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The Impact of Extended Heat Exposure on Rapid Sulphoaluminate Cement Concrete Up To 120°C

This study examined the stability of rapid sulphoaluminate cement concrete (R-SACC) when exposed to heat for extended periods of time. The physicochemical processes present in R-SACC as a function of temperature were determined through various tests. The general behavior of rapid sulphoaluminate cement (R-SAC) at a range of temperatures is summarized. The results show that observing color change could be a simple way to identify deterioration of R-SACC, along with the rebound hammer. The matrix formation of ettringite was broken and the mass of the hydrated product decreased with heat exposure; the major mineral composition of the paste consisted of CaSO4, CaCO3 and β-C2S; and the interface between aggregate and paste in the R-SACC become loosely structured with cracks. Between 50°C and 120°C, the rapid sulphoaluminate cement (R-SAC) paste first expanded and then shrank, and the shrinkage rate of R-SAC was much greater than that of R-SACC.


Introduction
Rapid sulphoaluminate cement concrete (R-SACC) is widely used as an important structural material. China and other countries, such as India, have used billions of tons of R-SACC in construction due to its several advantages, such as high early strength, short setting time, good corrosion, freeze-thaw resistance, and low production cost, which give it the prospect of reaching a broad market. Concrete structural members, when used in construction, must meet fire safety specification specified in construction codes [1,2]. This is because fire represents one of the most severe environmental threats to which R-SACC may be subjected. Therefore, the planning of appropriate fire safety measures for structural components is a foremost aspect of ensuring building stability. Numerous issues related to R-SACC structures are becoming important factors in many industries. These include the risk of structural collapse when heated to a certain extent, property deterioration caused by aggressive environmental impacts, and premature strength. By 2050, the use of concrete overall is forecasted to reach four times the amount in 1990 [3]. Therefore, rapid sulphoaluminate cement (R-SAC) is getting increased attention since its manufacture produces less CO 2 than that of Portland cement [4]. This cement may have quite changeable composition, but all forms of it have a Ye'elimite phase, also called tetracalcium trialuminate sulfate (C4A3S), as the main phase [5]. It may also have a minor phase such as C 2 S, CA, C 4 AF, CS, C S H 2 [6], where C is used to represent CaO, S represents SiO 2 , A represents Al 2 O 3 , F represents Fe 2 O 3 , S represents SO 3 , M represents MgO, T represents TiO 2 and H represents H 2 O. The paste and concretes obtained from this cement show high early strength development [7] and could also be utilized for radioactive component encapsulation [8]. Ettringite is one of the most important elements giving early strength to R-SAC, it constitutes one of the principal components of the structural matrix formed by hardened R-SAC. Caporale et al. [9] and Zhou [10] has shown that its dehydration at 50°C to 65°C entails a rapid loss of water; this temperature range represents the zone of ettringite persistence. The post-decomposition at 95°C registers more loss of water by the AFt followed by a complete decomposition at 120°C. Its decomposition is a mixture of gypsum and amorphous material as a dehydrated product.Hence, the temperature range at which we can study our sample is 50°C to 120°C.
R-SACC is frequently used to build power plants in China and India that could possibly put millions of people in danger, so it is essential for engineers to find ways to rapidly monitor the extent of deterioration in existing buildings. Therefore, it is important to address the potential negative effect that dehydration at this range of temperatures could have on the cement's strength. In the best-known papers describing the effect of heat damage on the properties of cements, concretes, and aggregates generally [11,12], no mention is made of changes in other important physical and mechanical characteristics of concretes and their components as a result of exposure to the surrounding heat. When a building structure experiences elevated temperatures for an extended period of time, concrete is prone to cracking. The high density of the R-SAC and the aggregate thermal expansion coefficient could be important factors affecting the structures. They are bound to increase the thermal stress inside the heated structure, making it more crackable. When cracks occur in concrete, its thermal resistance is significantly reduced. Studies by Damidot and Glasser [13], Sanfelix et al. [14] and Collier [15] pointed out that when a 0.4 cm crack occurs in a 20 cm-thick concrete structure, its thermal protection performance drops to less than 10 % of the original. Therefore, concrete should have good thermal stability to ensure its load-bearing ability. The temperature at some structures, such as power plants, under normal operating conditions can be as high as 120°C [16][17][18][19]. The objective of this limited study was to provide data and information on the effects of elevated temperatures between 50° and 120°C on the mechanical behavior of the R-SAC-based materials for use in assessments of power plant concrete structures that are subjected to temperatures in excess of the current Chinese Society of Mechanical Engineers Code limitations. In this study, the compressive, flexural and tensile strength of R-SACC after exposure to temperatures of 50° to 120°C was tested. In addition, we have proposed and texted two methods for quick identification thermally induced deterioration in R-SACC, particularly the rebound hammer and colorimeter. Finally, the thermal decomposition, and microstructure were studied by using an X-ray diffraction instrument and SEM/EDS tools.

