Structure quantification and imaging at submicrometer scales is paramount in research fields from materials science to biology and medical diagnostics. At the molecular level, ultrasmall angle X-ray scattering, often in combination with neutron scattering and nuclear magnetic resonance and computation-heavy molecular modeling, has been very successful in characterizing isolated single molecule structures in solutions. Electron microscopy can provide information about much more complex structural organization such as that of biological cells or tissues with nanometer-resolution imaging. However, it is extremely time, labor, and resource intensive, most often requiring contrast agents, and the extensive sample processing alters the native structure of biomaterials. Optical microscopy techniques are key for imaging materials at the microscale due to their ease of real-time operation and the nondestructive nature of the visible light. The difficulties associated with light microscopy investigation of biological materials are the diffraction limit of resolution () and the optically transparent nature of the biological samples. To characterize structural properties that are indiscernible in microscope images, various techniques have coupled microscopic imaging with spectroscopic quantification.
In particular, spectral or angular properties of light scattering are utilized in techniques such as confocal light absorption and scattering spectroscopic1 microscopy or spectral encoding of spatial frequency,23.–4 for quantifying sizes of structures within the samples. In addition, a multitude of quantitative phase imaging techniques utilizes the spectral interference profiles of wavelength-dependent bright-field microscope images for accurately extracting phase information in a spatially resolved manner.56.7.–8 Conventionally, the light scattering-based techniques quantify the inhomogeneities within the studied samples, and the phase-quantification techniques focus on more cumulative characteristics such as mass and thickness. At the same time, some studies use the spatial distribution or slight changes in a sample’s optical path length to quantify its internal organization at unresolvable scales.89.–10 While some of the above techniques can sense changes occurring at the nanoscale, the rigorous analytical link between exact sample structure and the measured quantity is either unclear or involves strong assumptions about sample structure.
Here, we review one distinct form of spectroscopic microscopy (SM) founded on the interferometric spectroscopy of scattered light, which utilizes the second-order spectral statistic of wavelength-resolved bright-field far-zone microscope images to characterize complex, weakly scattering, label-free media at subdiffraction scales. We also review the three-dimensional (3-D) light transport theory behind the technology with the explicit expression relating to the statistics of refractive index (RI) fluctuations inside the weakly scattering label-free sample with an arbitrary form of RI distribution. SM’s sensitivity to subtle structural changes is widely applicable in fields from semiconductors and material science to biology and medical diagnostics. In particular, SM-based partial-wave spectroscopic (PWS) microscopy has facilitated the development of screening techniques for multiple early stage human cancers1220.127.116.11.16.–17 as well as label-free imaging of the native, living cellular nanoarchitecture.18
Here, we review and emphasize the most important theoretical aspects behind this form of SM. Section 2 provides a basic introduction to SM theory, establishing the physics phenomenon behind its nanoscale sensitivity. Section 3 discusses the length scale (LS) sensitivity of SM in detail from various physically meaningful perspectives. Section 4 presents the main approaches to extracting the internal-only structural information of biological cell structure. Specifically, we will discuss how to design an SM instrument that is perfectly suited to the type of samples studied by the user, methods for measuring structure inside rough media, and comparisons between samples with different thicknesses. Section 5 presents alternative approaches to structural quantification using the SM signal including real-time, whole-slide imaging, temporally resolved quantification, explicit measures of sample structure, etc. Finally, Sec. 6 summarizes and discusses future directions in SM.
Theoretical Principles of Spectroscopic Microscopy
One of the approaches to subdiffraction-scale analysis of material structure is based on the notion of statistical nanosensing, which postulates that structural properties at LSs below a certain limit of resolution can be extracted from the sample organization statistics at larger LSs. In short, when true structure cannot be resolved with absolute precision due to fundamental resolution limits, an optical instrument effectively senses an RI distribution that is blurred or smeared in space. Notwithstanding, when the spatial correlation function (SCF) of this locally averaged RI distribution is quantified by scanning the sample in lateral (as in Ref. 19) or axial directions (as in Ref. 20), the SCF of the original perfect resolution RI can be reconstructed, yielding structural information about LSs far below the resolution limit.21,22 Inverse spectroscopic optical coherence tomography is one example technique founded on statistical nanosensing, and it focuses on evaluating the decay rate of the locally averaged RI SCF.20 The herein reviewed SM technique, in turn, focuses on measuring the area under the effective SCF,19 as discussed in greater detail in Sec. 2.3.
The SM instrument is a white-light epi-illumination, bright-field far-zone microscope with spectrally resolved image acquisition, small numerical aperture () of illumination (), moderate-to-large NA of collection (), and with a pixel size of microscope image corresponding to an area in sample space that is smaller than the diffraction limit of light. In turn, the requirements to sample geometry include: (i) a weakly scattering sample of interest, (ii) sample thickness not greater than the microscope’s depth of field (for most setups, 5 to ), (iii) in the axial dimension, the sample should be RI-matched on one side (substrate in Fig. 1) and has a strong RI mismatch on the other (air in Fig. 1). Below, we thoroughly review the theoretical principles of the method, explaining the physical basis behind the above requirements.
The sample geometry utilized by the SM technique is as follows: a spatially inhomogeneous sample with RI distribution as a function of location is placed on a microscopy slide and exposed to air. Thus, the SM requirements are satisfied as the sample is sandwiched between two semi-infinite homogeneous media (Fig. 1), one of which has a strong RI mismatch with the sample (air ), and the other is RI-matched (substrate RI denoted as ). We assume , mimicking the case of fixed biological samples on a glass slide, where was evaluated using the Gladstone–Dale relation , where is the refractive index of water, is the specific refractive increment (), and is the cell dry density which was approximated as that of stratum mucosum ().2425.–26
To describe light propagation through SM sample, an accurate model of the sample’s internal organization is required. Electron microscopy-based observations of nanoscale material distribution indicate that mass-density distribution inside biological media is best described as continuous random media rather than a multitude of discrete particles. A versatile mathematical approach for modeling light propagation through such media is based on the Whittle–Matern (WM) family of SCF .27,28 The flexible WM correlation family is expressed as2930.31.–32 stretch-exponential at ,32,33 Heyney–Greenstein at ,34 exponential at ,21 and Gaussian at .
