Startseite Naturwissenschaften Mechanical properties and frost resistance of recycled brick aggregate concrete modified by nano-SiO2
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Mechanical properties and frost resistance of recycled brick aggregate concrete modified by nano-SiO2

  • Tian Su , Ting Wang , Zhaochuan Zhang , Xiao Sun , Shangwei Gong , Xuefeng Mei , Zhenyu Tan und Shenao Cui EMAIL logo
Veröffentlicht/Copyright: 23. September 2023
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Nanotechnology Reviews
Aus der Zeitschrift Nanotechnology Reviews Band 12 Heft 1

Abstract

In this work, brick aggregates were immersed in nano-SiO2 solution for 2 days, and the effects of nano-SiO2 on the brick aggregate properties, mechanical properties (compressive strength, flexural strength, and splitting tensile strength), frost resistance (apparent phenomenon, mass loss, relative dynamic modulus of elasticity, and compressive strength) of recycled brick aggregate concrete and the microstructure of recycled brick aggregate concrete were investigated. The results show that nano-SiO2 can effectively improve the performance of recycled brick aggregate and the mechanical properties of recycled brick aggregate concrete, mainly by reducing the water absorption and crushing index and improving the compressive strength, flexural strength, and splitting tensile strength. With increasing nano-SiO2 solution concentration, the compressive strength, flexural strength, and splitting tensile strength of recycled brick aggregate concrete first increase and then decrease. The frost resistance of recycled brick aggregate concrete is superior to that of ordinary aggregate concrete, while the frost resistance of nano-SiO2-modified recycled brick aggregate concrete is inferior to that of recycled brick aggregate concrete. In addition, the freeze‒thaw damage mechanism of recycled brick aggregate concrete is analyzed, and a freeze‒thaw damage life prediction model of nano-SiO2-modified recycled brick aggregate concrete based on the Weibull distribution is proposed.

Graphical abstract

Keywords: recycled brick aggregate; nano-SiO2 ; mechanical property; frost resistance; microstructure; life prediction model

1 Introduction

With the increasing demand for infrastructure construction in various countries, a large amount of natural resources are consumed. At the same time, a large number of construction waste materials and construction waste are generated during the construction and demolition process, causing serious environmental pollution problems [1]. The composition of construction waste is complex, among which waste concrete and waste bricks account for a large proportion. According to statistics provided by the United States Environmental Protection Agency, from 2012 to 2014, approximately 44 million tons of waste bricks were generated from construction and demolition activities [2]. In China, there are approximately 400 million tons of waste bricks every year [3]. To realize the resource utilization of construction waste, the technology of recycled aggregate concrete has been proposed and has been widely studied by scholars all over the world.

Due to the mortar attached to the surface of the recycled coarse aggregate, the porosity and water absorption of the aggregate were high [4]. The concrete prepared by recycled coarse aggregate had multiple interface transition zones and a large number of microcracks and pores in the interface transition zone, resulting in the mechanical properties and frost resistance of recycled coarse aggregate concrete being generally inferior to ordinary concrete [5]. Compared with recycled stone aggregate, recycled brick aggregate had more pores and cracks, small hardness, high water absorption, and large crushing index, resulting in two weak links of recycled brick aggregate concrete: interface transition zone and recycled brick aggregate [6]. The replacement of natural aggregate with recycled stone aggregate and recycled brick aggregate reduced the mechanical properties of concrete, and with the increase in the replacement rate of recycled aggregate, the mechanical properties of concrete decreased.

Freeze–thaw damage is an important threat to reinforced concrete buildings in cold regions [7]. Freeze‒thaw damage leads to concrete frost heaving and cracking [8], which causes corrosion of internal reinforcement and seriously threatens the long-term safe use of concrete structures [9,10]. The frost resistance of concrete is affected by many factors, such as porosity, pore structure, water-cement ratio, environmental conditions, and aggregate type [11]. Due to the adhesion of old cement mortar on the surface of recycled aggregate and the secondary damage during the crushing process [12], the porosity of aggregate was increased, the pore structure deteriorated [13], and the type of aggregate was changed [14], resulting in the frost resistance of recycled aggregate concrete being inferior to that of ordinary concrete [15]. When the number of freeze‒thaw cycles was small, the frost resistance of recycled concrete was not significantly different from that of ordinary concrete; with the increase in the number of freeze‒thaw cycles, the frost resistance of recycled concrete deteriorated more seriously [16]. With the increasing number of freeze‒thaw cycles, the mass loss rate, relative dynamic modulus loss, and compressive strength loss of recycled concrete were significantly faster [17]. In addition, with the increase in the replacement rate of recycled aggregate, this phenomenon was more significant [18]. In particular, concrete containing recycled brick aggregate had worse frost resistance than recycled stone concrete [19], and its frost resistance must be improved to achieve its application in cold regions [20]. Therefore, improving the frost resistance of recycled concrete has become a research hotspot.

Domestic and foreign scholars have carried out corresponding research on improving the frost resistance of recycled concrete and have achieved some results [21]. The frost resistance of recycled concrete could be enhanced by reducing the water-cement ratio of concrete [22], improving the aggregate distribution and quality [23], adding silica fume or air-entraining agent [24], and using the aggregate produced by the original concrete with air-entraining agent [25,26].

In recent years, nanomaterials have been gradually applied to improve the mechanical properties and frost resistance of recycled concrete [27,28]. Among nanomaterials, nano-SiO2 not only has the advantages of high permeability [29], high specific surface energy, and good hydrophilicity but can also accelerate the hydration rate of cement [30] and improve the mechanical properties and porosity of concrete [31]. Therefore, nano-SiO2 began to be applied to enhance the performance of recycled concrete. Shahbazpanahi et al. [32] found that the incorporation of nano-SiO2 made the interfacial transition zone between recycled aggregate and mortar denser, increasing the C–S–H content, reducing the content of CH and AFt, and improving the internal pore structure of concrete. Li et al. [33] noted that nano-SiO2 could significantly enhance the microhardness of the interface transition zone, thereby improving the mechanical properties and durability of concrete [34,35]. However, the incorporation of nano-SiO2 should be controlled within a certain range. If the incorporation of nano-SiO2 was too large, it could lead to a decrease in the mechanical properties and durability of concrete [36,37].

