Following the derivation of Orchard et al.,35 we assume that surface absorption is negligible compared with bulk absorption. The derived formula therefore places an upper limit on bulk absorption.

In Fig. 9, radiant power P0 is incident on the first surface of the optical disk at the left. If the single-surface transmittance is τ, and if there is negligible surface absorption and scatter, then the power that enters the first surface is τP0. When the forward ray reaches the right-hand surface, some is transmitted to the right and some is reflected back to the left. When the reflected beam reaches the left-hand surface, some is transmitted to the left and some is reflected back to the right. There are an infinite number of progressively smaller internal reflections. The total radiant power traveling in the forward direction (to the right) inside the sample is designated PF in Fig. 9. This power is the sum of the power that entered the sample and the infinite number of reflections from the left-hand surface. Similarly, the total radiant power traveling in the reverse direction (to the left) inside the sample is designated PR.

Fig. 9

For derivation of Eq. (14).


At the output face, the total transmitted power is PT, so the total power incident on the output face from inside the sample must be PT/τ because the transmittance of the output face is τ. The total power propagating from left to right inside the sample is PF. It is attenuated over a path length b by a material with a bulk absorption coefficient α. We say35 that power PT/τ reaching the output face is a result of power PF being attenuated by a factor eαb.



If the single-surface reflection coefficient is R, and total power PT/τ reaches the output face, then the total reflected power propagating to the left inside the sample is



The total power absorbed inside the sample is a result of powers PF and PR each being attenuated over path length b.


Pabsorbed=(PF+PR)radiant power in disk×(1eαb)fraction of power absorbed=aP0,
where a is the absorptance. Equation (27) can be rearranged to



The total transmitted power (PT in Fig. 9) results from the incident power P0 being transmitted through two surfaces and suffering an infinite number of partial reflections between those two surfaces. The following equation accounts for all losses:


PT=P0τ2eαbloss from tranmission through two surfaces(1+R2e2αb+R4e4αb+R6e6αb+)one term for eachround-trip reflection.

The parentheses contain an infinite geometric series of the form n=0n=xn, where x=R2e2αb. For |x|<1, the sum converges to xn=1/(1x), so



Substituting the expression at the right of Eq. (30) for the infinite series into Eq. (29) gives



Finally, we substitute the expression for PT from Eq. (31) into Eq. (28).



Solving Eq. (32) for eαb gives

which is Eq. (14).

Equation (14) relates the absorption coefficient (α) to the measured absorptance (a). The single-surface Fresnel reflectance (R) is given by Eq. (15) and the Fresnel transmittance (τ) is given by Eq. (16). If we know the refractive index of the material at the laser wavelength, Eq. (14) allows us to calculate the absorption coefficient from the measured absorptance.


1. D. C. Harris, Materials for Infrared Windows and Domes, SPIE Press, Bellingham, WA (1999). Google Scholar

2. K. A. WickersheimR. A. LaFever, “Optical properties of synthetic spinel,” J. Opt. Soc. Am. 50(8), 831–832 (1960).JOSAAH0030-3941 http://dx.doi.org/10.1364/JOSA.50.0831_1 Google Scholar

3. M. E. ThomasW. J. Tropf, “Aluminum oxide (Al2O3) revisited,” in Handbook of Optical Constants of Solids III, E. D. Palik, Ed., pp. 653–682, Academic Press, San Diego (1998). Google Scholar

4. D. W. Ricks, “Polarization analysis of sapphire domes,” Proc. SPIE 891, 172–178 (1988).PSISDG0277-786X http://dx.doi.org/10.1117/12.944304 Google Scholar

5. M. E. ThomasR. I. JosephW. J. Tropf, “Infrared transmission properties of sapphire, spinel, yttria, and ALON as a function of temperature and frequency,” Appl. Opt. 27(2), 239–245 (1988).APOPAI0003-6935 http://dx.doi.org/10.1364/AO.27.000239 Google Scholar

6. M. E. Thomas, “Infrared properties of the extraordinary ray multiphonon process in sapphire,” Appl. Opt. 28(16), 3277–3278 (1989).APOPAI0003-6935 http://dx.doi.org/10.1364/AO.28.003277 Google Scholar