In terms of scaling the SCF along the vertical axis, several approaches for the normalization coefficient have been discussed,27 with the major issue lying in the fact that, mathematically, a power-law SCF is infinite at separation distances . At the same time, physically, SCF must equal the variance of RI at . Thus, we follow a normalization approach, in which a smallest structural LS is introduced, and is defined so that is satisfied27,3535 The value of being equal to the size of biological monomers ensures that the macroscopic view of matter applies to all the length scales considered.
In terms of scaling the SCF along the horizontal axis, the width of SCF is regulated by parameters and , with changing the functional form of SCF (in turn affecting its decay rate) and denoting the LS after which RI correlation decays exponentially. Hence, the “width” of SCF is determined by an interplay of and , rather than either of them independently. Therefore, we introduce a more intuitive and universal measure of the SCF width, the effective correlation length , which is the LS at which RI correlation decreases by a factor of from its value at (Fig. 2).
Finally, we note that in a biologically relevant range of sample properties, the physical size of the sample is comparable in magnitude to the characteristic LS of its internal structure (e.g., size of the nucleus as well as chromatin aggregates is comparable to the size of a cell). Therefore, the true SCF of is an anisotropic function which depends on both the internal organization and the sample thickness . Hence, we define and as the statistical properties of an unbounded medium , and the sample as a horizontal slice of with thickness
Importantly, despite the sample being weakly scattering, the Born approximation in its traditional form does not apply due to the required strong RI mismatch at sample–air interface.36,37 As has been validated by numerical full-vector solutions of Maxwell’s equations,19 the Born approximation can still be utilized for calculation of the scattered field inside the weakly scattering object, and ray optics can be used to describe propagation of the incident and the scattered fields across high RI-mismatch interfaces.
Thus, as a unit-amplitude plane wave with a wave vector is normally incident onto the sample, its reflection from and transmission into the sample is described by ray optics. Then, the transmitted field with amplitude is scattered from RI fluctuations inside the sample as described by the Born approximation: the far-zone scattering amplitude of the scattered field with wave vector is , where is the scattering wave vector (inside the sample).36 When the scattered field leaves the sample, its transmission amplitude through the top interface is described again by ray optics . Finally, the field that reaches the image plane of an epi-illumination bright-field microscope is a result of optical interference between (i) the field reflected from the sample’s top surface [referred to as reference arm , amplitude ] and (ii) the field scattered from its internal fluctuations [sample arm , Fig. 1], with only the waves propagating at solid angles within the NA of the objective being collected. Thus, for a microscope with magnification , moderate NA (), focused at a point () in the image plane is38Fig. 3(a)]. As seen in Eq. (4), the objective performs low-pass transverse-plane spatial frequency filtering, with the cutoff corresponding to the spatial coherence length.
Substituting into Eq. (4) and introducing a windowing function that equals one at and zero at [Fig. 3(a)], is
Finally, the wavelength-resolved reflectance intensity recorded in the microscope image, normalized by the image of the light source, is an interferogram
Equation (6) describes the explicit relation between the SM signal and the sample RI distribution. From the optics perspective, Eq. (6) has extended the traditional Born approximation to include high RI mismatch at sample boundaries as well as far-field microscope imaging. From the mathematics perspective, Eq. (6) has established that to describe a one-dimensional (1-D) SM signal, the 3-D problem of light propagation can be reduced to a 1-D problem where the RI is convolved with the Airy disk in the transverse plane.
One important observation to make from Eq. (6) is that due to the RI mismatch at sample interface, the amplitudes of weakly scattered waves are multiplied by the strong reference wave, as a result of which the measured scattering signal increases from to . Thus, the experimental noise generated by background photon flux, shot noise, and dark current noise become negligible, and the remaining noise from temporal lamp intensity fluctuations, on- and off-chip camera noise (i) is much lower in magnitude and (ii) can be reduced even further by frame averaging and frequency-based signal processing. As a result, the signal-to-noise ratio (SNR) is significantly enhanced. A second advantage, as compared to traditional interferometric techniques, such as optical coherence tomography or microscopy, is the simplicity of instrumentation, wherein the reference arm originates at the sample plane, eliminating the need for building a separate optical path for the reference arm.
Quantification of Subdiffraction Length Scales Using Spectroscopic Microscopy
There can be a range of approaches for the quantification of from the SM signal. One notable optical measure of nanoscale sample structure is : the spectral variance of the image intensity within the detector bandwidth .19,21 Since the expectation of the spectrally averaged image intensity equals , is defined asFig. 3(a)]. Denoting as the value of the central wavenumber of illumination bandwidth inside the sample, equals19 Fig. 3(a)].
Given an infinite bandwidth, one could reconstruct the full 3-D RI from . However, since and are finite, detects the variance of an “effective RI distribution,” i.e., of the refractive index that has been smeared in space according to the degree of spatiotemporal coherence, [Eq. (8)]. The SCF of this locally averaged RI, in turn, is a convolution of the SCF of the true RI distribution with the autocorrelation of the underlying resolution-limiting spatial filter of RI:
As shown below, the height of this effective SCF or the variance of the spatially filtered RI distribution presents a measure of sample organization that is sensitive to arbitrarily small structural LSs.
The statistical nanosensing, or the quantification of subdiffractional structural composition of the sample, is achieved by calculating the expected value of (denoted as ), which is related to the RI distribution within the sample as Ref. 19
The general quadrature-form expression relating to PSD [Eq. (10)] is valid for an arbitrary weakly scattering sample, which is RI matched on one side and RI-mismatched on the other side (in the special case of , the expression for has deterministic change in the prefactor and an additional offset value, both of which are defined by the sample geometry19).
As follows from Eq. (10) in most general terms, measures the integral of the tail of the PSD within . Several properties of are direct consequences of this relation:
• is a linear function of the standard deviation of RI fluctuations (which is ).
• As described in more detail below, can be a monotonic function of the width of RI PSD.
• scales linearly with the deterministic sample-geometry parameter .
Importantly, while does not include spatial frequencies above , the subdiffraction-scale structural alterations change the width of PSD and, therefore, the value of . This phenomenon embodies the concept of statistical nanosensing.