The poor performance of recycled aggregate was the main reason for the poor mechanical properties and durability of recycled concrete [38,39]. Therefore, improving the performance of recycled aggregate could effectively improve the mechanical properties and durability of recycled concrete [40]. Meng et al. [41] found that after the modification of nanomaterials, the crushing index of recycled coarse aggregate decreased, which improved the mechanical properties of recycled concrete. Wang et al. [42] noted that after the modification of nanomaterials, the water absorption and crushing index of recycled brick aggregate decreased, while the compressive strength of brick aggregate concrete at different ages increased.

In the existing research, there have been relatively few studies on the frost resistance of concrete prepared by nano-modified recycled aggregate. However, improving the frost resistance of recycled concrete is the key to its application in cold regions. The objective of this study is to investigate the mechanical properties and frost resistance of recycled brick aggregate concrete modified by nano-SiO2 and compare them with those of unmodified brick aggregate concrete and ordinary concrete, investigate the effects of nano-SiO2 on the microstructure of recycled brick aggregate concrete, and propose a freeze‒thaw damage life prediction model of nano-modified recycled brick aggregate concrete based on the Weibull distribution.

2 Experimental overview

2.1 Raw materials

  1. Cement

P.O 42.5 ordinary Portland cement used for the concrete mixtures was produced by Zibo Shanshui Cement Co., Ltd. The physical performance and chemical composition are listed in Tables 1 and 2, respectively.

  1. Fine aggregate

    Natural river sand was used as fine aggregate conforming to the Chinese standard GB/T 14684−2011 [43], and the fineness modulus was 2.9.

  2. Coarse aggregate

    Coarse aggregates included natural gravel and recycled brick aggregates with a particle size of 5–25 mm. The water absorption of natural aggregate and recycled brick aggregate was 1.10 and 16.50%, respectively, and the crushing index was 8.70 and 27.90%, respectively.

  3. Nanomaterial

    Nano-SiO2 with a particle size of 20 nm was selected, and the properties are listed in Table 3.

Table 1

Properties of P.O 42.5 ordinary Portland cement

Specific surface area (m2 kg−1) Ignition loss (%) Initial/final setting times (min) 3 days/28 days flexural strength (MPa) 3 days/28 days compressive strength (MPa)
322 2.4 205/255 5.6/8.9 25.5/47.6
Table 2

Chemical composition of P.O 42.5 ordinary Portland cement

Chemical composition SiO2 Al2O3 Fe2O3 CaO MgO SO3
Content (%) 21.6 5.78 3.96 61.25 1.76 2.46
Table 3

Properties of nano-SiO2

Particle size (nm) Specific surface area (m2 g−1) Bulk density (g m−3)
20 240 0.06

2.2 Recycled brick aggregate modified by nanomaterials

The recycled bricks were crushed by a jaw crusher, and then the recycled brick aggregates were cleaned and dried. Finally, the recycled brick aggregates were graded to meet the requirements of aggregate distribution.

Nano-SiO2 powder was added to the solution and mechanically stirred for 5 min. The brick aggregate was immersed in 1, 2, and 3% nano-SiO2 solutions for 2 days, and the nano-SiO2 solution was dispersed by an ultrasonic disperser to prevent particle agglomeration. The process is shown in Figure 1.

Figure 1 Aggregate modification process.
Figure 1

Aggregate modification process.

2.3 Mixture proportion

The mixture proportions of natural aggregate concrete and recycled brick aggregate concrete were designed according to JGJ55-2011 [44], and the design water-to-binder (w/b) ratio of concrete was 0.5, as detailed in Table 4 (due to the large difference between the density of recycled brick aggregate and natural aggregate, this study adopted the volume substitution method to ensure that the absolute volume of each cubic meter of concrete remained unchanged). It should be noted that the recycled brick aggregate was soaked with nano-SiO2 solution at concentrations of 0, 1, 2, and 3% before being used.

Table 4

Mix proportions of concrete (kg m−3)

Type Water Cement Sand NCA RCA Q1* Q2* Q3*
p 175 350 700 1,140 0 0 0 0
B25 175 350 700 855 234 − − −
B50 175 350 700 570 468 − − −
B75 175 350 700 285 702 − − −
B100 175 350 700 0 936 − − −
LB25 175 350 700 855 − 234 − −
LB50 175 350 700 570 − 468 − −
LB75 175 350 700 285 − 702 − −
LB100 175 350 700 0 − 936 − −
MB25 175 350 700 855 − − 234 −
MB50 175 350 700 570 − − 468 −
MB75 175 350 700 285 − − 702 −
MB100 175 350 700 0 − − 936 −
HB25 175 350 700 855 − − − 234
HB50 175 350 700 570 − − − 468
HB75 175 350 700 285 − − − 702
HB100 175 350 700 0 − − − 936

*Q1, Q2, and Q3 are recycled brick aggregates modified with nano-SiO2 solutions at concentrations of 1, 2, and 3%, respectively. The unmodified recycled brick aggregate was soaked in water for 2 days to ensure that it reached a saturated surface dry state.

2.4 Test method

2.4.1 Mechanical properties test

The mechanical properties of the concrete specimens were tested in accordance with GBT 50081–2019 [45], as shown in Figure 2, and the test details are shown in Table 5.

Figure 2 Mechanical properties test. (a) Compressive strength test, (b) splitting tensile strength test, and (c) flexural strength test.
Figure 2

Mechanical properties test. (a) Compressive strength test, (b) splitting tensile strength test, and (c) flexural strength test.

Table 5

Mechanical properties test details

Test Specimen size (mm) Conversion coefficient Loading speed (MPa/s)
Compressive strength test 100 × 100 × 100 0.95 0.6
Flexural strength test 100 × 100 × 400 0.85 0.05
Splitting tensile strength test 100 × 100 × 100 0.85 0.05

2.4.2 Freeze‒thaw cycle test

According to the Standard for Long-term Performance and Durability of Ordinary Concrete [46], the concrete prism specimens (100 mm × 100 mm × 400 mm) and concrete cube specimens (100 mm × 100 mm × 100 mm) were tested by a rapid freeze‒thaw cycle testing machine, as shown in Figure 3.

Figure 3 Rapid freeze‒thaw cycle testing machine.
Figure 3

Rapid freeze‒thaw cycle testing machine.