7. M. E. Thomas, “A computer code for modeling optical properties of window materials,” Proc. SPIE 1112, 260–267 (1989).PSISDG0277-786X http://dx.doi.org/10.1117/12.960785 Google Scholar

8. OPTIMATR® (A Computer Program to Calculate Optical Properties of Materials), ARSoftware, 8201 Corporate Drive, Suite 1110, Landover MD 20785. Google Scholar

9. S. G. KaplanM. E. Thomas, “Measurement of the o-ray and e-ray infrared refractive index and absorption coefficient of sapphire from 10 K to 295 K,” Proc. SPIE 4822, 41–50 (2002).PSISDG0277-786X http://dx.doi.org/10.1117/12.451770 Google Scholar

10. W. J. TropfM. E. Thomas, “Aluminum oxynitride (ALON) spinel,” in Handbook of Optical Constants of Solids II, E. D. Palik, Ed., pp. 777–787, Academic Press, Boston (1991). Google Scholar

11. W. J. TropfM. E. Thomas, “Magnesium aluminum spinel (MgAl2O4),” in Handbook of Optical Constants of Solids II, E. D. Palik, Ed., pp. 883–897, Academic Press, Boston (1991). Google Scholar

12. D. G. Archer, “Thermodynamic properties of synthetic sapphire (α-Al2O3) standard reference material 720 and the effect of temperature-scale differences on thermodynamic properties,” J. Phys. Chem. Ref. Data 22(6), 1441–1453 (1993).JPCRBU0047-2689 http://dx.doi.org/10.1063/1.555931 Google Scholar

13. P. C. ArchibaldH. E. Bennett, “Scattering from infrared missile domes,” Opt. Eng. 17(6), 647–651 (1978).OPEGAR0091-3286 http://dx.doi.org/10.1117/12.7972298 Google Scholar

14. M. BornE. WolfA. B. Bhatia, Principles of Optics, 7th ed., pp. 191–192, Cambridge University Press, New York (1999). Google Scholar

15. A. Joshiet al., “Impurity concentration and temperature dependence of the refractive indices of Er3+-doped ceramic Y2O3,” Opt. Express 20(4), 4428–4435 (2012).OPEXFF1094-4087 http://dx.doi.org/10.1364/OE.20.004428 Google Scholar

16. Y. SatoT. Taira, “Thermo-optical and mechanical parameters of NdGdVO4 and NdYVO4,” presented at Quantum Electronics and Laser Science Conference, 2007, Baltimore, MD, Paper JWA87 (May 2007). Google Scholar

17. R. Weil, “Interference of 10.6 m coherent radiation in a 5-cm long gallium arsenide parallelepiped,” J. Appl. Phys. 40(7), 2857–2859 (1969).JAPIAU0021-8979 http://dx.doi.org/10.1063/1.1658088 Google Scholar

18. I. Malitson, “Revisiting the optical properties of calcium fluoride,” Appl. Opt. 2(11), 1103–1107 (1963).APOPAI0003-6935 http://dx.doi.org/10.1364/AO.2.001103 Google Scholar

19. A. Feldmanet al., NBS Technical Note #993 (1978). Google Scholar

20. G. Turriet al., “Optical absorption, depolarization, and scatter of epitaxial single-crystal chemical-vapor-deposited diamond at 1.064 μm,” Opt. Eng. 46(6), 064002 (2007).OPEGAR0091-3286 http://dx.doi.org/10.1117/1.2748044 Google Scholar

21. S. KlemmeM. Ahrens, “Low-temperature heat capacities of MgAl2O4 and spinels of the MgCr2O4MgAl2O4 solid solution,” Phys. Chem. Minerals 34(2), 59–72 (2007).PCMIDU0342-1791 http://dx.doi.org/10.1007/s00269-006-0128-4 Google Scholar

22. J. R. Koenig, “Thermostructural evaluation of four infrared seeker dome materials,” Report TP 6539, Part 2, (Naval Weapons Center, China Lake, CA 1985). Google Scholar