Using Eq. (10), closed-form solutions for for specific cases with any particular functional forms of RI SCF can be obtained. The general nature of Eq. (10) also allows numerical evaluation of for a given experimentally obtained SCF that may not have an explicit, analytically defined functional form.
We here present an analytical solution for for the general case when RI SCF is described by the versatile WM family widely applicable in the field of light scattering.27 The PSD of such sample with an infinite size is19
is calculated using the fact that at the RI contrast causing reflection of light is measured by the variance of in the transverse plane19 Substituting the expression for from Eq. (1) and introducing a unitless parameter of size with respect to wavelength , is found:
Therefore, the corresponding contribution to spectral variance becomes
In practice, it is often advantageous to approximate the RI SCF within the sample as exponential, reducing the three-parameter model to two: the LS and the amplitude of RI fluctuations. The exponential approximation of SCF may not be as robust in terms of describing the nature of RI organization as the WM model does via , but it can be useful from the experimental perspective. Furthermore, calculations based on electron microscopy images of biological cell nuclei have shown that the predicted based on the actual, experimentally measured RI distribution is in good agreement with that predicted based on a correlation length value that assumes an exponential RI correlation.21 In this special case of exponential functional form of SCF with RI variance (no is necessary in this case) and exponential correlation length , is found from Eqs. (10) and (14) as19
Length Scale Sensitivity
After establishing that quantifies the statistics of RI distribution inside weakly scattering media by analyzing the spectroscopic content of their microscope image [Eq. (10)], a question arises: what are the structural LSs sensed by ? At first, the answer seems quite simple: senses sample structure with spatial frequencies contained within . However, identification of a more comprehensive LS sensitivity range for , as well as other light scattering means of structure quantification, is remarkably nontrivial.
The difficulty in quantification of LS sensitivity is underlined by the fundamental difference between “resolution” and “sensitivity”: whereas resolution applies to imaging techniques and has a hard, purely instrument-dependent limit (e.g., diffraction limit), the ability to sense scattering events from certain structural sizes largely depends on the sample itself. First, it is simply a matter of which LSs and in what proportion is present inside the sample. The most illustrative example is the blue sky: even the human eye can sense light scattering by molecules smaller than 1 nm when larger ones are absent. Second, as seen in Eqs. (12) and (13), the shape of a sample’s PSD and, therefore, the sensitivity of depend on . Finally, due to the nonlinear relation between and , scattering contributions from different internal structures are not independent or linearly additive.
Thus, a universal LS sensitivity interval of cannot exist, as it always depends on the sample structure. Below, we summarize approaches to assess various aspects of the LS sensitivity of , including (i) the functional dependence of on the shape of RI SCF; (ii) fundamental limits to sizes of detectable structures; (iii) ranges of sizes predominantly detected by within complex samples with various properties of internal organization, including those with analytically defined and experimentally obtained forms of RI SCF.
Functional Dependence on the Shape of Spatial Correlation Function
As a light scattering-based parameter for structure quantification, is defined by the statistics of RI distribution inside the sample rather than the exact 3-D profile of RI. Therefore, we follow the common (in the field of light scattering37) approach of characterizing structural sensitivities through the functional dependence of the measured marker on the width parameters of RI SCF (Fig. 4).
For the general case of WM family of SCFs, Eq. (19) postulates that increases monotonically with the shape parameter within the physiologically relevant range and is weakly dependent on the outer LS [Figs. 4(a) and 4(b)]. Furthermore, for materials with fractal organization ( between 2 and 3), is an approximately linear function of fractal dimension . Note that here to ensure that the functional form of SCF at separation distances below the diffraction limit of light is indeed determined by (SCF decays exponentially at ).
An alternative way to describe the dependence of on the width of SCF is through a single parameter , defined as the separation distance at which SCF decays by a factor of , and referred to as “effective correlation length.” As illustrated in Figs. 4(c) and 4(d), senses arbitrarily small, deeply subdiffractional RI correlation lengths.19 is a monotonically increasing function of the width of SCF, and its functional form at is well approximated to be . At the same time, is independent of for , and therefore, the sensitivity of to changes at smaller correlation lengths is not obscured by changes at larger scales.
We note that in the above two approaches to SCF parameterization, and measure the width of SCF in an interdependent manner [as seen in Figs. 4(c) and 4(d), is bound to increase with ], the use of can be advantageous in cases when the functional form of SCF is unknown, or is not well-represented by an analytical expression (e.g., when the SCF is measured directly from an experiment21,32). At the same time, has a well-defined physical meaning and its use is preferred in cases when the SCF can be well described by .
To summarize, the combination of spectroscopy and microscopy achieves “quantification” of subdiffractional structure using spectroscopy and “visualization” of larger-scale structures using microscopy.
Fundamental Limits to Sizes of Detectable Structures
Next, we note that the width of SCF is a cumulative statistic of all LS present within a sample, and therefore, is a measure of light scattering from all LSs within the sample, including those larger than the diffraction limit of light. Thus, when quantifying the LS sensitivity of through a statistic of RI distribution, it remains ambiguous precisely that structural LSs within the sample are detected. One way to isolate the sensitivity to a given size, or spatial frequency of RI fluctuations, is to evaluate measured from a sample composed of structures with only that spatial frequency.21
Mathematically, unbounded media composed of a single spatial frequency (evaluated in vacuum) are characterized by expectation of PSD in the spatial-frequency domain which is an infinitely thin spherical shell with a radius centered at the origin, [illustrations in Figs. 5(a)–5(d)]. The finite sample, following the definitions of the Eq. (3), is defined as a section of with thickness . It is important to note that the PSD of , due to its finite thickness, is no longer a spherical shell and is expressed as , as shown in Figs. 5(c) and 5(d).
Using Eq. (10), is readily evaluated for single-LS samples with ranging from 10 to 500 nm by computing the integral of within (Fig. 6).