2.4.3 Relative dynamic modulus elasticity test

The DT-10 W dynamic elastic modulus tester produced by Tianjin Luda Construction Instrument Co., Ltd was used to test concrete prism specimens under different freeze‒thaw cycles, as shown in Figure 4.

Figure 4 Relative dynamic modulus elasticity test.
Figure 4

Relative dynamic modulus elasticity test.

2.4.4 Microstructure test

Microstructure tests include general microscope tests and electron microscope scanning tests. An electronic microscope produced by Jiangsu Leyes Technology Co., Ltd was used for the general microscope test, and field emission environmental scanning electron microscopy was used for the electron microscope scanning test, as shown in Figure 5.

Figure 5 Microstructure test. (a) General microscope test and (b) scanning electron microscope test.
Figure 5

Microstructure test. (a) General microscope test and (b) scanning electron microscope test.

Concrete specimens with a size of 15 mm × 15 mm × 15 mm were selected for observation under a general electronic microscope; concrete specimens with a size of 10 mm × 10 mm × 10 mm were selected for gold spraying treatment and then tested under a scanning electron microscope.

3 Results and analysis

3.1 Nano-modified recycled brick aggregate properties

The apparent phenomena of aggregates were observed through a general microscope, as shown in Figure 6. The surface of the stone aggregate was smooth with fewer pores and cracks, and its compactness was relatively high; the surface of the brick aggregate was rough with a large number of cracks and pores, and its compactness was low. After the brick aggregate is modified with nano-SiO2, its surface pores and cracks are filled with nano-SiO2 particles. As the concentration of nano-SiO2 solution increased, the number and size of surface cracks and pores on the brick aggregate gradually decreased, and the roughness gradually decreased. However, with the continuous increase in the concentration of the nano-SiO2 solution, some nano-SiO2 exhibited agglomeration phenomena. The reason for this phenomenon is that nano-SiO2 is insoluble in water. When the concentration of nano-SiO2 is too high, a small portion of nano-SiO2 will enter the brick aggregate together with water, while another portion of nano-SiO2 will adsorb on the surface of the brick aggregate due to its rough surface and even distribution. Most of the nano-SiO2 will gradually settle on the surface of the brick aggregate under the action of gravity, which easily causes nano-SiO2 agglomeration.

Figure 6 Apparent phenomena of aggregates before and after nano-SiO2 modification. (a) P, (b) B, (c) LB, (d) MB, and (e) HB.
Figure 6

Apparent phenomena of aggregates before and after nano-SiO2 modification. (a) P, (b) B, (c) LB, (d) MB, and (e) HB.

The crushing index and water absorption of recycled brick aggregate before and after nano-SiO2 modification are shown in Figure 7. After nano-modification, the water absorption and crushing index of the recycled brick aggregate decreased, and with the increase in the nano-SiO2 concentration, the water absorption and crushing index decreased more significantly. The decrease in water absorption was larger than that of the crushing index, and the water absorption of recycled brick aggregate decreased by 15.09, 19.52, and 27.09%, respectively, after being modified by soaking in 1, 2, and 3% nano-SiO2 solution, while the crushing index decreased by 6.74, 10.18, and 14.52%, respectively. This is due to the filling of recycled brick aggregate pores with nano-SiO2, which reduces the water absorption and crushing index of the aggregate. This was consistent with the results of Wang et al. [42]. However, nano-SiO2 does not react with the recycled brick aggregate and only fills the pores, with limited improvement in aggregate strength.

Figure 7 Aggregate properties before and after nano-SiO2 modification. (a) Crushing index and (b) water absorption.
Figure 7

Aggregate properties before and after nano-SiO2 modification. (a) Crushing index and (b) water absorption.

3.2 Mechanical properties

The compressive strength, flexural strength, and splitting tensile strength before and after nano-SiO2 modification are shown in Figures 8–10. As the replacement rate of brick aggregate increased, the compressive strength, flexural strength, and splitting tensile strength of the concrete showed a downward trend, and the downward trend was increasingly obvious. The reasons are as follows: on the one hand, the recycled brick aggregate has low strength and high porosity, resulting in lower strength of concrete; while on the other hand, due to the high moisture content of the brick aggregate, the effective water cement ratio of concrete increases, which leads to a decrease in concrete strength.

Figure 8 Compressive strength before and after nano-SiO2 modification.
Figure 8

Compressive strength before and after nano-SiO2 modification.

Figure 9 Flexural strength before and after nano-SiO2 modification.
Figure 9

Flexural strength before and after nano-SiO2 modification.

Figure 10 Splitting tensile strength before and after nano-SiO2 modification.
Figure 10

Splitting tensile strength before and after nano-SiO2 modification.

After nano-SiO2 modification, the compressive strength, flexural strength, and splitting tensile strength of recycled brick aggregate concrete were significantly improved. The reason is that nano-SiO2 can fill the pores of recycled brick aggregate and increase the compactness of concrete. In addition, nano-SiO2 has chemical activity, which can promote cement hydration and secondary reaction with Ca(OH)2 to produce C–S–H gel to strengthen the interfacial transition zone between cement mortar and recycled brick aggregate, thereby improving the mechanical properties of recycled brick aggregate concrete.

With the increase in the nano-SiO2 solution concentration, the compressive strength, flexural strength, and splitting tensile strength of recycled brick aggregate concrete first increased and then decreased. Therefore, when the concentration of nano-solution was 2%, the mechanical properties of recycled brick aggregate concrete were the best. This may be because although nano-SiO2 is adsorbed on the recycled brick aggregate, it easily falls off and integrates into the cement mortar. With the increase in the nano-SiO2 solution concentration, more nanomaterials are integrated into the cement mortar, and nano-SiO2 is not easy to disperse in the wet state, which leads to the agglomeration of nano-SiO2 and reduces the strength of concrete cement stone, thus reducing the strength of concrete.

