Abstract
Cementitious materials are complex composites that exhibit significant spatial heterogeneity in their chemical composition and micromechanical response. Modern 3-dimensional characterization techniques using X-rays from synchrotron light sources, such as micro-computed tomography (μCT) and far-field high-energy diffraction microscopy (ff-HEDM), are now capable of probing this micromechanical heterogeneity. In this work, the above mentioned techniques are used to understand the varying micromechanical response of crystalline phases (cubic iron oxide and α-quartz) inherently present within an alkali-activated fly ash (AAF) during in-situ confined compression. A subset of the crystals probed using ff-HEDM are registered with the tomographic reconstructions and tracked through the applied loads, highlighting the combination of μCT and ff-HEDM as a means to examine both elastic strain in the crystalline particles (and by extension local stress response) and plastic strain in the matrix. In this study, significant differences in the load carrying behaviors of the crystalline phases were observed wherein the cubic iron oxide crystals laterally expanded during the confined compression test, while the α-quartz particles laterally contracted and at the final load step, shed load likely due to failure in the surrounding matrix. Finally, the two characterization techniques are discussed in terms of both advantages and associated challenges for analysis of multi-phase cementitious materials.
Similar content being viewed by others
Introduction
By quantity, concrete is the world’s most prevalent structural material and its production comes with a sizable carbon footprint: production of one ton of portland cement generates 0.9 tons of CO21. In 2017, 4.1 billion tons of cement were produced worldwide resulting in approximately 5% of the global CO2 emissions2. As such, any advances that reduce the amount of portland cement produced, either through replacement with more environmentally-friendly alternatives or more judicious usage, can provide major ecological benefits. However, before alternative cementitious materials (ACM) are adopted or new design parameters implemented, the response of the material under its expected environmental conditions must be well understood. Over the past decade, several laboratory-scale tests have been conducted to probe the behavior of ACMs3,4, but significant gaps still exist between our understanding of the connections between microstructure and macroscale properties.
The example ACM studied herein, alkali-activated fly ash (AAF), falls under a class of alkali-activated binders that form inorganic polymers5. This class of materials is generally produced by activating an alumino-silicate powder such as fly ash, blast furnace slag, or metakaolin, with an alkaline solution such as sodium/potassium hydroxide occasionally mixed with sodium/potassium silicates6. Apart from being low cost and environmentally friendly7, these materials are receiving increasing attention as a replacement for portland cement-based concretes because of their: resistance to alkali aggregate reaction8,9, freeze-thaw durability10,11, sulfate attack12,13, corrosion resistance14, improved early age shrinkage15, less susceptibility to carbonation16,17, ability to encapsulate nuclear waste18, improved compatibility with oil well drilling fluids19 and good adhesion and binding to multiple surfaces including metallic substrates20.
Although these materials are promising, their use in the industry has been limited. A path forward for accelerating the adoption of ACMs requires a better understanding of how the micro structure of a cementitious material ultimately dictates its macroscale performance21,22,23,24. Ideally, characterization of a micro structure could lead directly to prediction of performance, precluding the need for exhaustive macroscale testing to find materials suitable for use. Efforts have been placed to understand dissolution kinetics5, geopolymerization process5 and degree of hydration25 in order to improve prediction models. One of the greatest identified challenges in the modeling of cement-based materials is accounting for the heterogeneous spatial distribution and properties of the various phases in the cement paste. To date, the primary tool for characterizing the spatial heterogeneity of mechanical response at lower length scales has been nanoindentation22,26,27,28. While providing excellent spatial resolution of elastic moduli across phases, the highly localized nature of the measurement prevents it from being able to explore interactions between phases and how these interactions change with deformation. In this work, we demonstrate how methods such as 3-dimensional (3-D) X-ray absorption and diffraction-based characterization techniques can be used to quantify the micromechanical response of crystalline phases. In ACMs, the response of these phases is influenced by the surrounding matrix, and understanding these interactions brings the field one step closer to the rapid adoption and effective use of by-products and waste materials.
The X-ray techniques used to study the AAF in this work are micro-computed tomography (μCT) and the far-field variant of high-energy diffraction microscopy (ff-HEDM). The use of μCT29 to characterize damage induced in cementitious materials is well established for studying the evolution of void and crack growth under load30,31,32,33, corrosion-induced cracking34, alkali-silica reaction35,36, sulfate attack37,38, autogenous healing39, leaching40, and freeze-thaw cracking41. X-ray diffraction has been used to study cement hydration and geopolymerization kinetics42,43,44,45,46,47,48 using synchrotron light sources, however the application of 3-D diffraction techniques, such as ff-HEDM, to study micromechanical behavior of cementitious materials is significantly less well established. The ff-HEDM technique is capable of quantifying the orientation, centroid, and elastic strain state of individual crystals as a sample is deforming in-situ. A combination of μCT and ff-HEDM applied to probing the deformation of a model portland cement paste embedded with ~100 μm pure single crystal α-quartz, which served as distributed micromechanical measurement points, is the only [known] study to date49. The model system, however, avoided many data analysis challenges associated with tracking crystalline phases that are inherently present in most cementitious materials.
In general, cementitious materials are composed of multiple crystalline phases with a wide distribution of crystal sizes, producing diffraction signals ranging from distinct diffraction peaks to continuous Debye-Scherrer rings. The ff-HEDM technique relies on the ability to track diffraction peaks from individual crystals generally in the 10 μm to 500 μm range. Other X-ray scattering from fine crystalline phases (crystal size <10 μm) or amorphous phases are also captured on the detector, but are not the focus of the current study. Herein, we will explore how ff-HEDM can be used to analyze the elastic strains of phases with crystals of size and number density conducive to producing distinct single crystal diffraction peaks on the detector and subsequently the distribution of load within these crystals.
The structure of the paper is as follows. μCT and diffraction based strain data are provided in the results section. The results are discussed, with special focus placed on the challenges of data reduction and possible means to extract more from the data, followed by a summary. In the Methods section, the composition of the fly ash used and the sample preparation method are provided. Next, the experimental and data processing procedures are outlined. In this work, compressive normal strains and stresses will be defined as positive.