23. S.-Y. Jinget al., “Investigation on lattice constants of Mg-Al spinels,” J. Mater. Sci. Lett. 19(3), 225–227 (2000).JMSLD50261-8028 http://dx.doi.org/10.1023/A:1006774318019 Google Scholar

24. R. L. Gentilman, “Current and emerging materials for 3–5 micron IR transmission,” Proc. SPIE 683, 2–11 (1986).PSISDG0277-786X http://dx.doi.org/10.1117/12.936409 Google Scholar

25. D. W. RoyC. G. Martin Jr., “Advances in spinel optical quality, size and shape capability and applications,” Proc. SPIE 1760, 2–13 (1992).PSISDG0277-786X http://dx.doi.org/10.1117/12.130781 Google Scholar

26. J. J. Swabet al., “Fracture analysis of transparent armor ceramics,” in Fractography of Glasses and Ceramics IV, Ceramic Transactions, J. R. VarnerG. D. Quinn, Eds., Vol. 122, pp. 489–508, American Ceramic Society, Westerville, OH (2001). Google Scholar

27. K. W. WhiteG. P. Kelkar, “Fracture mechanisms of a coarse-grained, transparent MgAl2O4 at elevated temperatures,” J. Am. Ceram. Soc. 75(12), 3440–3444 (1992).JACTAW0002-7820 http://dx.doi.org/10.1111/jace.1992.75.issue-12 Google Scholar

28. J. A. Salem, “Transparent armor ceramics as spacecraft windows,” J. Am. Ceram. Soc. 96(1), 281–289 (2013).JACTAW0002-7820 http://dx.doi.org/10.1111/jace.12089 Google Scholar

29. D. F. PorterJ. S. ReedD. Lewis, “Elastic moduli of refractory spinels,” J. Am. Ceram. Soc. 60(7–8), 345–349 (1977).JACTAW0002-7820 http://dx.doi.org/10.1111/jace.1977.60.issue-7-8 Google Scholar

30. R. L. StewartR. C. Bradt, “Fracture of polycrystalline MgAl2O4,” J. Am. Ceram. Soc. 63(11–12), 619–623 (1980).JACTAW0002-7820 http://dx.doi.org/10.1111/jace.1980.63.issue-11-12 Google Scholar

31. C. BaudinR. MartinezP. Pena, “High-temperature mechanical behavior of stoichiometric magnesium spinel,” J. Am. Ceram. Soc. 78(7), 1857–1862 (1995).JACTAW0002-7820 http://dx.doi.org/10.1111/jace.1995.78.issue-7 Google Scholar

32. “Test method for absorptance of optical laser components,” ISO/FDIS 11551, Geneva (1995). Google Scholar

33. U. WillamowskiD. RistauE. Welsch, “Measuring the absolute absorptance of optical laser components,” Appl. Opt. 37(36), 8362–8370 (1998).APOPAI0003-6935 http://dx.doi.org/10.1364/AO.37.008362 Google Scholar

34. U. Willamowskiet al., “Calorimetric measurement of optical absorption at 532 nm and 1064 nm according to ISO/DIS 11551,” Proc. SPIE 2870, 483–494 (1996).PSISDG0277-786X http://dx.doi.org/10.1117/12.259934 Google Scholar

35. D. A. Orchardet al., “Laser calorimetry as a tool for the optimisation of midIR OPO materials,” Proc. SPIE 5273, 379–387 (2003).PSISDG0277-786X http://dx.doi.org/10.1117/12.523316 Google Scholar

36. M. J. Dodge, “Refractive index,” in CRC Handbook of Laser Science and Technology, M. J. Weber, Ed., Vol. IV, p. 30, CRC Press, Boca Raton, Florida (1986). Google Scholar

37. I. H. MalitsonM. Dodge, “Refractive index and birefringence of synthetic sapphire,” J. Opt. Soc. Am. 62(11), 1405 (1972).JOSAAH0030-3941 Google Scholar