3.3 Freeze‒thaw test phenomenon

The apparent phenomena of each group of concrete specimens after different freeze‒thaw cycles are shown in Figure 11. Before the freeze‒thaw cycles, the surface of the specimen was smooth, and there was no significant difference between each group of specimens. After 10 freeze‒thaw cycles, a small amount of cement mortar fell off the surface of each group of specimens, and there were small holes. The shedding phenomenon of the specimens was not significant, and the apparent phenomenon of each group of specimens was not significantly different. After 20 freeze‒thaw cycles, the number of small holes in the P-group specimens increased, and the coarse aggregate was exposed. The surface of the B50-group specimens became rough, there were dense small holes, and the amount of mortar shedding increased. The surface holes in B50-group specimens were smaller than those in MB50-group specimens. As the number of freeze‒thaw cycles continued to increase, the aggregate exposure of the P-group specimens was more significant than that of the B50-group and MB50-group, and the number of holes in the B50-group was less than that in the MB50-group. The reasons for this situation are as follows: According to hydrostatic pressure theory [47] and osmotic pressure theory [48], when the freeze‒thaw cycle occurs, the large pores in the connected pores will absorb the water in the small pore, thus squeezing the pore wall and causing internal damage to the concrete. For ordinary aggregate concrete, the interface transition zone is equivalent to the large pore, which is the part where freeze‒thaw damage occurs. After the interface transition zone is damaged, the aggregate is peeled off from the cement mortar, resulting in the exposure of coarse aggregate. For recycled brick aggregate concrete, due to the large water absorption of recycled brick aggregate, the water in the interfacial transition zone will enter the recycled brick aggregate during the freeze‒thaw cycles, which alleviates the pressure in the interfacial transition zone. In addition, the surface of the recycled brick aggregate is rougher, and the pores and cracks are increasingly larger so that the cement slurry flows into the brick aggregate and melts into one. The bonding effect between the recycled brick aggregate and cement mortar is better, which improves the frost resistance of concrete to a certain extent. For nano-SiO2-modified recycled brick aggregate concrete, nano-SiO2 fills the cracks and pores on the surface of the recycled brick aggregate, reduces its surface roughness, blocks the passage of cement mortar into the brick aggregate, making it easier for the cement mortar to fall off, and reduces the frost resistance of the concrete.

Figure 11 Apparent phenomena of concrete after freeze‒thaw cycles. (a) 10 freeze‒thaw cycles, (b) 20 freeze‒thaw cycles, (c) 30 freeze‒thaw cycles, (d) 40 freeze‒thaw cycles, (e) 50 freeze‒thaw cycles, and (f) 60 freeze‒thaw cycles.
Figure 11

Apparent phenomena of concrete after freeze‒thaw cycles. (a) 10 freeze‒thaw cycles, (b) 20 freeze‒thaw cycles, (c) 30 freeze‒thaw cycles, (d) 40 freeze‒thaw cycles, (e) 50 freeze‒thaw cycles, and (f) 60 freeze‒thaw cycles.

3.4 Mass loss after freeze‒thaw cycles

The mass loss of each group of concrete specimens after different freeze‒thaw cycles is shown in Figure 12. Figure 12 shows that as the number of freeze‒thaw cycles increased, the mass loss first decreased and then increased. When the number of freeze‒thaw cycles was less, the mass loss of the specimen decreased. The reason is that the mass loss of concrete caused by freeze‒thaw is less at this time, while the small holes and cracks in the concrete increase after the freeze‒thaw cycle, resulting in a larger mass of water absorbed inside the concrete.

Figure 12 Mass loss of concrete after freeze‒thaw cycles.
Figure 12

Mass loss of concrete after freeze‒thaw cycles.

In addition, the mass loss of ordinary aggregate concrete was larger than that of recycled brick aggregate concrete. The reason is that the porosity and water absorption of brick aggregate are larger than those of ordinary aggregate, which leads to more water absorption of recycled brick aggregate concrete during freeze‒thaw cycles. In addition, recycled brick aggregate has a stronger bonding ability with cement mortar, resulting in less cement mortar shedding.

Before 40 freeze‒thaw cycles, the mass loss of recycled brick aggregate concrete was larger than that of nano-SiO2-modified recycled brick aggregate concrete. After 40 freeze‒thaw cycles, the mass loss of recycled brick aggregate concrete was lower than that of nano-SiO2-modified recycled brick aggregate concrete. This may be because nano-SiO2 blocks some of the pores in the brick aggregate during the initial stage of freezing and thawing, forming closed pores and resulting in a relatively small frost pressure. As the number of freeze‒thaw cycles increases, the pores blocked by nano-SiO2 gradually connect with the large pores, absorbing a large amount of water and resulting in an increase in frost pressure.

3.5 Relative dynamic elastic modulus after freeze‒thaw cycles

The relative dynamic elastic modulus of each group of concrete specimens after different freeze‒thaw cycles is shown in Figure 13. The relative dynamic elastic modulus of the concrete specimens presented a downward trend with increasing freeze‒thaw cycles. This is due to the increasing freeze‒thaw damage of concrete, which leads to a decrease in the relative dynamic elastic modulus. After 60 freeze‒thaw cycles, the relative dynamic elastic modulus of ordinary aggregate concrete, recycled brick aggregate concrete, and nano-SiO2-modified recycled brick aggregate concrete were 52, 60, and 55%, respectively. The appropriate addition of brick aggregate can play the role of an air-entraining agent, thereby enhancing the frost resistance of concrete. However, the nano-SiO2-modified recycled brick aggregate will prevent the water in the interfacial transition zone from flowing into the brick aggregate, which reduces the effect of the brick aggregate air-entraining agent.

Figure 13 Relative dynamic elastic modulus of concrete after freeze‒thaw cycles.
Figure 13

Relative dynamic elastic modulus of concrete after freeze‒thaw cycles.

3.6 Compressive strength after freeze‒thaw cycles

The compressive strength of each group of concrete specimens after different freeze‒thaw cycles is shown in Figure 14. With the increase in the number of freeze‒thaw cycles, the compressive strength of concrete decreased gradually. At 15 freeze‒thaw cycles, the compressive strength loss of ordinary aggregate concrete and nano-SiO2-modified recycled brick aggregate concrete was small (compressive strength loss rates were 10 and 16.9%, respectively), while the compressive strength loss of recycled brick aggregate concrete was large (compressive strength loss rate was 26.5%). This is because when the number of freeze‒thaw cycles is small, the density of concrete plays a major role in frost resistance. The effective water-cement ratio of ordinary concrete is low, and its compactness is larger than that of recycled brick aggregate concrete. Nano-SiO2 can promote the hydration reaction, so the compactness of nano-SiO2-modified recycled brick aggregate concrete is also larger than that of recycled brick aggregate concrete.