Methods
Materials and sample design
A reclaimed, thermally-beneficiated class F fly ash50 from a coal power plant in Maryland was used in this study. The oxide composition was provided by the manufacturer (SEFA group) and can be viewed in Table 1. The fly ash is composed of ~70% aluminosilicates by weight and more than 20% iron oxide, with minor amounts of calcium oxide and magnesium oxide. Fly ash in general is composed of both crystalline and amorphous phases with a wide distribution of particle sizes. The particle size distribution of the raw fly ash particles was obtained using Malvern Mastersizer 2000 with a wet dispersion unit and can be viewed in Fig. 1. The d50 of the fly ash is 14 μm, indicating that 50% of the particles by volume are larger than 14 μm.
The AAF sample was prepared by mixing the fly ash described above with 8 M sodium hydroxide solution at a solution-to-fly ash ratio of 0.485 (by weight) based on preliminary tests for optimum strength and workability. 8 M sodium hydroxide solution was prepared by weighing reagent grade sodium hydroxide pellets and dissolving them in ultrapure water (resistivity of 18 MΩ-cm). The solution was set aside for at least 24 hours to allow for dissipation of heat. The AAF slurry was mixed in a 15 ml centrifuge tube using a vortex mixer for 1 minute. A vortex mixer was used instead of a high shear mixer51 because of the high viscosity of the slurry. After mixing, the slurry was injected into a 1.59 mm \((\tfrac{1}{16}^{\prime\prime} )\,{\rm{ID}}\), 3.18 mm \((\tfrac{1}{8}^{\prime\prime} )\,{\rm{OD}}\), 5 mm long polyether ether ketone (PEEK) tube (c.f. Fig. 2a) using a blunt #18 gauge needle. PEEK was chosen for its resistance to degradation in the presence of unreacted sodium hydroxide solution. A 3 mm tall volume of slurry was injected into the tube, providing a 2 mm gap at the bottom of the PEEK tube, which was used for guiding the sample onto the bottom loading platen. The current sample design was formulated in an attempt to follow common practice for compressive strength testing (cylinders in ratio of 1:2 for diameter:height), along with ensuring the cylindrical samples were centralized on the loading platen and in the path of the beam.
The AAF slurry contained within the PEEK tube was cured in a high humidity environment at 76 °C (170 °F) for 10 days. Typically for mixtures with low calcium fly ashes, it has been reported in literature that curing temperatures in the range of 40°–100 °C yield higher early strengths3. Prior to this work, extensive research was conducted to understand the behavior of this AAF for oil well cementing, a bottom hole temperature of 76 °C is typical. Furthermore, the age was chosen to satisfy time constraints associated with synchrotron use and so that the results could be compared to existing results52 in the 7–14 day age range. Details about the mechanical properties of this AAF slurry in comparison to ordinary portland cement slurry can be found elsewhere52. Care was taken to ensure both the top and bottom surface of the sample were flat and parallel to each other. This ensures that the sample will remain vertical and the load will be transmitted uniformly along the loading axis.
Experimental description
The AAF specimen was deformed under confined uniaxial compression at the F2 station of the Cornell High Energy Synchrotron Source (CHESS) with confinement provided by the previously described PEEK tube. Loading was performed using the second generation of the Rotation and Axial Motion System (RAMS2). RAMS2 is a screw-driven uniaxial loading system that allows for 360° of rotation without impeding X-ray measurements as a sample is loaded in-situ53. The compressive load was applied by Inconel718 (nickel-based alloy) platens with a diameter of \(\tfrac{1}{16}^{\prime\prime} \), sized to slide through the PEEK tubing without friction (c.f. Fig. 2a). X-ray data was collected prior to loading and at six intermittent load steps as the sample was compressed. At each load step, a peak load was applied and then the sample was allowed to relax while holding the compression platens in position. Once the load had stabilized, X-ray measurements were performed.
A schematic of the experimental geometry is given in Fig. 2. In the given geometry, the incoming X-ray beam travels in the −z direction, while the sample is loaded and rotated during measurement along the y axis. For the X-ray measurements, the sample was illuminated by a 41.991 keV (λ = 0.296 Å) X-ray box beam that was 1.1 mm tall and 2.5 mm wide. In order to probe the entire volume of the specimen, three separate measurements were performed at heights spaced 1 mm apart in the specimen (providing 50 μm of overlap between layers). For each of the three volumes and at each of the load increments, the sample was rotated 180° to obtain transmission radiographs (Fig. 2b). The radiographs were obtained at 0.1° rotation increments (totaling 1800 radiographs), using a Retiga 4000DC camera coupled to a LuAG:Ce scintillator with a 5× lens (1.48 μm effective pixel pitch) placed 6 mm from the sample. An example radiograph is shown in the inset of Fig. 2b. The scintillator was then moved out of the path and the sample was rotated 360°, capturing diffraction patterns (Fig. 2c) at 0.25° rotational increments (totaling 1440 patterns) using two Dexela 2923 detectors (74.8 μm effective pixel pitch, 3888 × 3072 pixels) that were positioned 734 mm away from the sample. The detector distance and the mounted angle with respect to the sample location were calibrated using CeO2 standard reference material, followed by a pre-calibrated multiruby crystal with known parameters. A magnified view of part of the diffraction image obtained for the AAF specimen is presented in the inset of Fig. 2c, showing a diffuse diffraction ring with regions of intense, isolated diffraction peaks.
Data processing
3-D tomographic reconstructions were generated from the raw radiographs using custom Python scripts based on a GPU implementation of the Simultaneous Iterative Reconstruction Technique (SIRT) algorithm within the ASTRA-toolbox 1.8.354,55 through TomoPY 1.1.256. The spacial resolution of the μCT reconstructions are in the order of 1.45 μm. The centroids, orientations, and elastic strain tensors within crystals of different phases were found from the diffraction data using the HEXRD software package 5.2657. The ff-HEDM processing algorithm consists of ‘indexing’ and fitting routines. Indexing is the process of associating individual diffraction peaks with crystals in the illuminated volume. First, for a given crystal type and lattice orientation, the positions and angles at which diffraction peaks will appear are simulated. If a prescribed set of these peaks are found in the measured experimental data (quantified in the output as ‘completeness’), the measured diffraction peaks are then associated with a crystal now determined to be in the illuminated volume. The process is repeated for a discrete set of possible lattice orientations for each crystal type of interest to index as many crystals present as possible. Once diffraction peaks have been associated with crystals present, an optimization procedure is used to refine the lattice orientation, centroid, and elastic strain tensor εE. This procedure is repeated at each load step to monitor the evolution of elastic strain state of the indexed crystals. For measurements performed at the F2 beamline, experimental uncertainties in elastic strain tensor components are ~10−4 and 0.05° for lattice orientations58. More complete details of the solution algorithm can be found in57.