Experimental program
The experiments aimed to determine the change of strength of R-SACC in the zone of ettringite persistence, where the ettringite matrix remains in high concentration even though there is ongoing dehydration, and in the zone of ettringite decomposition, where the loss of water by the AFt is more obvious at temperatures up to 120°C, as illustrated in Fig. 1. The specific exposure temperatures were chosen based on expected critical chemical and micro-structural behavior changes and to represent the range of low-temperature exposures common to buildings.

Significance of the study
Results from this study can complement previous research in helping to predict the degree of decay that a structure or structural element made with R-SAC could face. This aspect is of great importance for designing the reconstruction, reinforcement or retrofitting of such a structure or structural element. Gaining a more precise understanding of the failure mechanisms of R-SACC could help us increase fire resistance in buildings in which it is used.

Heat
In large concrete masses, such as dams, and in other facilities, heat dissipates very slowly, so the whole structure experiences a rise in temperature. This rise in turn causes volume expansion of the concrete. Eventually, the temperature rise reaches a maximum and then the structure begins to cool slowly. With subsequent cooling, the material begins to contract. As the material heats and cools repeatedly, it expands and contracts, and cracking can result.

Mix proportions and materials
The concrete grade C40 was adopted in this work, corresponding to a nominal strength of 72.1 MPa. For the experimental R-SACC mix, the fine aggregate was medium sand from the Yangtze River, with a fineness modulus of 2.5 and apparent density of 2584 kg/m 3 . The coarse aggregate was  (Table 1). R-SAC P.O 42.5 grade cement (Table 2) from Wuhan Yadong Yangfang Cement Group Co., Ltd. was used. It has a specific surface area of 348 m 2 /kg with a water absorption rate of 0.83 %. The proportions of concrete are given in Table 3. Preliminary tests (specific gravity, sieve analysis) were performed on the aggregates (river sand and crushed granite) in accordance with Bs 812, and workability tests were performed on the fresh concrete to determine their suitability.

Sample preparation
R-SACC mixing took place with the aid of a mixer; the concrete was prepared according to the mixing ratio shown in Table 3. A sample size of 40 × 40 × 150 mm (15 samples) was adopted for tests of the flexural strength, tensile strength, mass changes, ultrasonic waves, and shrinkage; then a sample size of 100 × 100 × 100 mm (15 samples) was used to perform the rebound hammer number non-destructive test, along with tests of compressive strength, stressstrain, mass loss and Poisson ratio for each temperature. In addition, 20 mm cubic specimens (15 samples) were produced to represent R-SAC paste so as to understand the dehydration phase that occurs as temperature increases.

Curing process
Immediately after the samples had been cast and consolidated, they were placed in a concrete chamber of the material testing cure room with a temperature range of +20°C ± 1.5°C for 24 h; after that, they were demolded and stored in a curing chamber at a constant temperature of 20°C and a relative humidity of 95 % for 28 days. Then they were air-dried inside the laboratory for 7 days.