Figure 14 Compressive strength of concrete after freeze‒thaw cycles.
Figure 14

Compressive strength of concrete after freeze‒thaw cycles.

When the number of freeze‒thaw cycles exceeded 15, the compressive strength loss of the concrete began to increase. This is because due to the increase in the number of freeze‒thaw cycles, the cement stone on the surface of the specimen continues to fall off, and the free water of the smaller pores gradually produces ice crystals. The specimen is subjected to the expansion of a large number of ice crystals, which gradually accelerates the growth of the compressive strength loss of the specimen. In addition, the compressive strength loss of ordinary aggregate concrete and nano-SiO2-modified recycled brick aggregate concrete was gradually higher than that of recycled brick aggregate concrete. After 60 freeze‒thaw cycles, the compressive strength losses of ordinary aggregate concrete, nano-SiO2-modified recycled brick aggregate concrete, and recycled brick aggregate concrete were 83.2, 76.4, and 68.9%, respectively. This is because when the number of freeze‒thaw cycles is large, the frost damage of concrete is mainly caused by the spalling of cement paste. When the recycled brick aggregate concrete is subjected to freeze‒thaw damage, the voids on the surface of the recycled brick aggregate can alleviate the volume expansion pressure caused by water icing, thereby improving its frost resistance; in addition, the surface of the brick aggregate is rough, and the bond strength with the cement paste is stronger, so that the cement paste of the specimen does not easily fall off, which slows down the continuous damage caused by the new pores of the specimen [16]. After nano-SiO2 modification of the recycled brick aggregate, cracks and holes on the surface of the brick aggregate are filled. When the freezing pressure is too large, nano-SiO2 hinders the flow of water from the interface transition zone to the brick aggregate, which makes the pressure in the interface transition zone too large, making it easier for the cement stone to fall off the aggregate and reducing the frost resistance of the specimen.

3.7 Microstructure after freeze‒thaw cycles

The microstructure of each group of concrete specimens after different freeze‒thaw cycles is shown in Figure 15. After freeze‒thaw cycles, the cement stone in the interface transition zone of each group of concrete specimens gradually became dispersed, some cement stone was missing, and cracks appeared in the bonding zone with the aggregate. This is due to the action of hydrostatic pressure and osmotic pressure, and cement stone produces cracks and holes, which continue to develop, resulting in cement stone splitting and missing.

Figure 15 Microstructure of concrete after freeze‒thaw cycles. (a) P after 15 freeze‒thaw cycles, (b) P after 45 freeze‒thaw cycles, (c) B50 before freeze‒thaw cycles, (d) B50 after 15 freeze‒thaw cycles, (e) B50 after 45 freeze‒thaw cycles, (f) MB50 before freeze‒thaw cycles, (g) MB50 after 15 freeze‒thaw cycles, (h) MB50 after 45 freeze‒thaw cycles, and (i) MB50 after 60 freeze‒thaw cycles.
Figure 15 Microstructure of concrete after freeze‒thaw cycles. (a) P after 15 freeze‒thaw cycles, (b) P after 45 freeze‒thaw cycles, (c) B50 before freeze‒thaw cycles, (d) B50 after 15 freeze‒thaw cycles, (e) B50 after 45 freeze‒thaw cycles, (f) MB50 before freeze‒thaw cycles, (g) MB50 after 15 freeze‒thaw cycles, (h) MB50 after 45 freeze‒thaw cycles, and (i) MB50 after 60 freeze‒thaw cycles.
Figure 15 Microstructure of concrete after freeze‒thaw cycles. (a) P after 15 freeze‒thaw cycles, (b) P after 45 freeze‒thaw cycles, (c) B50 before freeze‒thaw cycles, (d) B50 after 15 freeze‒thaw cycles, (e) B50 after 45 freeze‒thaw cycles, (f) MB50 before freeze‒thaw cycles, (g) MB50 after 15 freeze‒thaw cycles, (h) MB50 after 45 freeze‒thaw cycles, and (i) MB50 after 60 freeze‒thaw cycles.
Figure 15

Microstructure of concrete after freeze‒thaw cycles. (a) P after 15 freeze‒thaw cycles, (b) P after 45 freeze‒thaw cycles, (c) B50 before freeze‒thaw cycles, (d) B50 after 15 freeze‒thaw cycles, (e) B50 after 45 freeze‒thaw cycles, (f) MB50 before freeze‒thaw cycles, (g) MB50 after 15 freeze‒thaw cycles, (h) MB50 after 45 freeze‒thaw cycles, and (i) MB50 after 60 freeze‒thaw cycles.

Figure 15(a-1, b-1, d-1, e-1) shows that under the same number of freeze‒thaw cycles, the interfacial transition zone between stone aggregate and mortar was more likely to produce cracks and pores. The cracks divided the cement mortar into small pieces (a-1), and the separation speed of stone aggregate and cement mortar was faster than that of brick aggregate and cement mortar.

Figure 15(a-2, b-2, d-2, e-2) shows that under the same number of freeze‒thaw cycles, the pores in the interfacial transition zone of ordinary aggregate concrete were larger, and the spalling of cement mortar was more serious. Although there were also pores in the interfacial transition zone of recycled brick aggregate concrete, the integrity of the cement stone was good, and there was no large amount of cement stone spalling. This is because the surface of the recycled brick aggregate is rough and the cement mortar can enter the brick aggregate through the pores, so the bonding ability of the recycled brick aggregate and the cement mortar is stronger, and it is not easy to damage after the freeze‒thaw cycles. In addition, the pores on the surface of the recycled brick aggregate can alleviate the volume expansion pressure caused by water icing.

Figure 15(c-1, e-1, g-1, h-1) shows that under the same number of freeze‒thaw cycles, there were no significant cracks and pores in the cement paste in the interface transition zone of recycled brick aggregate concrete and nano-SiO2-modified brick aggregate concrete. However, after 45 freeze‒thaw cycles, the interfacial transition zone of recycled brick aggregate concrete and nano-SiO2-modified brick aggregate concrete appeared to have a significant boundary.