The assembling of data (both μCT and ff-HEDM) from different volumes along the sample height and the registration of data from different measurements were performed using custom scripts developed in Python. The registration of different data types was performed by matching centroids of crystals found using the ff-HEDM method with the nearest crystals found in the tomographic reconstruction.
Results
Macroscopic response and tomographic reconstructions
The macroscopic mechanical response at each load step where X-ray measurements were performed is plotted in Fig. 3 as the macroscopic compressive load vs total displacement. The crosshead was held fixed after each load increment throughout the duration of the X-ray measurements. After each load increment, the stress in the sample relaxed, so both the maximum load applied and the load after relaxation (‘Measurement Load’) are plotted in Fig. 3.
Tomographic reconstructions generated from the raw radiographs at each load step are shown in Fig. 4a for the entire sample volume. In-situ tomographic reconstructions provide valuable information regarding the microstructural neighborhood, influencing the measured micromechanical loading in the crystalline phases. The grey scale values of the reconstruction are proportional to the local density and, as such, are useful for identifying various phases. Also, with the high spatial resolution (≈2 μm), a much clearer understanding of the shape and motions of phases and voids/cracks can be attained. Evolution of micromechanical loads in crystalline phases measured using ff-HEDM while monitoring void collapse and crack growth may be of particular value in the future for predicting mechanical response.
In Fig. 4, a cylindrical mask was applied to the tomographic reconstruction to remove the PEEK tube from visibility. The sample height is shown to decrease with increasing applied load, as expected. This significant decrease is shown to be accompanied by lateral bulging of the specimen at later load steps, Fig. 4b, and the collapse of the largest voids in the sample, Fig. 4c. In the μCT measurements, the various intensities in the gray scale of the images are related to the material density (related to composition) at each pixel, where the darkest regions correspond to voids and the brightest regions correspond to the densest phase. The box in Fig. 4c (of a region near the top surface in Fig. 4b) highlights the tracking of a specific void which begins to collapse at Load 3 and is no longer present at the later load steps. The circle in 4c shows the ability to track a particle and obtain it’s new position at each applied load. Cracks large enough to be identified with the available resolution were not observed during loading.
Micromechanical response of crystalline phases
While numerous crystalline phases were present in the specimen, isolated diffraction peaks from two of the phases were analyzed using the ff-HEDM technique. An example of these distinct diffraction peaks is shown in the inset of Fig. 2c. The first crystalline phase identified was cubic iron oxide with an average lattice parameter a0 of 8.387 Å. The second crystalline phase was trigonal α-quartz with average lattice parameters a0 and c0 of 4.914 Å and 5.406 Å respectively. The ff-HEDM method was used to determine crystal orientation, centroid, and elastic strain state from the diffraction data obtained at each of the load steps.
At Load 0, ~250 cubic iron oxide crystals and ~80 α-quartz crystals were identified (indexed) and crystal parameters found with high confidence. For this material, high confidence consists of finding more than 90% of predicted diffraction peaks in the diffraction data and optimizing crystal parameters that maintain a solution consistency (related to Pearson’s \({\chi }^{2}\) test statistic) of less than 0.05 with the measured diffraction peak positions.
Combined spatial and micromechanical response of cubic iron oxide
Based on the centroids obtained from ff-HEDM, a few of the cubic iron oxide crystals were identified and isolated from the 3-D μCT reconstructions and registered with the corresponding elastic strain data measured using ff-HEDM. The cubic iron oxide particles were easily isolated from the surrounding matrix due to the good visual contract between the particles and the matrix. Such isolation was challenging for the α-quartz crystals due to similarities in density (and related pixel value in the reconstruction) with the surrounding matrix. Isolated tomographic reconstruction of the cubic iron oxide particles at Loads 0, 3, and 6 are shown in Fig. 5a. These reconstructions show the motion of these particles with increasing compressive load. These motions can also be viewed in the dotted paths of Fig. 5b. The bottom half of the specimen shows significantly smaller displacements in comparison to particles in the upper half of the sample because the bottom platen remains stationary during testing. The translation of these particles with increasing load can be ascribed to the total strain of the material (both elastic and plastic strain). The ff-HEDM strain tensor measurement registered to these particles, on the other hand, provides only a measure of the elastic strain response. The insets of Fig. 5b colors the particles according to the compressive elastic strain component along the loading direction \({\varepsilon }_{yy}^{E}\) measured using ff-HEDM. This strain component is shown to increase in magnitude for each of the example particles as a function of load step. The combination of the two measurement types provides a more complete picture of the micromechanical response: total particle motion from μCT provides information about the total strain state and ff-HEDM provides the elastic strain information.