The results of single-LS analysis shown in Fig. 6 established that in principle, can sense RI fluctuations at any spatial frequency whatsoever. Practically, the sensitivity to small LSs is limited only by the noise level of the system, and the largest detectable LS remains the sample thickness . This is in contrast to the fundamental diffraction limit of microscopic resolution that is founded in a physics phenomenon rather than an instrument imperfection. Due to the finite , weakly scattering structures of any size and shape, including RI fluctuations with subdiffractional frequencies above , can still be detected. This is explained by the fact that the Fourier transform of finite structures, due to the convolution with , is nonzero inside . Accordingly, lower values of correspond to wider , resulting in a higher sensitivity of to spatial frequencies outside . For comparison, analogous analysis results corresponding to bulk media with are shown (Fig. 6). In addition, this single-LS analysis has also expectedly demonstrated that has an enhanced sensitivity to frequencies with between and , which corresponded to structures with physical sizes between 20 and 40 nm.
The single-LS analysis presented above does not only establish whether can sense the presence of a particular LS, but also whether it can sense a change in its value. That is, conceptually, the -response as a function of spatial frequency profile shown in Fig. 6 can be thought of as a modulation transfer function, representing the magnitude contribution to from RI fluctuations of same amplitude but different spatial frequencies. Thus, the flat sensitivity profile at signifies that whereas the presence of these larger structures contributes to , their actual size has little to no effect on the value of . At the same time, is sensitive to the value of for small (with an example illustrated in Fig. 5). This twofold nature of LS sensitivity can be thought of both as a disadvantage (ambiguity due to the fact that different large spatial frequencies contribute equally), as well as an advantage ( predominantly senses changes only at small LSs) of the technique, depending on user’s preferences.
From the experimental perspective, it is often relevant to consider media with two LSs, only one of which changes as a result of a particular process. For example, DNA transcription can be represented as a process, in which structural organization at the nucleosome level changes to expose DNA binding sites while the nuclear structure at the level of chromatin aggregates remains unchanged. Inversely, in processes such as macromolecular decondensation, the overall size of the polymer is affected while the monomer structure remains intact.
To model the above-described processes, we consider a sample with two spatial frequencies, and . Then, the larger LSs are retained, whereas the smaller LSs are increased to (no changes in amplitudes of RI fluctuations are applied, illustrations in Fig. 7). This change in small-LS structural organization is reflected in a significant increase in the observed , as calculated using Eq. (10) [Fig. 7(d)]. Then, the is kept unchanged while the larger structures are increased further to . Unlike the first case, this was not reflected in the value of , which is consistent with estimates made based on the LS-sensitivity profile in Fig. 6.
Length Scales Inside Complex Media with the Greatest Contribution to Signal
In actual experimental conditions, samples contain not one or two, but an infinite number of LSs, and a universal interval of LSs having the largest contribution to the measured cannot be determined as it would change with sample structure. First, it is simply a matter of which LSs and in what proportion is present. Second, as shown above, the sensitivity of depends on . Most importantly, as also emphasized above, contributions from different internal structures are not additive due to the nonlinear relation between and . Therefore, the range of LSs predominantly detected by can be found only for a given sample structure.
One method to identify whether a particular LS has a significant contribution to a measured parameter, originally developed in Ref. 39, is to ask a practical question: “Given the SNR of the instrument, can the measured parameter () detect the presence of certain LSs?” The way to answer this question is to simulate “removal” of that LS from the sample and calculate the consequent change in signal. Thus, for lower-LS analysis, the sample’s original is convolved with a 3-D Gaussian filter with full-width half-maximum to result in a “blurred” medium that retains all structures from the original medium that are larger than , but is lacking those smaller than . Similarly, represents with LSs larger than removed from the sample: . Then, the spectral variance of a microscope image that would be measured from a sample without LSs lower () or higher () than was evaluated numerically:21 That is, the lower () and upper () limits of LS sensitivity are the values of such that and .
The results of this analysis, summarized in Fig. 8, have established the lower () and upper () limits of LS sensitivity for a wide range of sample parameters. Naturally, since the range of LSs detected by depends on the LS composition of the sample, and change as a function of RI correlation length (Fig. 8). While there is no analytical relationship describing and in terms of and , their qualitative behavior is the following. As increases, the amount of large LSs increases, and hence the range of detected LSs shifts upward, increasing both and (note that cannot reach and therefore saturates below it at ). Expectedly, the effect of a finite on is much greater in magnitude than that on . In contrast, at small , the sensitivity of to shorter LSs is emphasized, which is quantified by values of lower than that for and approaching its value corresponding to when . For samples with nanoscale RI correlation length and noise floor of 5%, the range of LSs detected by can be summarized as 22–240 nm for all .
The described LS perturbation analysis has been also similarly applied to SCFs that have been measured experimentally. Thus, to identify the size range of structures inside biological cells is quantified by SM, we estimate the RI distribution typical to biological cell nuclei using mass-density SCF measured from transmission electron microscopy (TEM).21,32 Following standard TEM protocol, human colonic cell nuclei were stained with osmium tetroxide (specific to DNA), sectioned, and imaged [Fig. 9(a)]. The gray-scale image intensity, assumed to be proportional to the local density of chromatin, was used to compute the mass-density SCFs of 36 micrographs, after which an average SCF of nuclear material was obtained [Fig. 9(b)]. Since the RI of biological media is a linear function of mass density,26 the SCF of RI distribution equals that of mass-density distribution with a constant prefactor. Since the prefactors of mass-density SCF were unknown (due to the variability in the depth of staining), the RI SCF was normalized to 1 at the origin ().
The information contained in the experimental SCF was used following two approaches. First, an exponential SCF was fitted to the experimental [coefficient of determination for the fit between 39 and 1000 nm was , Fig. 9(b)] and the effective exponential correlation length was found as 156 nm. Then, the previously described analysis was carried out for two values of , 1.5 and (mimicking the thickness of squamous and columnar epithelial cell nuclei). Second, to evaluate how well the model of an exponentially correlated medium applies to biological cells, the EM-measured SCF was used by itself. However, since the experimental SCF was only defined at (resolution of TEM micrographs), some analytical extrapolation was necessary to extend it to , which was performed using the fitted exponential SCF at [Fig. 9(b)]. Continuous random media with SCF equivalent to the experimental were then generated and the LS perturbation procedure was performed.