Figure 15(d-2, h-2) shows that after 45 freeze‒thaw cycles, the cracks and pores of cement mortar in the interfacial transition zone of nano-SiO2-modified brick aggregate concrete were significantly more than those of recycled brick aggregate concrete. This is due to nano-SiO2 filling the pores and cracks on the surface of the recycled brick aggregate and reducing its roughness [49], resulting in a decrease in the amount of cement mortar entering the recycled brick aggregate and a decrease in the bond force between the cement mortar and recycled brick aggregate. In addition, nano-SiO2 hinders the passage of recycled brick aggregates that alleviate water pressure in the interface transition zone.

3.8 Freeze‒thaw damage mechanism

The concrete freeze‒thaw damage schematic diagram is shown in Figure 16. After the concrete was soaked in water for 4 days, water and air sacs coexisted in the pores of the concrete, as shown in Figure 16(a). Ordinary concrete had fewer overall air sacs, ordinary recycled brick aggregate concrete had more air sacs, and nano-modified recycled brick aggregate had the most air sacs. This is because the water cannot completely exclude the air sac in the concrete under normal pressure, and the larger the porosity of the aggregate, the higher the content of the air sacs. The stone aggregate is nearly solid, and there are very few air sacs in ordinary concrete. Brick aggregate has more air sacs due to its high porosity and complexity of pore structure. Although nano-modified concrete reduces the porosity of the transition zone due to the filling of brick aggregates with nanomaterials and the promotion of hydration products in the interface transition zone, it also blocks the channel of water flow into the brick aggregate, resulting in more air sacs in the concrete. This can be proven by the mass loss of concrete during freeze‒thaw cycles; that is, when the number of freeze‒thaw cycles is small, the concrete mass continues to increase. The degree of mass increase is ordinary concrete < recycled brick aggregate concrete < nano-modified recycled brick aggregate concrete, which reflects the volume of air sacs contained in the concrete.

Figure 16 Concrete freeze‒thaw damage schematic diagram. (a) Concrete soaking for 4 days, (b) concrete freezing process, and (c) concrete thawing process.
Figure 16 Concrete freeze‒thaw damage schematic diagram. (a) Concrete soaking for 4 days, (b) concrete freezing process, and (c) concrete thawing process.
Figure 16

Concrete freeze‒thaw damage schematic diagram. (a) Concrete soaking for 4 days, (b) concrete freezing process, and (c) concrete thawing process.

When the concrete was frozen, the water around the specimen froze from the outside to the inside due to the temperature transfer process, causing the surface water of the specimen to first freeze and form a closed space to wrap the specimen, preventing the flow of water inside and outside the specimen. Then, the water inside the specimen partially froze, resulting in an increase in the volume and movement of the internal water, as shown in Figure 16(b). For ordinary stone aggregate concrete, due to the larger pore size of the interface transition zone than that of cement stone, water flow converged toward the interface transition zone during the freezing process, and the interface transition zone first froze. Due to the lack of air sacs in the interface transition zone to relieve pressure, it is subjected to significant water pressure, resulting in severe freeze‒thaw damage. For recycled brick aggregate concrete, due to the smaller pore size of the interface transition zone compared to the internal pores of the brick aggregate, water flowed into the brick aggregate during the freezing process. The water inside the capillary opening carried some air sacs to flow toward the large or small pores; the water inside the small pores carried some air sacs to flow toward the large pores, which could effectively alleviate water pressure. According to osmotic pressure theory, the large pores and small pores in the brick produced greater water pressure, but there were air sacs in the large pores and small pores to relieve the water pressure. Therefore, the degree of damage caused by pore water pressure inside the brick aggregate was limited, and the water pressure in the interface transition zone was very low because brick aggregate absorbed water in the interface transition zone. For nano-modified recycled brick aggregate concrete, the surface pores of the brick aggregate were blocked by nanomaterials and their hydration products, which hindered the flow of water between the interface transition zone and the brick aggregate. The interface transition zone first froze, and then the water flow of small holes in the surrounding cement stone converged toward the interface transition zone. Similar to recycled brick aggregate concrete, the presence of air sacs alleviated water pressure. The water pressure in the interfacial transition zone of nano-modified recycled brick aggregate concrete was larger than that of recycled brick aggregate concrete; the water pressure in the interfacial transition zone of nano-modified recycled brick aggregate concrete was lower than that of ordinary concrete. Therefore, the frost resistance of nano-modified recycled brick aggregate concrete was superior to that of ordinary concrete but inferior to that of recycled brick aggregate concrete.

During the thawing process, the external water of the concrete first thawed, and the enclosed space formed by the ice layer disappeared. The internal and external water could flow, as shown in Figure 16(c). Due to the shedding of cement stone during the freeze‒thaw process, the concrete formed a deep-water channel inside the specimen (the size of the water channel in ordinary concrete specimens > the size of the water channel in nano-modified recycled brick aggregate concrete > the size of the water channel in recycled brick aggregate concrete). The water channel made the external water enter the interior of the specimen and increased the channel for the air sacs to discharge the specimen, thereby increasing the saturation of the specimen. For ordinary concrete, due to the smooth surface of the stone aggregate, the cement stone was prone to separation and detachment from the stones, which could easily form a water flow channel entering the interior of the specimen, which was detrimental to the frost resistance of the specimen. For recycled brick aggregate concrete, the water pressure in the interfacial transition zone was slowed down, which reduced the speed of cement stone shedding on the surface, thus slowing down the speed of external cracks penetrating into the interior, reducing the growth rate of saturation, and thereby improving the frost resistance of concrete. Compared with recycled brick aggregate concrete, the water pressure in the interfacial transition zone of nano-modified recycled brick aggregate concrete was higher, and the cement stone fell off relatively faster, which improved the speed of external cracks penetrating into the interior, increasing the growth rate of saturation and thereby reducing the frost resistance of concrete.

3.9 Prediction of frost resistance life

In this study, the damage degree D n is defined as follows:

(1) D n = E 0 − E n E 0 ,

where E 0 is the dynamic elastic modulus without a freeze‒thaw cycle; and E n is the dynamic elastic modulus after n freeze‒thaw cycles.

The probability density function of the concrete freeze‒thaw cycle life N was established using a two-parameter model as follows [50]:

(2) f ( N ) = b a n a ( b − 1 ) exp − n a b ,

where a is the scale standard, and b is the shape standard.

The probability distribution function for the life of concrete structures is as follows:

(3) F ( N ) = 1 − exp − n a b .