Testing procedure
Prior to any other testing, the width of the cracks in each sample was measured using an intelligent crack width meter [20], the experimental device shown in Fig. 2(c). When the probe was aimed at the crack during the test, the magnified crack image could be seen on the LCD screen. A fine-tune probe made the image clearer and saved it. Then the color images of each sample surface were analyzed, using a method in accordance with recent studies that evaluated the color change in heated concrete [21][22][23][24]. Pictures were taken with a stereomicroscope, with a flatbed at the same scale. The images were then analyzed using the ImageJ analysis software package called Scion Image (version 4.0.3, Scion Corporation © , USA) [25]. This package enabled us to measure the intensity of various component colors in regions of interest (ROIs). After that, the ultrasonic test was conducted; changes in ultrasonic waves can reflect the internal degradation of the concrete structure and predict internal collapse [26][27][28][29]. A Tektronix AFG3022B arbitrary waveform generator and Tektronix TDS1002B-SC provided the source and receiver signals, respectively, as digital oscilloscope in this experiment (Fig. 3). The ultrasonic frequency was 30 kHz and the input voltage was 10V. The transmitting amplitude values and waveform of the ultrasonic waves were recorded. The experimental device is shown in Fig. 2(d). For the ultrasonic test, grease was applied as couplant to enhance adequate contact between the R-SACC and the transducers.
Next, the rebound hammer test was conducted; the surface samples under investigation were systematically smoothed in all cases. During this test, the plunger of the rebound hammer is pressed against the surface of the  R-SACC after being exposed to the target temperature. A spring-controlled mass with constant energy is made to hit the concrete surface; when it rebounds back, the force of the rebound, which is a measure of surface hardness, is measured on a graduated scale. This study included two non-destructive test (NDT) methods that enable certain properties of the R-SACC to be evaluated in situ, from which an estimation of the quality of the concrete was made. Before exposure, the samples of 40 × 40 × 150, 100 × 100 × 100 and 20 × 20 × 20 mm were weighed (M 0 ). Some samples were then reserved and used as controls (20˚C). Then the other samples were subjected to varying temperatures from 50° to 120°C. Previous studies by Tchekwagep et al. [30] have shown that major physico-chemical changes occur between 20° and 120°C, so we selected picked roughly equal increments to cover the range. The temperatures of 20° and 100°C were chosen to match previous studies as "control points"; 50° and 70°C were chosen as intermediate temperatures within the zone of ettringite persistence. Each temperature was maintained for 4 hours, to attain steady state conditions (thermal equilibrium) [31] in the specimens at all target temperatures. The temperature was increased at a rate of 4°C/min inside the electric furnace. After the 4-hr period, the samples were immediately weighed and the distance from the surface was measured (for both the concrete samples and cement samples), then they were left to cool down in the furnace at a rate of 2°C/min to ambient temperature (20°C) and weighed (M i ) with an electronic balance of 0.01 g precision. The control and exposed samples were then tested for strength performance using appropriate machines for each test. Loads were applied to the R-SACC at the rate of 0.5 MPa/s, 0.05 MPa/s and 0.01 MPa/s for the compressive strength, flexural strength and tensile strength tests, respectively, according to the Chinese standard. Each sample of 100 × 100 × 100 mm was equipped on the surface with four strain gauge sensors, two installed vertically and two horizontally (BQ120-80AA-P200) on the surface of each sample, able to record the change in stress-strain in the R-SACC. Before we performed the compressive stressstrain test, moisture in each sample was determined with an electronic meter. Tests were performed and the separate strain deformations were recorded through a linear transformer (DH3821 static strain collector [32,33] (see Fig. 2(a)) to quantify our understanding of the stress-strain relationship and Poisson ratio of the R-SACC after exposure to different elevated temperatures. The residual strength of the sample is the ratio of the strength at temperature Ө°C to that at ambient temperature. A graph of compressive, flexural, tensile and residual strength (Rs) versus temperature was plotted to study the failure mechanism behavior of the R-SACC in the two zones. After that, the XRD/TGA and SEM/EDS of different samples were performed to support the recorded strength and further explain the stability of the structure at each temperature. These were then compared to that of the control sample (20°C). Fig. 4 shows the color change of the external surface of the R-SACC. When heated to a certain temperature, R-SACC changes color. The R-SACC containing limestone aggregates will turn hurricane at approximately 50° to 70°C, rolling stone at about 100°C, and tapa color at 120°C. The color change of heated R-SACC results principally from the water removal and dehydration of the R-SAC paste, but is also caused by the transformations occurring within the aggregate.