Elastic mechanical response of cubic iron oxide and α-quartz
Before comparing the elastic mechanical response of the two indexed crystalline phases, it is important to note that while this paper presents only the normal components of the strain tensor for analysis, all six components of the elastic strain tensor (and by extension elastic stress tensor) were calculated using the ff-HEDM technique. Figure 6 shows the elastic strain component in the loading direction, \({\varepsilon }_{yy}^{E}\), as a function of position along loading direction at Loads 0, 3, and 6 for (a) cubic iron oxide and (b) α–quartz crystals. At Load 0, in the case of the cubic iron oxide phase, there is a large distribution in the strain \({\varepsilon }_{yy}^{E}\) values (−2 × 10−3 to 4 × 10−3), much greater than the per component uncertainty of ~10−4 which has been previously determined for this technique58. This large variation in strain across the cubic iron oxide crystals can be attributed to variation in lattice parameter (calculated to be in the range of 8.344–8.404 Å) due to substitution of Fe atoms by Ca, Al, Mg, Mn or Ti during coal combustion47,59 and possible local variations of shrinkage stresses. Comparing elastic strains in the loading direction at various load steps, it can be seen that on average the compressive elastic strains in both phases increased as the macroscopic load applied to the specimen was increased (refer to lines plotted across Fig. 6). It should be noted that with the ff-HEDM analysis method used, more than half of the α-quartz crystals initially indexed with high confidence could not be tracked at Load 6, likely due to the beginning of crystal fracture which will be discussed later. To compare average elastic strain behavior across the two phases, the change (Δ) in the average strains for the three normal strain components \({\varepsilon }_{xx}^{E}\), \({\varepsilon }_{yy}^{E}\), and \({\varepsilon }_{zz}^{E}\) are shown in Fig. 7a. To calculate these values, the strain components from each identified crystal in the sample frame are averaged. The change in this average value from Load 0 are then determined. For \(\Delta {\varepsilon }_{yy}^{E}\), the values within the α-quartz were generally larger than the cubic iron oxide until Load 6. The \(\Delta {\varepsilon }_{xx}^{E}\) and \(\Delta {\varepsilon }_{zz}^{E}\) values within each phase are generally similar as expected from the symmetry of the loading and the specimen. The primary difference occurs in the components transverse to the loading direction, wherein the α-quartz is generally contracting (positive change in elastic strain), while the cubic iron oxide is expanding (negative change in elastic strain). This is possibly due to the interactions of these crystals with the matrix and the confinement provided by the PEEK tube leading to non-uniaxial loading conditions. Based on current findings from the tomographic reconstructions and micromechanical data, sample designs that provide less constraint are being considered for future experiments.
In order to examine the differences in load transmitted through the two phases, the anisotropic form of Hooke’s Law
where σ is stress and \({\mathbb{C}}\) is the fourth order stiffness tensor, was used to calculate stresses from the elastic strain tensors of the crystals. Since the lattices within the crystals can be oriented in any direction with respect to the loading axis, determination of stress in each crystal was simplified by performing the calculation in a frame fixed to the lattice basis vectors of each crystal (crystal frame). The process for calculating the average change in stress was to use the elastic strains in the crystal frame, evaluate Hooke’s law to determine the current grain stress, transform the stresses back to the sample frame, and lastly, average the stress tensor components from all high confidence crystals. Changes in the average stress are calculated from Load 0. The single crystal moduli for the cubic iron oxide used60 were (in GPa): \({C}_{11}=260.5\), \({C}_{12}=148.3\), and \({C}_{44}=63.3\), while the α-quartz moduli used61 were: \({C}_{11}=87.2\), \({C}_{12}=6.6\), \({C}_{13}=11.9\), \({C}_{14}=-\,17.2\), \({C}_{33}=105.8\), \({C}_{44}=57.2\), and \({C}_{66}=40.4\). The average changes in stress with increasing macroscopic strain can be seen in Fig. 7b. The macroscopic engineering stress calculated from applied load is also shown in Fig. 7b for a general reference of the applied stress magnitude.
The change in average stresses in the two phases along the loading direction are of the same order of magnitude as the applied macroscopic engineering stress. Although it should be made clear that there are many more constitutive phases in the bulk that support the applied load, the crystal stresses calculated are found to be reasonable for the system. Due to the sample being confined in the PEEK tube, the stresses in the two phases are generally not uniaxial and are compressive for all normal stress components. From the changes in stress in Fig. 7b, it can be seen that the increase in stresses in the cubic iron oxide phase along the loading direction are larger than the α-quartz phase. The increase in transverse stresses in the cubic iron oxide phases are also larger than in the α-quartz phase. We also see that there appears to be an inflection to higher load in Δσyy in the cubic iron oxide phase and an inflection to lower load in the α-quartz phase, while noting that many α-quartz crystals could no longer be tracked at Load 6.
Discussion
In this work, the micromechanical response of the alternative cementitious material, alkali-activated fly ash, was quantified in-situ using both imaging (μCT) and spatially resolved diffraction (ff-HEDM) techniques. ff-HEDM provided the ability to locally quantify the elastic strain, and by extension calculate the stress, in crystalline particles spread throughout the sample, while μCT provided information about the rigid displacement of these crystals through the matrix due to plastic deformation.
The iron oxide and α-quartz crystals are a natural component of the AAF studied here (rather than an additional material added solely as a probe) and play a role in the micromechanical response of the AAF. While the stresses determined from ff-HEDM data are the average from within these crystals, it is important to remember that the stress state is dictated not only by the local elastic properties (stiffness of crystal), but also the local boundary conditions governed by the surrounding matrix62: a change to the surrounding matrix will alter the stress state in the crystals. As such, these stresses provide an important window to gaining understanding about phase interactions in the AAF in-situ, and subsequently predicting the micromechanical response. In addition, the interfaces between stiff inclusions and a more compliant surrounding matrix are often found to nucleation points or easy paths for traversal for cracks63, and ultimately drivers for failure.
Using the elastic strain and stress data shown in the results section, some of the spatial heterogeneities and interactions of mechanical response at the μm to mm length scale can be explored. In Fig. 7a, the effect of crystal composition on the mechanical (strain) response can be observed. For most of the test, the changes in strains along the loading direction (\(\Delta {\varepsilon }_{yy}^{E}\)) in the α-quartz were higher than the cubic iron oxide due to α-quartz’s lower stiffness (the inflection at the final load step is likely due to inelastic events in the α-quartz). The translation from elastic strain to stress using Hooke’s law also provides interesting insights into load partitioning. Even with only probing two of the crystalline phases, this study captured distinct mechanical responses, with the α-quartz contracting and the cubic iron oxide phase expanding on average transverse to the loading direction.
The average change in stresses in the crystals also provides complimentary information about load partitioning. While, the average changes in strain in the cubic iron oxide crystals along the loading directions were generally lower than the α-quartz, the average changes in stress (\(\Delta {\sigma }_{yy}^{E}\)) were higher. In the results, it was mentioned that there appears to be a redistribution of stress along the loading direction at Load 6 between the cubic iron oxide and α-quartz phases (an increase and decrease in \(\Delta {\sigma }_{yy}^{E}\)). At the same time, there was a significant decrease in the number of α-quartz crystals that could be tracked using ff-HEDM. A loss of the ability to track crystals in ff-HEDM is usually due to a degradation of diffraction peak quality, namely decreases of intensity and broadening caused by an increase in defect content. The loss of tracking of the α-quartz crystals and the load redistribution are likely related. As the α-quartz crystals begin to develop internal fracture networks, regions within each crystal become misoriented, diffraction peaks broaden, and the crystal loses its ability to support increased load. Similar behavior has been observed during the compression of a loose, granular collection of α-quartz crystals64. As the macroscopic load is still increasing, other constituent phases, such as the cubic iron oxide, must support a relatively larger percentage of the applied load.