An excellent match between and calculated based on analytical and experimental SCFs was observed for all values of (Fig. 10). Applying the 5% SNR threshold, the following ranges of to intranuclear structures were derived: predominant LS sensitivity was observed from 25 to 427 nm based on the analytical SCF, and from 25 to 441 nm based on the experimental for nuclei with , and from 23 to 324 nm for analytical SCF, and from 23 to 334 nm for experimental for nuclei with . Additionally, from the interval corresponding to the steepest decline in and calculated for both thicknesses and SCFs, it has been observed that the greatest contribution to measured from biological cell nuclei originates from structures smaller than 200 nm in size (Fig. 10).
Quantification of Sample’s Internal Organization: Practical Considerations
Instrument Design: Numerical Apertures, Light Bandwidth, and Central Wavenumber
Generally, the design specifics of an SM instrument are very simple with example schematic shown in Fig. 11: a bright-field reflected light microscope with broadband incoherent illumination (Koehler illumination scheme is recommended for spatial uniformity of light intensity), low NA of light incidence () and moderate-to-large NA of the light collection (simply NA throughout this review). Below, we review the main design principles to guide the user choices for any particular technique application.
In order to the underlying relation in Eq. (5) to hold, one needs to ensure that RI effective averaging in the lateral plane occurs only due to the diffraction limit of the light. Therefore, the pixel size of the detector CCD camera needs to be small enough to oversample the diffraction limited area , where is the microscope’s total magnification and is the size of a diffraction-limited spot in the sample plane.
Illumination Numerical Aperture
Our derivations in Eq. (4) assume plane-wave illumination normal to the sample, i.e., an of zero. Using FDTD-synthesized SM images of 800 samples with two different thicknesses ( and ), and 20 subdiffractional , it was established that the value of is independent of ( change compared to ) for any finite (Fig. 12). Note that reducing the also reduces the light output and, subsequently, the speed of data acquisition. At higher above 0.4, an overall decrease in the absolute value of is observed at all with an insignificant reduction in the slope of its correlation-length dependence . Thus, is independent of when , and begins to decrease in magnitude at , leading to a lower SNR and a gradual decrease in dependency on . Based on this analysis, we suggest selecting . Finally, we note that these FDTD simulation results also confirm the accuracy of the plane-wave illumination approximation that has been used in the original derivation in Sec. 2.2.
Collection numerical aperture
The collection NA is a crucial setting of the SM instrument as it not only affects the SNR of the collected signal, but also has the ability to qualitatively alter the functional dependence of on the LSs within the sample (Fig. 13). The dependence of on NA is best explained through the two constituents of : and [Eq. (14)]. As easily seen in the simplified Eq. (20), is nonmonotonic and increases rapidly with NA, whereas is monotonic and less dependent on NA [Figs. 13(a) and 13(b)]. Thus, as NA rises, the relative contribution from the nonmonotonic component increases, as a result of which the total becomes less monotonic [Fig. 13(c)]. This transition is best noticed when the magnitudes of and are comparable . For this regime, we suggest a moderate NA of 0.3 to 0.6. For thinner samples, is monotonic even at large NA, hence should be chosen as it maximizes the SNR. For thicker samples, a monotonic functional dependence of can be always achieved by reduction of NA.
Wavenumber range Δk
In order to accurately measure the spectral variance , the spectra should contain at least one full oscillation. Since a wider bandwidth allows observing lower spectral frequencies, the spectral bandwidth should be chosen to satisfy , with denoting the average RI of the sample.
Central wavenumber kc
The central wavenumber affects along both the vertical (magnitude of ) and horizontal () axes. Along the vertical axis, the impact of is similar to that of NA: while overall a higher leads to a higher SNR, increases more rapidly than hence can affect the monotonicity of . Along the horizontal axis, the LSs of the material are always measured with respect to the wavelength of light, and from the physics perspective is truly a function of rather than alone. Thus, by varying , one can stretch or shrink along the horizontal axis. From the experimental perspective, unlike the NAs of the system, is not an easily adjustable parameter. Thus, it is most often impractical to significantly change in order to affect the system’s SNR or the shape of dependence. Nevertheless, understanding of the effect of on can guide light source choices and other instrument design adjustments. For example, if is low, one might consider increasing the objective NA to compensate for the loss in SNR without sacrificing the monotonicity of or vice versa. Note that the design recommendations and curves provided in this review were based on 500 to 700 nm bandwidth of light.
In conclusion, the instrument design parameters can be selected as the following: (1) choose microscope magnification and camera pixel size to ensure that the sample area imaged by one camera pixel is smaller than the diffraction limit of light, (2) set to keep -dependent SNR loss , (3) set a moderate NA between 0.3 and 0.6, with exact value optimized depending on sample thickness and the observed SNR, and (4) choose a light source with bandwidth satisfying in order to capture at least one full oscillation in the spectra (Table 1).
Choice of instrument parameters to achieve optimal performance.
|M||Camera pixel size below M×1.22λ/(NAi+NA)|
Optimal NA values depend on L, range given for isolated fixed biological cells, L<3 μm.
Measurements from Rough Samples
As seen in Eq. (6), the light reflection occurring at the air–sample interface serves as a reference arm performing a crucial role in the formation of the SM signal. For samples with smooth top surfaces and the magnitude of reference arm reflection, is a zero-frequency deterministic offset determined solely by the contrast between RI of air and the average RI of sample. When the dispersion of sample RI is weak (as it is in biological media), is wavelength-independent and simply scales the value of .
In cases when the sample top interface is not a horizontal plane, a careful consideration of sample surface features is needed. Thus, if the variation in sample height within a diffraction-limited area is negligible (standard deviation of height 40), then for every pixel of SM image the sample can be considered flat. The between-pixel differences in sample height are accounted for when is subsequently normalized by , as discussed later in this review.
However, when the top surface of the sample has significant height variations within a diffraction-limited area (i.e., ), the reference-arm reflectance becomes dependent on wavenumber (Fig. 14). Therefore, as seen in Eq. (6), the consequent effect of nanoscale roughness on the SM spectra is twofold: (1) the baseline, reference-arm reflectance ceases to be a zero-frequency offset and thus contributes to the measured spectral variance and (2) the interferogram of reference-arm reflection and the light scattered from internal RI fluctuations spectral oscillations is multiplied by a wavelength-dependent reflectance . As a result, a low-frequency component is added to the detected interference oscillations [blue spectrum in Fig. 15(j)].