Fig. 3 Ultrasonic test schematic diagram
As shown in Fig. 5(a), the mean gray values were found to be generally increasing with the rise in temperature. The most intense color change occurred at 100° and 120°C. Fig. 5(b) presents counts of pixel intensity that increase with temperature as well, and could be a clear indicator of the strength decreasing when exposed to those temperatures. This may be used to evaluate the actual temperature reached by the R-SACC structure when affected by fire. Fig. 6 shows the microscopic images of cracks in four samples at different temperatures. The width of the cracks in the samples heated to 50°C varied between 0.06 and 0.09 mm; at 70°C, it varied between 0.1 and 0.14 mm; at 100°C, it varied between 0.14 and 0.16 mm; and at 120°C, it varied between 0.17 and 0.30 mm. The crack width was found to increase as the temperature increased, consistent with the internal structure observation (Fig. 7), the lower mass changes and the lower strength measurement recorded at higher temperatures. Fig. 8 shows typical ultrasonic waveforms for the control sample at 20°, as well as at 50°, 70°, 100° and 120°C, obtained in the pre-cracking stage and after exposure for 4 hrs. The transmitting times and amplitude values are acquired from the head wave of the ultrasonic waveform. The transmitting times were found to increase and the amplitude values decreased as the temperature increased, as shown in Table 4. This is due to the cracks, which have  The R-SACC samples tested at normal temperature (20°C) had the smallest transmitting time and the largest amplitude value, which indicates that the defects inside those samples tested before heating to different temperatures had a greater homogeneity and compactness. After heating, the peak-to-peak variation of those values was less evident, highlighting the severe effect that exposure to this range of temperatures for an extensive period can have on R-SACC. The waveform change may be caused by the energy attenuation of the ultrasonic wave during the propagation process, which encounters many microcracks. The ultrasonic wave encounters multiple reflections at the concrete interface, leading to the waveform attenuation and causing the non-reflecting waves observed when samples are heated. This result is correlated with the interior and exterior cracks observed on the surface of the samples as the temperature increases.

Rebound hammer number (RHN)
The rebound hammer allowed us to evaluate the hardness of the R-SACC after exposure. The output of the rebound hammer is referred to as a rebound number and corresponds with the surface hardness of the R-SACC. This method enables us to evaluate, in situ, the surface hardness of the R-SACC. Fig. 9 shows the interpretation of the RHN results. Using the average RHN results obtained for each sample, it was concluded that the heat-affected sample lost 5-23 % of its strength from 50°C to 100°C, relative to the JGJ/T23-2001 [34] recommendation; R-SACC with this amount of strength loss is still acceptable for use but requires adequate rehabilitation. Samples at 120°C were the most severely affected by heat, as about 28 % of the samples' strength was lost, suggesting that R-SACC members subjected to temperature above 120°C must be considered not serviceable. Table 5 summarizes the changes in properties of the R-SACC after extended heating.

Mass change analysis
The mass of the sample was found to be decreasing: Fig. 10 shows the mass change of the different samples after exposure to different temperatures. The mass of the control sample of cement paste was 0.016 kg for the 20 × 20 × 20 mm sample, 0.625 kg for the 40 × 40 × 150 mm sample, and 2.47 kg for the 100 × 100 × 100 mm sample. Table 6 shows the mass decrease by percentage.
Compared with the control sample, the mass was found to decrease, because the R-SAC samples exposed to elevated temperatures experience greater dehydration. The rising temperature induces deterioration due to the dehydration-related decomposition of ettringite, which creates pores followed by cracks. The surface of the R-SACC has a larger crack density. According to the test results in Fig. 11, the length of the samples shrank slightly with heating. Compared with the initial length of 20 mm at 20°C, it became 19.79 mm at 120°C; the cement sample was in a shrunken state, and the R-SACC's initial length of 40 mm at 20°C changed to 39.85 mm at 120°C. The shrinkage amount of the R-SAC paste was far greater than the shrinkage value of R-SACC.