For both the crystalline phases, the changes in transverse stresses (\(\Delta {\sigma }_{xx}^{E}\) and \(\Delta {\sigma }_{zz}^{E}\)) were increasingly compressive in load, but the transverse stresses stop increasing in the α-quartz at Load 4. Conversely, the rate of change of transverse stresses in the cubic iron oxide appears to increase from Load 4 onwards. While the average phase response may provide a general overview of how load is partitioned among the different phases, the stress responses of individual crystals is strongly related to the neighboring matrix response. It is important to remember that these crystals were embedded as part of a surrounding matrix that strained significantly more than the relatively hard crystalline phases. The stress and strain responses are not just due to the phase stiffnesses, but rather a combination of crystal stiffness and surrounding matrix. ff-HEDM is providing a means to probe these interactions.
To explore the impact and response of surrounding matrix on individual crystals, the ff-HEDM techniques can, with some effort, be paired with computed tomography techniques. Figure 5 shows an example of isolating a few crystals and tracking their spatial movement, which can be related to an associated total strain. With volumetric image correlations, there is an opportunity to track the total strain of a material by simply tracking all the particles, and voids, as they move through each volume. By pairing this information with the local elastic stress response from a crystal, the response of the surrounding matrix (such as fracture), and reciprocal effects such as void compaction on local stress state, can be directly probed. It is the dynamic response of the crystals and matrix within their neighborhoods that is essential to capturing the impact of spatial heterogeneity on material properties. However, in complex material systems, identifying regions of interest and isolating individual crystals, let alone thousands of crystals of varying phases, and their response has many associated challenges. Adding to this complexity is the limited resolution currently available to automate the identification and isolation of crystals. Smoothing algorithms and robust segmentation schemes that can be implemented on noisy and large data sets need to be developed.
While the initial results for probing micromechanical response in cement pastes are promising, there are difficulties that need to be addressed with regard to processing and interpreting the diffraction data for cementitious materials in comparison to metallic alloy systems for which the ff-HEDM technique was developed. Cement pastes made from portland cement or recycled materials such as the AAF studied here are not only composed of multiple phases but also have significant heterogeneity within the composition of each phase65,66. The ability to measure an absolute lattice strain and the related stress (rather than a change) is intimately tied to knowing the initial local lattice parameters of the individual crystals. The wide spread of initial strains (at Load 0) in Fig. 6 may be an artifact of differences in unstrained lattice parameters. However, we also note that the crystals may indeed have residual strains due to shrinkage during the curing process. Separating the effects of composition difference and true residual strains is a challenge for all diffraction based stress measurements67 and is particularly acute for the study of concrete. Furthermore, the conversion of lattice strains to stresses using Hooke’s law is based on chosen single crystal moduli for a pure phase. Further work is warranted to explore the effect of compositional changes on the single crystal elastic moduli.
The ff-HEDM technique used in this work is only suitable for extracting information from isolated diffraction peaks. For multi-phase samples such as the AAF studied here, scattered X-rays from both amorphous and fine-grained crystalline phases are also detected. It should be highlighted that the scattering from these phases, although not a focus this study, can be analyzed to gain more information about load partitioning, albeit without the ability to locate the position of scattering in the illuminated volume and register the loading data with a tomographic reconstruction. The broad scattering of the amorphous phases can be used to determine correlation lengths between atoms which will expand or contract with applied load68,69. While the fine-grained crystalline phases can be analyzed using strain pole figure methods to study the crystal lattice orientation dependence of load partitioning70,71,72. However, the challenge lies in the ability to deconvolve the overlapping scattering from different phases. New image processing methodologies will need to be developed and adopted before these analyses can be performed simultaneously. Although if made possible, a more complete picture of the micromechanical response of all phases present can be reconstructed and used to inform modeling efforts. Analyzing complex scattering patterns from other cementitious systems, including portland cement, are currently underway.
Summary
To aid the development of micromechanical models of complex cementitious systems, the combination of two high-energy X-ray 3-D characterization techniques has been demonstrated. Far-field high-energy diffraction microscopy measurements provided the ability to probe the partitioning of load within different crystalline phases (cubic iron oxide and α-quartz) present in an alkali activated fly ash specimen, while the combination of μCT and ff-HEDM demonstrated the ability to visualize the local strains and understand their effect on the surrounding matrix. Such information is vital for modeling the deformation of cementitious materials and also to probe the effect of heterogeneity on the micromechanical response.
References
Mahasenan, N., Smith, S. & Humphreys, K. The cement industry and global climate change: Current and potential future cement industry co2 emissions. In Gale, J. & Kaya, Y. (eds.) Greenhouse Gas Control Technologies - 6th International Conference, 995–1000, https://doi.org/10.1016/B978-008044276-1/50157-4 (Pergamon, Oxford, 2003).
Hasanbeigi, A., Price, L. & Lin, E. Emerging energy-efficiency and co2 emission-reduction technologies for cement and concrete production: A technical review. Renew. Sust. Energ. Rev. 16, 6220–6238, https://doi.org/10.1016/j.rser.2012.07.019 (2012).
Provis, J. L. & van Deventer, J. S. J. Alkali Activated Materials: State-of-the-Art Report, RILEM TC 224-AAM. RILEM State-of-the-Art Reports, https://doi.org/10.1007/978-94-007-7672-2 (Springer Netherlands, 2013).
Kurtis, K. E. Innovations in cement-based materials: Addressing sustainability in structural and infrastructure applications. MRS Bulletin 40, 1102–1109, https://doi.org/10.1557/mrs.2015.279 (2015).
Duxson, P. et al. Geopolymer Technology: The Current State of the Art. J. Mater. Sci. 42, 2917–2933, https://doi.org/10.1007/s10853-006-0637-z (2007).