In order to quantify the RI fluctuations within the rough sample, the detected reflectance spectrum undergoes simple postprocessing to remove the effect of nanoscale roughness: (i) is computed as a second-order polynomial fit to the detected spectrum , (ii) the fluctuating part of the reflectance intensity is obtained as (transmission coefficients and are neglected here as they ), and (iii) that is independent of sample surface properties is calculated as the standard deviation of . Physically, the newly introduced parameter is a measure of nanoscale organization within the sample equivalent to the previously described . However, unlike , is calculated not simply as standard deviation of detected spectra, but rather the standard deviation of the surface-independent fluctuating part which is here necessitated due to surface roughness.
Figure 15 shows illustration to the established ability of the SM technique to quantify structural differences at deeply subdiffractional scales within samples with smooth as well as rough surfaces. Thus, while structural composition within the inhomogeneous samples is impossible to assess from their bright-field microscope images [Figs. 15(a)–15(c)], panels (d) and (e) illustrate that can quantify subdiffractional differences inside smooth samples, and panels (e) and (f) show that is affected by surface roughness. Meanwhile, figures in panels (g)–(i) confirm the ability of to measure changes in internal-only sample structure, independent of their surface features. The influence of (amplitude of spectral oscillations) and surface roughness (additional low-frequency component creating an overall “tilt” to the spectrum) on SM spectra are shown in panel (j).
Comparing Samples with Different
As seen in Eq. (10), depends on sample thickness , and when an SM signal is acquired from samples with different values of , may not accurately quantify the differences in the internal-only organization within those samples [Fig. 17(a)]. Thus, in order to quantify the internal structure of a sample, must be normalized by . Note that the expected value of spectral variance normalized by the unitless parameter is the integral of the PSD tail of sample’s internal organization with known prefactors determined by the instrument setup (NA, , ) and sample geometry ():Fig. 16(a). Transition from to for samples with very different thicknesses and nanoscale correlation lengths is illustrated in Fig. 17.
An alternative way to define the disorder strength is , which can be predicted from as with . While this relation is more accurate than that in Eq. (23) (, between 0.5 and as above) and has been utilized in previous works,4142.–43 it is only valid for a smaller range of structural LSs .
Finally, for fractal media can also be used to measure the fractal dimension of sample organization. While the explicit analytical relation between and given in Eq. (19) is quite complex, for fractal media is linearly proportional to both [, Figs. 4(a) and 4(b)] and , therefore, a simplified empirical expression can be obtained. For samples with , the fractal dimension in combination with the standard deviation of RI can be predicted from measured by SM asFigure 16(b) shows the predictions of from for samples with different thicknesses, also confirming the lack of their dependence on . Based on Eq. (19), becomes independent of when thickness is large, as a result of which predictions converge to their true theoretical values. For , in turn, the predicted is still a monotonic function of the theoretical, but overestimates its true value.
Importantly, while the above relations are shown on examples of exponential or fractal RI SCFs, an arbitrary correlation function can always be described through the effective correlation length , defined as separation distance at which correlation decays by a factor of . In this case, the relation still holds (as illustrated in Fig. 4), and the spatial distribution of material can still be described through . The monotonic relation between the fractal dimension and the effective correlation length is shown in Fig. 18.
In summary, to measure the structural characteristic of purely internal nanoscale organization of complex, weakly scattering samples, one needs to measure as well as the sample’s optical thickness with respect to central wavenumber . To measure a sample’s optical thickness, a range of techniques can be employed. Methodologies for measuring a sample’s physical thickness (which necessitates an assumption of sample’s RI) include atomic force microscopy and optical interference-based optical profilometry.44 At the same time, a sample’s optical thickness can be measured via a range of quantitative phase microscopy (QPM) techniques as reviewed in Refs. 45 and 46. Regarding the QPM techniques, we note that the QPM feature could not be combined with our instrument since an altered incident light path would be required along with transmission-mode light collection scheme. Below, we review two methods for obtaining a sample’s optical thickness from SM-registered signal itself, with no need for additional instrumentation or data acquisition steps.
As follows from Eq. (6), the classical SM spectrum consists of a deterministic zero-frequency offset and a fluctuating component . The highest spectral frequency in the fluctuating component corresponds to the interference between the waves reflected at and , with the corresponding optical path difference (OPD) between the two waves equal to . Thus, the optical thickness of the sample can be measured by taking the Fourier transform of the fluctuating component of registered SM spectrum evaluating the highest spectral frequency of the measured signal.
Note that the accurate measurement of sample optical thickness given the sample geometry required by the SM technique (RI match at one interface) is complicated by the fact that sample–substrate interface does not always reflect light due to the low RI contrast at the bottom interface typical to fixed biomaterials on glass slides. Specifically, this is the case when is smaller than the diffraction-limited spot and the frequency-space spectrum does not necessarily contain an evident peak at . Nevertheless, the spectral-frequency composition of the SM signal can be analyzed to extract thickness without the need for additional instrumentation or data acquisition steps. Below, we review two methods for sample thickness evaluation from an SM signal (a) based on the decay rate of the autocorrelation of the fluctuating component ,41,43 and (b) based on the shape of the frequency-space spectrum .23
Spectral correlation decay rate
One way to measure is through the autocorrelation of the registered SM spectrum. Let the autocorrelation function of be defined as . Then by definition, the correlation decay rate (CDR) is
Equation (27) simplifies the understanding of how CDR depends on . Depending on the shape of , CDR in a noiseless system can be anywhere from [scattering probability is same for all and can be approximated as a top hat function] to [simple thin-film interference, with being a delta-function ].
In realistic systems where detector noise is present, has noise contributions at all depths , and CDR becomes a complex function of , SNR, the type and cutoff of low-pass filter used to eliminate spectral noise, as well as the spectral resolution bandwidth of the detector. In simple terms, this dependence can be explained as follows: after low-pass filtration of the detected spectrum, noise contributions to at are eliminated, and CDR is expressed as
Defining SNR as , we obtainFigure 19 shows the accuracy of thickness predicted from CDR according to Eq. (30) for various and SNR, where the value of CDR is evaluated either directly from FDTD-simulated physical experiment [Figs. 19(b) and 19(c)] or theoretically via the Eq. (29) [Fig. 19(c)]. The close match with the CDR values obtained from FDTD simulations of a physical experiment confirm the accuracy of the CDR estimates in the conditions of experimental noise as derived in Eq. (29).