Mechanical properties 3.5.1 Compressive strength of the R-SACC
The change in compressive strength of the R-SACC after exposure to elevated temperature was closely related to the concrete structure and the properties of each component   Fig. 12. Below 50°C, the compressive strength of concrete shows a relatively low decreasing trend, but from 70° to 120°C, the compressive strength drops sharply. Fig. 12(a) shows that the compressive strength of pure R-SAC paste decreases with increasing temperature as well as that of R-SACC, and both reach the minimum value at 120° and 100°C. As the temperature rises from room temperature until it is higher than 70°C, shrinkage occurs and the compressive strength declines noticeably. The compressive strength of R-SACC continues to decrease with increasing temperature, but the decrease is greater between 70° and 120°C. In addition, between 70° and 120°C, some of the specimens in the R-SACC cracked, and most of the cracks occurred at the corners. The reasons for the bursting of R-SACC are complex and have many influencing factors, such as heating rate, thermal stress, density, amount of moisture contained, and aggregate mineral composition. Although the bursting mechanism has yet to be identified, two main explanations have been proposed: the water vapor pressure mechanism and the thermal stress mechanism [35,36]. Research by Thomas et al. [37] and Tchekwagep et al. [30] pointed out that the increase in porosity after exposure to elevated temperatures is one of the main reasons for strength loss.

Tensile strength of R-SACC
Elevated-temperature tensile strength is an important factor in evaluating the extent of spalling and fire resistance of concrete structures. The data collected in this study can be used as an input parameter in computer models to evaluate the spalling and fire resistance of R-SACC structural members. Fig. 13 shows the variation of tensile strength as a function of temperature. The decrease in tensile strength of the R-SACC with increasing temperature can be attributed to the weak microstructure observed internally in the R-SACC, allowing initiation of micro-cracks. At 50°C, R-SACC loses about 32.4 % of its initial tensile strength. Beyond 50°C, the tensile strength of R-SACC Fig. 12 Compressive strengths of R-SACC and R-SAC relative to temperature Fig. 13 Tensile strength of R-SACC as a function of temperature |597 decreases at a rapid rate due to more pronounced thermal damage in the form of micro-cracks, falling to about 58 % of its initial strength at 120°C.

Flexural performance of R-SACC
Test data indicate that exposure to elevated temperatures causes deterioration in the flexural strength of the R-SACC (Fig. 14). At 50°C and higher, exposure to heat for an extended period causes the dehydration of the R-SAC, mostly the ettringite, which will have an impact on strength measurement. The amount of strength lost by the R-SACC at different temperatures varies considerably.
Residual strength (Fig. 15) of both R-SACC and R-SAC drops in a similar pattern as temperature rises. That implies that the sample carrying load capacity is dropping, which will eventually lead to the failure of the sample. In accord with ASTM specification 936-96, the R-SACC samples exposed to temperatures above 50°C should be demolished, not repaired, because the strength drops to 42.2 MPa which is not acceptable. Fig. 16 shows the appearance after exposure to heat, followed by load application. The slope of the stress-strain deformation curve decreases with rising temperature. The R-SACC stress-strain behavior for the control sample (20°C) displays a linear-elastic curve for the first 80 % of its strength, followed by strain softening to rupture. The behavior of all the thermally exposed samples follows a classical elasto-plastic (strain-softening) curve with a generally softer response for samples exposed to elevated temperatures. The stress-strain variation curves can be attributed to the testing conditions, moisture percentage inside the R-SACC (which was 8.2 % at 20°C, 9.5 % at 50°C, 8.7 % at 70°C, 9.5 % at 100°C and 9.3 % at 120°C), and the different exposure temperature that affect the samples.