Juenger, M., Winnefeld, F., Provis, J. & Ideker, J. Advances in alternative cementitious binders. Cem. Concr. Res. 41, 1232–1243, https://doi.org/10.1016/j.cemconres.2010.11.012 (2011).
Yang, K.-H., Song, J.-K. & Song, K.-I. Assessment of co2 reduction of alkali-activated concrete. J. Clean. Prod. 39, 265–272, https://doi.org/10.1016/j.jclepro.2012.08.001 (2013).
Uehara, M. New Concrete with Low Environmental Load Using the Geopolymer Method. Q. Rep. RTRI 51, 1–7, https://doi.org/10.2219/rtriqr.51.1 (2010).
Garca-Lodeiro, I., Palomo, A. & Fernández-Jiménez, A. Alkali–aggregate reaction in activated fly ash systems. Cement and Concrete Research 37, 175–183, https://doi.org/10.1016/j.cemconres.2006.11.002 (2007).
Topçu, İ. B., Toprak, M. U. & Uygunoğlu, T. Durability and microstructure characteristics of alkali activated coal bottom ash geopolymer cement. Journal of Cleaner Production 81, 211–217, https://doi.org/10.1016/j.jclepro.2014.06.037 (2014).
Sun, P. & Wu, H.-C. Chemical and freeze–thaw resistance of fly ash-based inorganic mortars. Fuel 111, 740–745, https://doi.org/10.1016/j.fuel.2013.04.070 (2013).
Ismail, I., Bernal, S. A., Provis, J. L., Hamdan, S. & van Deventer, J. S. J. Microstructural changes in alkali activated fly ash/slag geopolymers with sulfate exposure. Materials and Structures 46, 361–373, https://doi.org/10.1617/s11527-012-9906-2 (2013).
Bakharev, T. Geopolymeric Materials Prepared using Class F Fly Ash and Elevated Temperature Curing. Cem. Concr. Res. 35, 1224–1232, https://doi.org/10.1016/j.cemconres.2004.06.031 (2005).
Miranda, J., Fernández-Jiménez, A., González, J. & Palomo, A. Corrosion resistance in activated fly ash mortars. Cement and Concrete Research 35, 1210–1217, https://doi.org/10.1016/j.cemconres.2004.07.030 (2005).
Olvera, R., Panchmatia, P., Juenger, M., Aldin, M. & van Oort, E. Long-term oil well zonal isolation control using geopolymers: An analysis of shrinkage behavior. In SPE/IADC International Drilling Conference and Exhibition, https://doi.org/10.2118/194092-MS (The Hague, The Netherlands, 2019).
Criado, M., Palomo, A. & Fernández-Jiménez, A. Alkali activation of fly ashes. part 1: Effect of curing conditions on the carbonation of the reaction products. Fuel 84, 2048–2054, https://doi.org/10.1016/j.fuel.2005.03.030 (2005).
Bernal, S. A. & Provis, J. L. Durability of alkali-activated materials: Progress and perspectives. Journal of the American Ceramic Society 97, 997–1008, https://doi.org/10.1111/jace.12831 (2014).
Shi, C. & Fernández-Jiménez, A. Stabilization/solidification of hazardous and radioactive wastes with alkali-activated cements. J. Hazard. Mater. 137, 1656–1663, https://doi.org/10.1016/j.jhazmat.2006.05.008 (2006).
Liu, X., Nair, S., Aughenbaugh, K. & van Oort, E. Mud-to-cement conversion of non-aqueous drilling fluids using alkali-activated fly ash. Journal of Petroleum Science and Engineering 182, 106242 (2019).
Bell, J., Gordon, M. & Kriven, W. Use of Geopolymeric Cements as a Refractory Adhesive for Metal and Ceramic Joins. In Zhu, D. & Plucknett, K. (eds) Advances in Ceramic Coatings and Ceramic-Metal Systems: Ceramic Engineering and Science Proceedings, 407–413, https://doi.org/10.1002/9780470291238.ch46 (John Wiley & Sons, Inc., 2005).
Jennings, H. M. et al. Modelling and Materials Science of Cement-Based Materials Part I: An Overview, 29–62, https://doi.org/10.1007/978-94-015-8646-7_2 (Springer Netherlands, Dordrecht, 1996).
Sanchez, F. & Sobolev, K. Nanotechnology in concrete– a review. Const. Build. Mater. 24, 2060–2071, https://doi.org/10.1016/j.conbuildmat.2010.03.014 (2010).
Zhang, M. & Jivkov, A. P. Microstructure-informed modelling of damage evolution in cement paste. Const. Build. Mater. 66, 731–742, https://doi.org/10.1016/j.conbuildmat.2014.06.017 (2014).
Bullard, J. W. et al. Measurement and modeling needs for microstructure and reactivity of next-generation concrete binders. Cem. Concr. Comp. 101, 24–31, https://doi.org/10.1016/j.cemconcomp.2017.06.012, Grand Challenges in Construction Materials 2016 (2019).
Snoeck, D., Pel, L. & De Belie, N. The water kinetics of superabsorbent polymers during cement hydration and internal curing visualized and studied by nmr. Scientific Reports 7, 9514, https://doi.org/10.1038/s41598-017-10306-0 (2017).
Mondal, P., Shah, S. P. & Marks, L. A reliable technique to determine the local mechanical properties at the nanoscale for cementitious materials. Cem. Concr. Res. 37, 1440–1444, https://doi.org/10.1016/j.cemconres.2007.07.001 (2007).
Mondal, P., Shah, S. P. & Marks, L. Nanoscale characterization of cementitious materials. ACI Mater. J. 105, 174–179, https://doi.org/10.14359/19758 (2008).
Thomas, R., Gebregziabiher, B. S., Giffin, A. & Peethamparan, S. Micromechanical properties of alkali-activated slag cement binders. Cem. Concr. Compos. 90, 241–256, https://doi.org/10.1016/j.cemconcomp.2018.04.003 (2018).
Landis, E. N. & Keane, D. T. X-ray microtomography. Mater. Charact. 61, 1305–1316, https://doi.org/10.1016/j.matchar.2010.09.012 (2010).
Yang, Z. et al. In-situ x-ray computed tomography characterisation of 3d fracture evolution and image-based numerical homogenisation of concrete. Cem. Concr. Compos. 75, 74–83, https://doi.org/10.1016/j.cemconcomp.2016.10.001 (2017).