Decay of the frequency-space spectrum
Another signal processing algorithm capable of accurate sample thickness measurements at even lower values of SNR utilizes the fact that no light scattering events occur at , and therefore, the expectation () of the absolute value of frequency-space spectrum always decays at .23 While the exact shape of decay tail at has no closed-form analytical expression, this shape can be quantified and stored numerically using the library if FDTD-simulated data for a range of sample properties.
Since the shape of depends on the RI correlation length , a fourth-order polynomial was fitted to all FDTD-calculated frequency-space spectra at for samples with 20 values of (between 20 and 250 nm), and a library of corresponding polynomial coefficients was stored. Then, the optical thickness of the sample is determined as the -location corresponding to the best fit between an arbitrary experimentally measured decay and that reconstructed from the stored library of . The excellent accuracy of thickness predicted from the tail of at for FDTD-synthesized SM data from sampled with various and SNR is shown in Fig. 20.
To summarize, optical thickness of a studied sample can be calculated from the SM signal using the frequency content of the registered spectra. One option is to use the decay rate of spectral correlation function, CDR. This method allows accurate thickness predictions for samples thicker than 800 nm [Fig. 19(c)]. In addition, thickness can be predicted for each diffraction-limited spot. The disadvantage of this method lies in the high sensitivity of CDR to the presence of experimental noise: when the thickness predictions become inversely proportional to [Fig. 19(b)].
Another method for thickness reconstruction using an SM signal is based on evaluating directly from the shape of its Fourier transform. The advantages of this method include the independence of noise floor for and a high accuracy in predicting thickness for samples as thin as 200 nm. However, this method requires calculation of the expected value of the frequency-space spectra, which means that from different diffraction-limited spots needs to be calculated and averaged to yield . Thus, the spatial resolution of thickness determined with this method is diffraction-limited spots.23 Other disadvantages of this method stem from the fact that it is based on a curve-fitting, error-minimization algorithm. Thus, in addition to requiring longer computational time, this method can be prone to large errors when the experimental and the theoretical curves do not match well, such as when the experimental sample has microscale roughness, or when due to certain hardware specifics the system’s noise is not white noise.
Finally, Fig. 21 shows the comparison of thickness predictions from a complex, rough experimental sample (tissue biopsy) predicted via CDR [Figs. 21(a) and 21(b)], decay of the frequency-space spectrum [Fig. 21(c)], and an atomic force microscope [Fig. 21(d)].
Alternative Markers of Spectroscopic Microscopy
Naturally, the SM microscopy signal can be analyzed in a range of ways. In this paper, we provided an in-depth review of the spectral variance and its measurement of the nanoscale structure within weakly scattering samples. In fact, the disorder strength measured through in the SM-based PWS microscopy technique has proven effective in detecting hallmarks of carcinogenesis in histologically normal-appearing cells, facilitating the development of accurate screening techniques for multiple early stage human cancers, including cancers in lung,13,42 colon,41,42,47 ovaries,14 pancreas,42 esophagus,15 and prostate.16
At the same time, an optical parameter equivalent to can be calculated when the standard deviation of reflectance (at a single wavelength of light) is taken across pixels of the registered bright-field microscope image, instead of evaluating it across different wavelengths as reviewed herein.48 That is, the standard deviation of reflectance across different realizations of media with same statistical properties (i.e., standard deviation across pixels) is identical to standard deviation of reflectance from the same medium (registered in a single pixel) measured at different wavelengths of light. In general, measuring the spectral standard deviation has the advantage of quantifying the sample subvolumes imaged by individual pixels independently and thus not making the assumption of different pixels imaging statistically equivalent samples with similar physical thicknesses. Nevertheless, in cases when samples can be assumed to be statistically homogeneous, evaluation of a sample’s internal properties using few () wavelengths of light instead of 200 has the advantage of system speed improvement by orders of magnitudes along with the possibility of obtaining measurements of whole microscopy slides,48 both of which have great promise for the translational applications of the technique. The applicability of reduced-wavelength to a given type of samples can be tested by performing an initial set of full-wavelength measurements after which the spatial homogeneity of structural properties within those sample can be evaluated when is compared to .
Another array of possible ways to quantify sample properties is through the frequency decomposition of reflectance spectra, i.e., their Fourier transform. From the physical origin of the SM signal as described by Eq. (6), frequency decomposition allows us to identify the depth inside the sample at which the measured scattering events have occurred (Fig. 20) with a resolution defined by the bandwidth of light. This information can be used in a range of ways, as follows. First, in the case of thick samples with the frequency spectrum can be used with no further postprocessing as means of depth-resolved nanoscale structural quantification. Second, a partial integration of the frequency-scape spectrum can be performed: , where is the smallest possible thickness for the given sample type. This method avoids the thickness-dependence of measured quantity , as only the scattering events occurring within are quantified regardless of the true sample thickness. The disadvantage of this method lies in the fact that when reflectance at is not measured, [Eq. (14)] which is a nonmonotonic function of the structural LS .
Finally, since conveys the power of light scattered at depth , it can be used to obtain two independent optical measures of sample structure: (scattering inside the sample) and [scattering at , Figure 22(a)23]. Hence, following the known analytical equations for and [Eqs. (18) and (17)], the explicit physical properties of sample structure and can be independently calculated [Fig. 22(b)]. The obvious great advantage of this approach lies in measuring nonambiguous, explicit, spatially resolved parameters of sample structure. The disadvantages include the assumption of sample statistical properties being similar at and as well as the necessary multistep signal postprocessing algorithm which, given imperfect experimental data, can cause error accumulation.
Summary and Outlook
Despite the diffraction limit of imaging resolution, the second-order statistic of the spectroscopic content of a reflected-light bright-field microscope image contains information about the structural organization within a label-free weakly scattering sample at arbitrarily small length scales, limited only by the SNR rather than by a physical phenomenon. Here, we have reviewed the fundamental principles behind the technique’s LS sensitivity and provided a detailed description of its various aspects. In addition, we discussed the different approaches to data analysis which can be taken depending on the characteristics of studied samples, such as degree of nanoscale surface roughness and sample thicknesses, as well as on how important the spatial resolution of nanoscale information () and the speed of data acquisition () are for the particular application. Similarly, some of the instrumentation features can be adjusted to achieve the desired depth of focus, or the sample geometry can be altered to allow measurements from other sample types, such as living biological cells,18,49 while satisfying the requirements of the technique.