When subjected to n 1 freeze‒thaw cycles, the failure probability of concrete is as follows:

(4) P f ( n 1 ) = 1 − exp − n 1 a b .

The reliability function can be obtained from the Weibull distribution function as follows:

(5) R ( n ) = 1 − F ( n ) = exp − n a b = 1 − D ( n ) .

Perform a Weibull transformation on equation (5):

(6) ln ln 1 R n = b ( ln ( n ) − ln ( a ) ) .

Order Y = ln(1/R(n)), X = ln(n), C = −bln(a), and equation (6) could be converted to Y = Y(X) = bx + C.

Using the actual number of freeze‒thaw cycles as an independent variable, data fitting was performed using Origin software to obtain the Weibull distribution value of the concrete life, as shown in Table 6. Linear fitting is performed on the Weibull values in Table 6 to obtain the corresponding Weibull parameter values b and C, as shown in Table 7 and Figure 17.

Table 6

Weibull distribution value

Freeze‒thaw cycles 1/R(n) X = ln(n) Y = ln(ln(1/R(n)))
P 10 1.033058 2.302585 −3.425802
20 1.075269 2.995732 −2.623194
30 1.199041 3.401197 −1.706379
40 1.538462 3.688879 −0.842151
50 1.666667 3.912023 −0.671727
60 1.923077 4.094345 −0.424760
B50 10 1.048218 2.302585 −3.055660
20 1.075269 2.995732 −2.623194
30 1.234568 3.401197 −1.557220
40 1.310616 3.688879 −1.307493
50 1.428571 3.912023 −1.030930
60 1.666667 4.094345 −0.671727
MB50 10 1.041667 2.302585 −3.198534
20 1.081081 2.995732 −2.551540
30 1.282051 3.401197 −1.392468
40 1.333333 3.688879 −1.245899
50 1.562500 3.912023 −0.806793
60 1.818182 4.094345 −0.514437
Table 7

Weibull fitting parameters

b C R 2
P 1.78883 −7.69613 0.97472
B50 1.38057 −6.40043 0.95773
MB50 1.54921 −6.88425 0.96955
Figure 17 Weibull fitting line.
Figure 17

Weibull fitting line.

From Table 7 and Figure 17, it can be seen that the correlation coefficient R 2 was larger than 0.95, indicating that the linear correlation between Y and X was good, that is, the measured data met the Weibull distribution. The Weibull distribution life prediction model for concrete under actual freeze‒thaw cycles is as follows:

(7) P : Y = ln ( ln ( 1 / R ( n ) ) ) = 1.78883 ln ( n ) − 7.69613 ,

(8) B 50 : Y = ln ( ln ( 1 / R ( n ) ) ) = 1.38057 ln ( n ) − 6.40043 ,

(9) WB 50 : Y = ln ( ln ( 1 / R ( n ) ) ) = 1.54921 ln ( n ) − 6.88425 ,

When R(n) = 0.6, the concrete could be judged as invalid. By substituting R(n) = 0.6 in the model obtained above, it could be concluded that the ultimate freeze‒thaw cycles for ordinary concrete, recycled brick aggregate concrete, and nano-SiO2-modified recycled brick aggregate concrete were 50, 63, and 55 times, respectively.

4 Conclusion

  1. The crushing index and water absorption of nano-SiO2-modified recycled brick aggregate were lower than those of recycled brick aggregate, and with increasing nano-SiO2 concentration, the water absorption and crushing index decreased more significantly.

  2. After nano-SiO2 modification, the compressive strength, flexural strength, and splitting tensile strength of recycled brick aggregate concrete were significantly improved. With the increase in the nano-SiO2 solution concentration, the compressive strength, flexural strength, and splitting tensile strength of recycled brick aggregate concrete first increased and then decreased.

  3. With the increase in the number of freeze‒thaw cycles, the mortar on the concrete surface fell off and the coarse aggregate was exposed, and the mass loss first decreased and then increased, while the relative dynamic elastic modulus and compressive strength decreased gradually.

  4. The frost resistance of recycled brick aggregate concrete was superior to that of ordinary aggregate concrete, while the frost resistance of nano-SiO2-modified recycled brick aggregate concrete was inferior to that of recycled brick aggregate concrete.

  5. The freeze‒thaw damage mechanism of recycled brick aggregate concrete was analyzed, and a freeze‒thaw damage life prediction model of nano-SiO2-modified recycled brick aggregate concrete based on the Weibull distribution was proposed.

  1. Funding information: The study was carried out with the support of the Foundation of China Postdoctoral Science Foundation (2022M723687); Doctoral Science and Technology Startup Foundation of Shandong University of Technology (420048); Shandong Province Natural Science Foundation (ZR2021QE209); and Shandong University of Technology Student Innovation and Entrepreneurship Training Program.

  2. Author contributions: Tian Su: investigation, experimental program, funding acquisition, writing – original draft preparation, and review and editing; Shenao Cui: experimental study, data analysis, and writing – original draft preparation; Ting Wang: data analysis, writing – review and editing, and checking the original draft; Zhaochuan Zhang and Xiao Sun: experimental study; Zhenyu Tan and Xuefeng Mei: checking the original draft. All authors have accepted responsibility for the entire content of this manuscript and approved its submission.

  3. Conflict of interest: The authors state no conflict of interest.

  4. Data availability statement: All data generated or analyzed during this study are included in this published article.

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Received: 2023-03-29
Revised: 2023-06-23
Accepted: 2023-06-30
Published Online: 2023-09-23

© 2023 the author(s), published by De Gruyter

This work is licensed under the Creative Commons Attribution 4.0 International License.