Wong, R. & Chau, K. Estimation of air void and aggregate spatial distributions in concrete under uniaxial compression using computer tomography scanning. Cem. Concr. Res. 35, 1566–1576, https://doi.org/10.1016/j.cemconres.2004.08.016 (2005).
Landis, E. N., Nagy, E. N. & Keane, D. T. Microstructure and fracture in three dimensions. Eng. Fract. Mech. 70, 911–925, https://doi.org/10.1016/S0013-7944(02)00157-1 (2003).
Lawler, J., Keane, D. T. & Shah, S. P. Measuring three-dimensional damage in concrete under compression. Mater. J. 98, 465–475, https://doi.org/10.14359/10847 (2001).
Dong, B. et al. Monitoring reinforcement corrosion and corrosion-induced cracking by x-ray microcomputed tomography method. Cem. Concr. Res. 100, 311–321, https://doi.org/10.1016/j.cemconres.2017.07.009 (2017).
Yang, S., Cui, H. & Poon, C. S. Assessment of in-situ alkali-silica reaction (asr) development of glass aggregate concrete prepared with dry-mix and conventional wet-mix methods by x-ray computed micro-tomography. Cem. Concr. Compos. 90, 266–276, https://doi.org/10.1016/j.cemconcomp.2018.03.027 (2018).
Marinoni, N. et al. An investigation of mortars affected by alkali-silica reaction by x-ray synchrotron microtomography: a preliminary study. J. Mater. Sci. 44, 5815–5823, https://doi.org/10.1007/s10853-009-3817-9 (2009).
Bentz, D. et al. X-ray microtomography of an astm c109 mortar exposed to sulfate attack. Mater. Res. Soc. Symp. Proc. 370, 77, https://doi.org/10.1557/PROC-370-77 (1994).
Stock, S., Naik, N., Wilkinson, A. & Kurtis, K. X-ray microtomography (microct) of the progression of sulfate attack of cement paste. Cem. Concr. Res. 32, 1673–1675, https://doi.org/10.1016/S0008-8846(02)00814-1 (2002).
Snoeck, D., Dewanckele, J., Cnudde, V. & Belie, N. D. X-ray computed microtomography to study autogenous healing of cementitious materials promoted by superabsorbent polymers. Cement and Concrete Composites 65, 83–93, https://doi.org/10.1016/j.cemconcomp.2015.10.016 (2016).
Burlion, N., Bernard, D. & Chen, D. X-ray microtomography: Application to microstructure analysis of a cementitious material during leaching process. Cem. Concr. Res. 36, 346–357, https://doi.org/10.1016/j.cemconres.2005.04.008 (2006).
Shields, Y., Garboczi, E., Weiss, J. & Farnam, Y. Freeze-thaw crack determination in cementitious materials using 3d x-ray computed tomography and acoustic emission. Cem. Concr. Compos. 89, 120–129, https://doi.org/10.1016/j.cemconcomp.2018.03.004 (2018).
Barnes, P. et al. Time- and Space-Resolved Dynamic Studies on Ceramic and Cementitious Materials. J. Synchrotron Radiat. 7, 167–177, https://doi.org/10.1107/S0909049500003137 (2000).
Provis, J. L. & van Deventer, J. S. Geopolymerisation kinetics. 1. In situ energy-dispersive x-ray diffractometry. Chem. Eng. Sci. 62, 2309–2317, https://doi.org/10.1016/j.ces.2007.01.027 (2007).
Jupe, A. C., Wilkinson, A. P., Luke, K. & Funkhouser, G. P. Slurry consistency and in situ synchrotron x-ray diffraction during the early hydration of portland cements with calcium chloride. J. Am. Ceram. Soc. 90, 2595–2602, https://doi.org/10.1111/j.1551-2916.2007.01806.x (2007).
Snellings, R., Mertens, G., Cizer, ö & Elsen, J. Early age hydration and pozzolanic reaction in natural zeolite blended cements: Reaction kinetics and products by in situ synchrotron x-ray powder diffraction. Cem. Concr. Res. 40, 1704–1713, https://doi.org/10.1016/j.cemconres.2010.08.012 (2010).
Aranda, M. A. Recent studies of cements and concretes by synchrotron radiation crystallographic and cognate methods. Crystallogr. Rev. 22, 150–196, https://doi.org/10.1080/0889311X.2015.1070260 (2016).
Williams, R. P. & van Riessen, A. The First 20 Hours of Geopolymerization: An in Situ WAXS Study of Flyash-Based Geopolymers. Mater. 9, 552, https://doi.org/10.3390/ma9070552 (2016).
Moradian, M. et al. Direct observation of void evolution during cement hydration. Mater. Des. 136, 137–149, https://doi.org/10.1016/j.matdes.2017.09.056 (2017).
Hurley, R. & Pagan, D. An in-situ study of stress evolution and fracture growth during compression of concrete. Int. J. Solids. Struct., https://doi.org/10.1016/j.ijsolstr.2019.03.015 (2019).
ASTM-International. C618-19 standard Specification for Coal Fly Ash and Raw or Calcined Natural Pozzolan for Use in Concrete. Tech. Rep., West Conshohocken, PA, https://doi.org/10.1520/C0618-19 (2019).
ASTM-International. C1738/c1738m-19 standard Practice for High-Shear Mixing of Hydraulic Cement Pastes. Tech. Rep., West Conshohocken, PA, https://doi.org/10.1520/C1738_C1738M-19 (2019).
Liu, X. et al. True self-healing geopolymer cements for improved zonal isolation and well abandonment. In SPE/IADC Drilling Conference and Exhibition, https://doi.org/10.2118/184675-MS (2017).
Shade, P. A. et al. A rotational and axial motion system load frame insert for in situ high energy x-ray studies. Rev. Sci. Instrum. 86, 093902, https://doi.org/10.1063/1.4927855 (2015).
Pelt, D. et al. Integration of tomopy and the astra toolbox for advanced processing and reconstruction of tomographic synchrotron data. J. Synchrotron Radiat. 23, 842–849, https://doi.org/10.1107/S1600577516005658/pp5084sup1.txt (2016).
van Aarle, W. et al. Fast and flexible x-ray tomography using the astra toolbox. Opt. Express 24, 25129–25147, https://doi.org/10.1364/OE.24.025129 (2016).