38. W. J. TropfM. E. ThomasT. J. Harris, “Properties of crystals and glasses,” Chapter 33 in Handbook of Optics, M. Basset al., Eds., Table 22, Vol. II, McGraw-Hill, New York (1995). Google Scholar

39. D. C. Harris, “Nonlinear least squares curve fitting with Microsoft Excel Solver,” J. Chem. Ed. 75(1), 119–121 (1998).JCEDA80021-9584 http://dx.doi.org/10.1021/ed075p119 Google Scholar

40. E. J. Billo, Excel for Chemists, 2nd ed., Wiley-VCH, New York (2001). Google Scholar

41. N. C. Ferneliuset al., “Multwavelength laser rate calorimetry on various infrared window materials,” Proc. SPIE 297, 137–142 (1981).PSISDG0277-786X http://dx.doi.org/10.1117/12.932495 Google Scholar

42. J. A. HarringtonD. A. GregoryW. F. Otto, “Infrared absorption in chemical laser window materials,” Appl. Opt. 15(8), 1953–1959 (1976).APOPAI0003-6935 http://dx.doi.org/10.1364/AO.15.001953 Google Scholar

43. J. A. Detrioet al., “Optical characterization of IR transmitting and laser window materials,” AFWAL-TR-80-4188 (1981) cited in  Google ScholarN. C. FerneliusG. A. GravesW. L. Knecht, Characterization of candidate laser window materials,” Proc. SPIE 297, 188–195 (1981).PSISDG0277-786X http://dx.doi.org/10.1117/12.932500 Google Scholar

44. M. E. Innocenziet al., “Room-temperature optical absorption in undoped α-Al2O3,” J. Appl. Phys. 67(12), 7542–7546 (1990).JAPIAU0021-8979 http://dx.doi.org/10.1063/1.345817 Google Scholar

45. P. S. Waylandet al., “Multiphonon extraordinary-ray absorption coefficient for sapphire,” Infrared Phys. Tech. 41(5), 307–312 (2000).IPTEEY1350-4495 http://dx.doi.org/10.1016/S1350-4495(00)00044-X Google Scholar

46. K. Schlossmacher, “Absorption and refraction of the red, blue, and violet spinels of Ceylon,” Z. Kristallogr. 72, 447 (1930). Google Scholar

47. K. VademJ. L. KirkB. N. N. Achar, “Piezo- and thermo-optic behavior of spinel (MgAl2O4),” J. Solid State Chem. 12(3–4), 213–218 (1975).JSSCBI0022-4596 http://dx.doi.org/10.1016/0022-4596(75)90308-4 Google Scholar

48. L. Volpi, “Excel macro Optimiz.xla,”  http://digilander.libero.it/foxes/SoftwareDownload.htm (14 August 2013). Google Scholar

49. C. H. LangeD. D. Duncan, “Temperature coefficient of refractive index for candidate optical windows,” Proc. SPIE 1326, 71–78 (1990).PSISDG0277-786X http://dx.doi.org/10.1117/12.22483 Google Scholar

50. J. A. Salem, “Slow crack growth and fracture toughness of sapphire for the international space station fluids and combustion facility,” NASA-TM-214023 (2006). Google Scholar

51. W. C. YoungR. G. Budynas, Roark’s Formulas for Stress and Strain, 7th Ed., Table 11.4 cases 1a and 8a for rectangular plates and Table 11.2 cases 2e and 10a for circular plates, McGraw-Hill, New York (2002). Google Scholar

52. C. KleinR. P. MillerR. L. Gentilman, “Characteristic strength and Weibull modulus of selected infrared-transmitting materials,” Opt. Eng. 41(9), 3151–3160 (2002).OPEGAR0091-3286 http://dx.doi.org/10.1117/1.1497398 Google Scholar

53. C. KleinR. P. Miller, “How to do a Weibull statistical analysis of flexural strength data,” Proc. SPIE 4375, 241–257 (2001).PSISDG0277-786X http://dx.doi.org/10.1117/12.439181 Google Scholar

54. C. A. Klein, “Flexural strength of infrared-transmitting window materials: bimodal Weibull statistical analysis,” Opt. Eng. 50(2), 023402 (2011).OPEGAR0091-3286 http://dx.doi.org/10.1117/1.3541804 Google Scholar