Strain-stress
At 100° and 120°C, the characteristic trend is elastic behavior starting with a shallow slope (shallower than at 20°C), followed by gradual decrease in slope until it fails. At 50°C, the initial elastic behavior was similar to that at 20°C but then changed promptly to a very low slope (i.e., high change in strain with a smaller change in stress, more of a visco-elastic and plastic nature) with less decrease in slope until failure. The variations in the stress-strain curves can be attributed to the interior degradation observed through the stereomicroscope as well as by the MIP (mercury intrusion porosimetry) observation. The results indicate a denser area of microstructure pores with diameter between 2 and 50 nm, caused by the heat, and the pores become larger when a load is applied. The compressive stress-strain curve of the R-SACC at 50°, 70°, 100°, and 120°C shows distinctly that stress has a tendency to decline and its peak evidently descends and moves toward the right-hand side as the testing temperature increases. These differences might be due to vapor evolvement during heating, or the thermal behavior difference observed on the surface of the samples coming out of the furnace. At 50°, 70°, 100°, and 120°C, micro-cracks between the coarse aggregate and cement paste interface were visible to the eye, and these cracks contribute to the descending stress-strain curve observed when load was applied. The stress-strain curve drops perceptibly, as observed in Fig. 17, as the temperature increases.

Poisson's ratio
Poisson's ratio (ν) was determined for each sample by dividing the vertical strain by the horizontal strain obtained through strain gauges, for the short-term instantaneous value. The average values of Poisson's ratio for most of the sample tests at different temperatures were in the range from 0.25 to 0.10 with large scattering (Fig. 18). Elevated temperatures caused both horizontal and vertical strain to increase by a similar amount, so the net effect on Poisson's ratio was small. The effect of both temperature exposure and moisture content on Poisson's ratio seemed to be significant. The reason why Poisson's ratio varied somewhat is that it is difficult to change the temperature and moisture contented in the entire sample at the same rate during testing. When the tests are conducted, the moisture inside the sample may change some as well and at an uneven rate, thus changing Poisson's ratio.

Thermal mechanism analysis of the R-SAC paste
As the temperature rises to about 70° to 100°C, the hydrated ettringite crystal water and structural water in the R-SAC paste are continuously released, and the cement paste structure becomes denser. At this point, the dehydration and shrinkage of R-SACC dominate. The overall behavior pattern of the R-SAC paste is shrinkage. When the temperature reaches 120°C, the dehydration (principally of the ettringite) is complete. The dehydration-related shrinkage of the rapid cement paste is basically balanced with the thermal expansion. The volume of the R-SACC changes; the thermal expansion of the paste is more complicated than that of the R-SACC. In addition to the thermal expansion and dehydration shrinkage of the R-SACC, it is also affected by the thermal expansion of the aggregate and the change of crystal form. Summarizing the results of the various tests, when the R-SAC paste is heated from room temperature to a temperature of 70°C, the main loss occurs. The macroscopically adsorbed water in the pores and a small amount of hydrated calcium sulphoaluminate are not firmly bound to the crystallization water. The loss of this water has a significant effect on the volume of the R-SAC paste. At this point, each solid phase component of the cement paste itself is dominated by thermal expansion. The status of the R-SAC sample as a whole is in an expanded state. Fig. 19 shows the TG-DSC spectrum of the 28-day compound of the R-SAC paste. When the temperature increases to 120°C, the ettringite completely disappears.

X-ray diffraction (XRD) analysis
The XRD spectra of the samples after exposure to different elevated temperature for 4 hours and at the control temperature are shown in Fig. 20. The spectrum of the diffractive  crystal corresponds to the standard diffraction peak and there are a few impurity peaks, indicating ongoing dehydration as the temperature increased. Narrow and sharp diffraction peaks were found in all four samples at T < 70. At the diffraction angles of 10°, higher than that of other samples, indicating that the AFt crystal formed at 100°C is more than the AFt crystal dehydrate in other samples.
It can be seen from the XRD pattern of the 28-day compound of the R-SAC powder cement paste (Fig. 20(a) . However, after 100˚C, the standard XRD pattern of mineral powder cement after 28 days changed significantly: the diffraction peaks of AFt had disappeared, the number of CaSO4 diffraction peaks had decreased significantly, the intensity had decreased, and a diffraction peak of CaCO3 appeared (d = 2.77, 2.39). This indicates that above 100°C, the mineral components of the powder of the R-SAC have obviously changed; the AFt has completely decomposed.