From the instrumentation perspective, the SM technique is quite simple and can even be built into a commercial microscope.18 A crucial aspect of the technique is the sample geometry. First, it ensures the existence of a reference arm and leads to an SNR () that is much greater than that of methods detecting the intensity of scattered light directly from the sample (). Second, combined with the sample thickness not exceeding the microscope’s depth of field, it defines the nature of SM’s LS sensitivity, as discussed in Sec. 3.2.21
Importantly, the unique aspect behind the technology is not the instrument itself, but rather the derived nanoscale-sensitive marker . It offers distinct advantages compared to the textbook optical properties which the common light scattering spectroscopic techniques quantify, such as the backscattering () and the total scattering () cross sections. has a nonmonotonic dependence on which makes the inverse problem ambiguous,37 and increases steeply and thus is relatively insensitive to structural changes at small length scales.39 , in turn, is a “monotonic” function of the length scale composition of the sample, with its value saturating at large length scales, as a result of which it exhibits a predominant sensitivity to changes at subdiffraction length scales.19 Finally, as reviewed herein, possesses a unique ability to detect structures at any length scale whatsoever.21
The SM approach also clearly differs from other label-free techniques utilizing the spectral content of diffraction-limited microscope images for extracting structural information about the sample. Unlike the high-precision quantitative phase techniques, it measures the fluctuations of RI rather than its longitudinal integral. Compared to subdiffraction-sensitive techniques such as confocal light scattering and absorption spectroscopy,1 spatial-domain low-coherence QPM,8,9 spectral encoding of spatial frequency,23.–4 or nanoscale nuclear architecture mapping,10 the theory behind SM1 does not impose strong assumptions such as approximation of the medium as solid spheres or having a dominant length scale2 and provides an explicit relation between the sample’s complex 3-D RI distribution and the derived quantitative measure . This relation is applicable to arbitrary types of RI distribution within the sample: continuous or discrete, random or deterministic, statistically isotropic or not.
SM, with its great advantages for basic science, biology and medical applications, enables quantitative assessment of the microscopically indiscernible, nanoscale structural features of optically transparent materials such as biological cells and tissues without the need for external contrast agents. Thus, PWS microscopy utilizes SM to detect intracellular structural alterations preceding tumor formation both for the development of early cancer screening methodology,17 and for basic biology studies of the mechanisms behind tumor-specific intracellular alterations as well as their effect on gene regulation.50 Prospects for the reviewed technique also include identification of new cancer therapeutics by offering intracellular ultrastructure-based approach to screen drugs for their ability to revert malignancy-associated changes. In addition, the relatively simple instrumentation requirements open the door to a wide range of possible directions for further technology development. This includes a high-throughput automated whole-slide SM approach complementing highly effective tools such as whole-slide microscopy and digital pathology, sample geometry alterations to allow both structural and temporal data acquisition from live biological cells, as well as implementation of confocal, structural, or other illumination techniques to obtain axially resolved, 3-D cubes of the nanoscale-sensitive marker or the explicit parameters such as RI correlation length and variance.
This study was supported by the National Institutes of Health under Grant Nos: R01CA200064, R01CA155284, R01CA165309, R01EB016983, and U54CA193419, and by the National Science Foundation under Grant No. CBET-1240416, and by the Lungevity Foundation. The FDTD simulations were made possible by a computational allocation from the quest high-performance computing facility at Northwestern University.
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Lusik Cherkezyan is a postdoctoral fellow in the Department of Biomedical Engineering, Northwestern University, Evanston, Illinois, USA, where she has also received her PhD. Her work focuses on the use of physics and engineering principles to the study of biological systems. In particular, she is interested in technology development for the spectroscopic quantification of biomaterials at nanometer scales. Her work has been published in multiple high-profile journals, including Physical Review Letters, BMC Cancer, Optics Letters, Endoscopy, etc.
Di Zhang received his BS degree in electrical engineering from Beijing Jiaotong University, China, in 2009. He is currently working toward his PhD in biomedical engineering at the Northwestern University, Evanston, Illinois, USA. His research interests include computational electromagnetics for modeling light interaction with biological tissue and optical imaging techniques for early stage cancer detection.
Hariharan Subramanian received his PhD in biomedical engineering from Northwestern University, where he is currently a research professor of biomedical engineering. He is the cofounder and chief technology officer of NanoCytomics, an in vitro medical diagnostic company developing screening strategies for different types of cancers (e.g., lung, colon, prostate, etc.). He has considerable experience in biomedical optics, cancer biology, and clinical research, with numerous publications appearing in leading peer-reviewed journals.
Ilker Capoglu received his PhD from the School of Electrical and Computer Engineering at Georgia Institute of Technology in 2007. Since 2014, he has been served as a local Houston manager and scientific advisor for the Electromagnetics Sensor Physics Group at Halliburton. He has authored 21 peer-reviewed publications in high profile journals such as Progress in Optics, IEEE TAP, Physics Review Letters, and PNAS. He is the principal developer of a comprehensive numerical electromagnetics software package (“Angora”).
Allen Taflove is a professor in the Department of Electrical Engineering and Computer Science, Northwestern University, Evanston, Illinois, USA. Since 1972, he has pioneered finite-difference time-domain (FDTD) computational solutions of Maxwell’s equations, for which he received the 2014 IEEE Electromagnetics Award. His major publication, Computational Electrodynamics: The Finite-Difference Time-Domain Method, is the 7th most-cited book in physics.
Vadim Backman is the Walter Dill Scott professor of biomedical engineering at Northwestern University and a program leader at the Robert H. Lurie Comprehensive Cancer Center in Chicago, Illinois, USA. An internationally renowned expert in biomedical optics, he develops revolutionary nanoscale imaging technologies that allow researchers to explore previously intractable questions in biology, disease diagnosis, and progression, with a focus on detecting cancer at its earliest and most treatable stages.