Gürsoy, D., De Carlo, F., Xiao, X. & Jacobsen, C. Tomopy: a framework for the analysis of synchrotron tomographic data. J. Synchrotron Radiat. 21, 1188–1193, https://doi.org/10.1107/S1600577514013939 (2014).
Bernier, J. V., Barton, N. R., Lienert, U. & Miller, M. P. Far-field high-energy diffraction microscopy: a tool for intergranular orientation and strain analysistation and strain analysis. J. Strain Anal. Eng. 46, 527–547, https://doi.org/10.1177/0309324711405761 (2011).
Hurley, R. C., Herbold, E. B. & Pagan, D. C. Characterization of the Crystal Structure, Kinematics, Stresses and Rotations in Angular Granular Quartz During Compaction. J. Appl. Crystallogr. 51, 1021–1034, https://doi.org/10.1107/S1600576718006957 (2018).
Sokol, E. et al. Ferrospheres from fly ashes of chelyabinsk coals: Chemical composition, morphology and formation conditions. Fuel 81, 867–876, https://doi.org/10.1016/S0016-2361(02)00005-4 (2002).
Reichmann, H. J. & Jacobsen, S. D. High-pressure elasticity of a natural magnetite crystal. Am. Mineral. 89, 1061–1066, https://doi.org/10.2138/am-2004-0718 (2004).
Heyliger, P., Ledbetter, H. & Kim, S. Elastic constants of natural quartz. J. Acoust. Soc. Am. 114, 644–650, https://doi.org/10.1121/1.1593063 (2003).
Mori, T. & Tanaka, K. Average stress in matrix and average elastic energy of materials with misfitting inclusions. Acta Metallurgica 21, 571–574, https://doi.org/10.1016/0001-6160(73)90064-3 (1973).
Scrivener, K. L., Crumbie, A. K. & Laugesen, P. The interfacial transition zone (itz) between cement paste and aggregate in concrete. Interface Science 12, 411–421, https://doi.org/10.1023/B:INTS.0000042339.92990.4c (2004).
Hurley, R., Lind, J., Pagan, D., Akin, M. & Herbold, E. In situ grain fracture mechanics during uniaxial compaction of granular solids. J. MEch. Phys. Solids 112, 273–290, https://doi.org/10.1016/j.jmps.2017.12.007 (2018).
Lee, W. & van Deventer, J. Use of infrared spectroscopy to study geopolymerization of heterogeneous amorphous aluminosilicates. Langmuir 19, 8726–8734, https://doi.org/10.1021/la026127e (2003).
Favier, A., Habert, G., d’Espinose de Lacaillerie, J. & Roussel, N. Mechanical properties and compositional heterogeneities of fresh geopolymer pastes. Cem. Concr. Res. 48, 9–16, https://doi.org/10.1016/j.cemconres.2013.02.001 (2013).
Klaus, M. & Genzel, C. Nondestructive separation of residual stress and composition gradients in thin films by angle- and energy-dispersive X-ray diffraction. I. Theoretical concepts. J. Appl. Crystallogr. 50, 252–264, https://doi.org/10.1107/S1600576716020598 (2017).
Poulsen, H. F., Wert, J. A., Neuefeind, J., Honkimäki, V. & Daymond, M. Measuring strain distributions in amorphous materials. Nat. Mater. 4, 33, https://doi.org/10.1038/nmat1266 (2005).
Ice, G. Amorphous materials: Characterizing amorphous strain. Nat. Mater. 4, 17, https://doi.org/10.1038/nmat1302 (2005).
Behnken, H. Strain-function method for the direct evaluation of intergranular strains and stresses. Physica Status Solidi A 177, 401–418, https://doi.org/10.1002/(SICI)1521-396X(200002)177:2<401::AID-PSSA401>3.0.CO;2-I (2000).
Miller, M. P., Bernier, J. V., Park, J.-S. & Kazimirov, A. Experimental measurement of lattice strain pole figures using synchrotron x rays. Rev. Sci. Instrum. 76, 113903, https://doi.org/10.1063/1.2130668 (2005).
Bernier, J., Park, J., Pilchak, A., Glavicic, M. & Miller, M. Measuring stress distributions in ti-6al-4v using synchrotron x-ray diffraction. Metall. Mater. Trans. A 39, 3120–3133, https://doi.org/10.1007/s11661-008-9639-6 (2008).
Kitware, Sandia, LANL, ARL & CSinSoft. Paraview 5.5, https://www.paraview.org.
Acknowledgements
This work is based upon research conducted at the Cornell High Energy Synchrotron Source (CHESS) which is supported by the National Science Foundation under award DMR-1332208. The authors would like to thank the SEFA Group for providing the fly ash used in this study and staff scientist Peter Ko for his help during beamtime at CHESS.
Author information
Authors and Affiliations
Contributions
All authors conceived the experiment, conducted the experiment and reviewed the manuscript. S.D.N. and D.C.P. processed the data and analyzed it. S.D.N. prepared all figures and K.E.N. helped with Figures 2, 4 and 5.
Corresponding author
Ethics declarations
Competing interests
The authors declare no competing interests.
Additional information
Publisher’s note Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.
Rights and permissions
Open Access This article is licensed under a Creative Commons Attribution 4.0 International License, which permits use, sharing, adaptation, distribution and reproduction in any medium or format, as long as you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons license, and indicate if changes were made. The images or other third party material in this article are included in the article’s Creative Commons license, unless indicated otherwise in a credit line to the material. If material is not included in the article’s Creative Commons license and your intended use is not permitted by statutory regulation or exceeds the permitted use, you will need to obtain permission directly from the copyright holder. To view a copy of this license, visit http://creativecommons.org/licenses/by/4.0/.
About this article
Cite this article
Nair, S.D., Nygren, K.E. & Pagan, D.C. Micromechanical Response of Crystalline Phases in Alternate Cementitious Materials using 3-Dimensional X-ray Techniques. Sci Rep 9, 18456 (2019). https://doi.org/10.1038/s41598-019-54724-8
Received:
Accepted:
Published:
DOI: https://doi.org/10.1038/s41598-019-54724-8
- Springer Nature Limited