SEM/EDS analysis of the R-SAC paste
We tested the R-SAC paste samples using SEM tools, to observe the micro-cracks with x10.00 magnification. The micro-cracks observed through SEM had diameters in the range of 1-20 nm. The micro-cracks seen in the SEM observation occupied only 0.1-0.2 % of total porous volume, and thus, little influence of micro-cracks in macron is induced on the macroporous volume of the R-SAC paste. In SEM images, two parts of micro-cracks are observed. One part is identified around paste with a flat surface and seems to be more isolated.
The further part of micro-cracks is generated around dehydrated R-SAC paste, is entirely connected with a capillary pore network, and thus may have large impact on the pore network connectivity. Two parts of micro-cracks occupy 5.4 to 9.1 % of total porous volume and are focused on the diameter of 20 to 100 nm. The ImageJ of microcrack-removed images shows only a little variation of the curve form and peak size. Moreover, the pore connectivity is only slightly weakened. The ratio between surface-connected porous volume and total porous volume decreased from 84.0 -85.3 % to 81.3-82.4 %. Overall, despite the fact that the micro-cracks contribute to whole porous volume especially in SEM images, they have minimal impact on the pore size distribution.
These tests allowed a quick visual determination of the groups of different chemical compositions that constitute a complex material. They also enabled the identification of micro-cracks, as well as apprehending the deterioration of the AFt and C-S-H, followed by the formation of AFm crystals (Fig. 21). At 120°C, the pattern of cracks was more pronounced, and the R-SAC matrix was strongly deteriorated. Fig. 22 presents the control sample at ambient temperature (20°C) and then some micrographs of the R-SACC sample after exposure to elevated temperatures. From a microstructural point of view, there was perceptible degradation of the R-SACC. According to various authors, AFt and (OH)3 dehydrate. In Fig. 22, the SEM images at ambient temperature, no visible cracking could be distinguished, and the surface of the concrete did not exhibit deterioration. Between 50° and 120°C, physicochemical changes in the R-SAC paste and aggregates occurred. Comparing the images at 50° and 70°C, we can see that the network structure of R-SAC paste dehydration product after 100°C elevated temperature is broken, the number is reduced, and cracks appear. Furthermore, the R-SACC interface structure between the material and the cement is loose, and cracks appear. Fig. 23 shows the increasing of the nanoparticle size with the rise in temperature, which correlates with the polydispersity in percentage and is in accord with the dehydration phenomenon.