55. F. SchmidD. C. Harris, “Effect of crystal orientation and temperature on the strength of sapphire,” J. Am. Ceram. Soc. 81(4), 885–893 (1998).JACTAW0002-7820 http://dx.doi.org/10.1111/j.1151-2916.1998.tb02423.x Google Scholar

56. T. M. Reganet al., “Neutron irradiation for sapphire compressive strengthening. II. Physical property changes,” J. Nucl. Mater. 300(1), 47–56 (2002).JNUMAM0022-3115 http://dx.doi.org/10.1016/S0022-3115(01)00708-5 Google Scholar

57. C. KleinF. Schmid, “Weibull statistical analysis of sapphire strength improvement through chemomechanical polishing,” Proc. SPIE 5786, 175–187 (2005).PSISDG0277-786X http://dx.doi.org/10.1117/12.603271 Google Scholar

58. S. M. Sweeneyet al., “High strength transparent spinel with fine, uni-modal grain size,” Proc. SPIE 7302, 73020G (2009).PSISDG0277-786X http://dx.doi.org/10.1117/12.821193 Google Scholar



Daniel C. Harris is a senior scientist and esteemed fellow at the Naval Air Systems Command, China Lake, California, where he is responsible for infrared window materials research and development programs. He has degrees in chemistry from Massachusetts Institute of Technology in 1968 and California Institute of Technology in 1973. He is the author of Materials for Infrared Windows and Domes and a series of widely used textbooks in analytical chemistry.

Robert Seaver received a BS in physics from the University of California, Los Angeles, in 2005. Since 2006, he has worked at the Naval Air Warfare Center Weapons Division, China Lake. His efforts focus on infrared optical metrology, including measurement of reflectance, scatter, absorption, and laser damage threshold.


Giorgio Turri graduated in 2001 at the Universita’ degli Studi di Milano and obtained his PhD in 2001 from the Politecnico di Milano. He began his research in experimental atomic and molecular physics, working at the Elettra Synchrotron in Trieste, Italy, and at the Advanced Light Source of the Lawrence Berkeley National Laboratory in California. His current interests are in optics and photonics, including laser calorimetry and characterization of lasing elements for solid-state lasers. He focuses on spectroscopic properties of rare-earth-doped crystals and glasses.


Michael Bass received a BS in physics from Carnegie-Mellon University and a PhD in physics from the University of Michigan in 1964. He has been active in quantum electronics research since his thesis work on optical rectification. He was among the first to demonstrate homogeneous broadening in dye lasers. He was responsible for the use of the statistical approach to understand laser-induced damage leading to the recognition of electron avalanche breakdown as the intrinsic cause of this phenomenon. He is the coinventor of the YAlO3 laser host and the use of fiber optics and lasers for the treatment of internal bleeding and tumors. He pioneered the use of laser calorimetry for the first absolute measurements of two-photon absorption. His current research centers on the design of improved solid-state lasers, materials with potential for use in upconversion lasers and displays, gain-guided index anti-guided fiber lasers, beam combining using volume Bragg gratings, and novel ceramic crystal optical materials. He is a fellow of OSA and a life fellow of IEEE.

Biographies and photographs of other authors are not available.

© The Authors. Published by SPIE under a Creative Commons Attribution 3.0 Unported License. Distribution or reproduction of this work in whole or in part requires full attribution of the original publication, including its DOI.
Daniel C. Harris, Daniel C. Harris, Linda F. Johnson, Linda F. Johnson, Robert Seaver, Robert Seaver, Tod Lewis, Tod Lewis, Giorgio Turri, Giorgio Turri, Michael A. Bass, Michael A. Bass, David E. Zelmon, David E. Zelmon, Nicholas Haynes, Nicholas Haynes, } "Optical and thermal properties of spinel with revised (increased) absorption at 4 to 5 μm wavelengths and comparison with sapphire," Optical Engineering 52(8), 087113 (26 August 2013). https://doi.org/10.1117/1.OE.52.8.087113 . Submission:


Back to Top