Mercury intrusion porosimetry (MIP)
The mercury intrusion curves provide the total porosity (τ) by percentage. The intrusion curves of the samples are shown in Fig. 24(a). The total pore volume of samples increased in conjunction with temperature increase. Porosity values ranged from a lowest value of 24 % (control sample) to the highest value of 28.62 % (sample at 120°C). The volumes of capillary pores (>1 nm) of samples from 20° to 70°C were very close. When the temperature changed from 70° to 120°C, both capillary pores (>0.01 nm) and gel pores (<0.01 nm) increased considerably. This may be due to the decomposition of AFt between 70° and 120°C. The pore size distribution differential curve is obtained by taking the slope of the pore size distribution curve log differential intrusion against pore sizes ( Fig. 24(b)). Several peaks can be found in this curve. These peaks represent the pore diameters corresponding to the higher rate of mercury intrusion per change in pressure. These peaks are called "threshold" pore diameters. The threshold pore diameters of samples could be observed from plotting the log of differential intrusion versus pore size, as shown in  Fig. 24(b). Peaks could be found in the curve of the sample heated at 100°C. But only one peak could be found at other temperatures in Fig. 24(b). This may be caused by the enlargement of gel pores due to dehydration. Table 7 shows the summary of the MIP testing.
The value of tortuosity (τ) plotted separately for each sample shows two trend curves; the tortuosity decreases with increasing temperature and then increases. Unlike ε, τ values show a definite trend; a sharp increase is noted at 70°C. The sharp reduction value implies a tortuous flow-path (Fig. 25).
The ratio ε/τ is a characteristic material constant [38]. With the same design composition, each R-SAC paste sample, as a different porous system as the temperature increases, is expected to have its own constant ε/τ ratio. Table 8 shows the average ratio for each sample; ε/τ seems to vary marginally across the range of temperature. The volumetric stability of the R-SACC is directly tied to the relative amount of AFt in the dehydration process, which is controlled by the chemistry of the R-SAC. When the temperature exceeded 70°C, the R-SACC properties decreased steadily. As the temperature increased from 50° to 120°C, the trend of linear expansion of R-SACC and R-SAC was generally the same, showing expansion  The use of colorimetry analysis and rebound hammer testing as a quick determination of thermally induced degradation (deterioration) of R-SACC, as described in this work, could be of great value to engineers responsible for monitoring the safety of structures made with R-SAC. We have shown that this method is effective, because the color intensity and the hammer number both evidence the reduction of strength, as shown in Table 9. The NDT rebound hammer performed and colorimetry concluded of a necessity reparation when the structure has been extended exposed to heat at the temperature between 50°C to 100°C and diagnose of the non-serviceability of the sample been extendedly exposure to 120°C. Thus, in practice any R-SACC or R-SAC that has turned a yellowish tapa in color could be regarded as probably having deteriorated. Table 10 proposes a threshold table to predict the mechanical properties of the R-SACC after extended exposure to temperatures of up to 120°C. Temperatures of 70°, 100°, and 120°C were found to have a significant impact not just on the chemical properties of the R-SAC but also on the stability of the structure.

Conclusions
This study has focused on the weakening of R-SACC and R-SAC in the zone of persistence of ettringite and on the zone of decomposition. The key conclusions are summarized below. 1. The RHN and colorimetry could serve as two quick predictive tests for monitoring R-SACC structures, since after extended heat exposure, both methods detected weakening in the properties of R-SACC and R-SAC paste. The RHN has demonstrated the non-serviceability of the specimens above 50°C by characterizing the R-SACC as only fair.
2. The chemico-physico-mechanical model of thermally induced degradation developed in this study shows that the acceptable mechanical properties were retained up to 50°C, but above 50°C, the strength dropped sharply. As the amount of ettringite decreased, the mechanical properties of the R-SACC and R-SAC pastes also decreased. The impact of the dehydration of the ettringite with increased temperatures was highlighted. Ettringite seemed to have the ability to compensate for dry shrinkage or to increase the expansion of R-SAC paste to a certain extent. XRD and TG-DSC results revealed that the ettringite promoted the dehydration of R-SAC paste.
3. The compressive strength decreased along with mass loss of the ettringite from 65.15 % at 20°C to 5 % at 104°C (TGA figure), while a shape decrease was observed at 120°C when ettringite content was above 0 %. The compressive strength reached its minimum value (36.9 MPa) at an ettringite dosage of 0 %. The extent of the phenomenon is significantly bearable by the R-SACC at up to 50°C.
Above this temperature, the mismatch of thermal deformations between the R-SAC and aggregates, which expand and then undergo shrinkage, prevails and results in the development of cracks. Important cracking continues, thus altering the R-SACC mechanical properties. 4. Although there were few changes in the total porosity of R-SAC pastes with ettringite crystals, ettringite could significantly improve the pore structure by transforming large pores into small pores. R-SAC pastes after the dehydration of the ettringite showed a denser microstructure than control samples. In SEM graphs, R-SACC showed a quite high degree of porosity between 50° and 70°C. Temperatures of 70°, 100°, and 120°C were found to have a significant impact not just on the chemical properties of the R-SAC but also on the stability of the structure. All in all, the extensive exposure to heat at the chosen range of temperatures in this work was found to have an impact on the stability of the structure, because the matrix formation of ettringite was broken, the mass of the hydrated product decreased with heat exposure, and the interface between aggregate and paste in the R-SACC became loosely structured with cracks. Therefore, builders of power plant structures should pay more attention to assuring their durability when exposed to heat.