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  65. Molecular dynamics study on dynamic interlayer friction of graphene and its strain effect
  66. Induction of apoptosis and autophagy via regulation of AKT and JNK mitogen-activated protein kinase pathways in breast cancer cell lines exposed to gold nanoparticles loaded with TNF-α and combined with doxorubicin
  67. Effect of PVA fibers on durability of nano-SiO2-reinforced cement-based composites subjected to wet-thermal and chloride salt-coupled environment
  68. Effect of polyvinyl alcohol fibers on mechanical properties of nano-SiO2-reinforced geopolymer composites under a complex environment
  69. In vitro studies of titanium dioxide nanoparticles modified with glutathione as a potential drug delivery system
  70. Comparative investigations of Ag/H2O nanofluid and Ag-CuO/H2O hybrid nanofluid with Darcy-Forchheimer flow over a curved surface
  71. Study on deformation characteristics of multi-pass continuous drawing of micro copper wire based on crystal plasticity finite element method
  72. Properties of ultra-high-performance self-compacting fiber-reinforced concrete modified with nanomaterials
  73. Prediction of lap shear strength of GNP and TiO2/epoxy nanocomposite adhesives
  74. A novel exploration of how localized magnetic field affects vortex generation of trihybrid nanofluids
  75. Fabrication and physicochemical characterization of copper oxide–pyrrhotite nanocomposites for the cytotoxic effects on HepG2 cells and the mechanism
  76. Thermal radiative flow of cross nanofluid due to a stretched cylinder containing microorganisms
  77. In vitro study of the biphasic calcium phosphate/chitosan hybrid biomaterial scaffold fabricated via solvent casting and evaporation technique for bone regeneration
  78. Insights into the thermal characteristics and dynamics of stagnant blood conveying titanium oxide, alumina, and silver nanoparticles subject to Lorentz force and internal heating over a curved surface
  79. Effects of nano-SiO2 additives on carbon fiber-reinforced fly ash–slag geopolymer composites performance: Workability, mechanical properties, and microstructure
  80. Energy bandgap and thermal characteristics of non-Darcian MHD rotating hybridity nanofluid thin film flow: Nanotechnology application
  81. Green synthesis and characterization of ginger-extract-based oxali-palladium nanoparticles for colorectal cancer: Downregulation of REG4 and apoptosis induction
  82. Abnormal evolution of resistivity and microstructure of annealed Ag nanoparticles/Ag–Mo films
  83. Preparation of water-based dextran-coated Fe3O4 magnetic fluid for magnetic hyperthermia
  84. Statistical investigations and morphological aspects of cross-rheological material suspended in transportation of alumina, silica, titanium, and ethylene glycol via the Galerkin algorithm
  85. Effect of CNT film interleaves on the flexural properties and strength after impact of CFRP composites
  86. Self-assembled nanoscale entities: Preparative process optimization, payload release, and enhanced bioavailability of thymoquinone natural product
  87. Structure–mechanical property relationships of 3D-printed porous polydimethylsiloxane films
  88. Nonlinear thermal radiation and the slip effect on a 3D bioconvection flow of the Casson nanofluid in a rotating frame via a homotopy analysis mechanism
  89. Residual mechanical properties of concrete incorporated with nano supplementary cementitious materials exposed to elevated temperature
  90. Time-independent three-dimensional flow of a water-based hybrid nanofluid past a Riga plate with slips and convective conditions: A homotopic solution
  91. Lightweight and high-strength polyarylene ether nitrile-based composites for efficient electromagnetic interference shielding
  92. Review Articles
  93. Recycling waste sources into nanocomposites of graphene materials: Overview from an energy-focused perspective
  94. Hybrid nanofiller reinforcement in thermoset and biothermoset applications: A review
  95. Current state-of-the-art review of nanotechnology-based therapeutics for viral pandemics: Special attention to COVID-19
  96. Solid lipid nanoparticles for targeted natural and synthetic drugs delivery in high-incidence cancers, and other diseases: Roles of preparation methods, lipid composition, transitional stability, and release profiles in nanocarriers’ development
  97. Critical review on experimental and theoretical studies of elastic properties of wurtzite-structured ZnO nanowires
  98. Polyurea micro-/nano-capsule applications in construction industry: A review
  99. A comprehensive review and clinical guide to molecular and serological diagnostic tests and future development: In vitro diagnostic testing for COVID-19
  100. Recent advances in electrocatalytic oxidation of 5-hydroxymethylfurfural to 2,5-furandicarboxylic acid: Mechanism, catalyst, coupling system
  101. Research progress and prospect of silica-based polymer nanofluids in enhanced oil recovery
  102. Review of the pharmacokinetics of nanodrugs
  103. Engineered nanoflowers, nanotrees, nanostars, nanodendrites, and nanoleaves for biomedical applications
  104. Research progress of biopolymers combined with stem cells in the repair of intrauterine adhesions
  105. Progress in FEM modeling on mechanical and electromechanical properties of carbon nanotube cement-based composites
  106. Antifouling induced by surface wettability of poly(dimethyl siloxane) and its nanocomposites
  107. TiO2 aerogel composite high-efficiency photocatalysts for environmental treatment and hydrogen energy production
  108. Structural properties of alumina surfaces and their roles in the synthesis of environmentally persistent free radicals (EPFRs)
  109. Nanoparticles for the potential treatment of Alzheimer’s disease: A physiopathological approach
  110. Current status of synthesis and consolidation strategies for thermo-resistant nanoalloys and their general applications
  111. Recent research progress on the stimuli-responsive smart membrane: A review
  112. Dispersion of carbon nanotubes in aqueous cementitious materials: A review
  113. Applications of DNA tetrahedron nanostructure in cancer diagnosis and anticancer drugs delivery
  114. Magnetic nanoparticles in 3D-printed scaffolds for biomedical applications
  115. An overview of the synthesis of silicon carbide–boron carbide composite powders
  116. Organolead halide perovskites: Synthetic routes, structural features, and their potential in the development of photovoltaic
  117. Recent advancements in nanotechnology application on wood and bamboo materials: A review
  118. Application of aptamer-functionalized nanomaterials in molecular imaging of tumors
  119. Recent progress on corrosion mechanisms of graphene-reinforced metal matrix composites
  120. Research progress on preparation, modification, and application of phenolic aerogel
  121. Application of nanomaterials in early diagnosis of cancer
  122. Plant mediated-green synthesis of zinc oxide nanoparticles: An insight into biomedical applications
  123. Recent developments in terahertz quantum cascade lasers for practical applications
  124. Recent progress in dielectric/metal/dielectric electrodes for foldable light-emitting devices
  125. Nanocoatings for ballistic applications: A review
  126. A mini-review on MoS2 membrane for water desalination: Recent development and challenges
  127. Recent updates in nanotechnological advances for wound healing: A narrative review
  128. Recent advances in DNA nanomaterials for cancer diagnosis and treatment
  129. Electrochemical micro- and nanobiosensors for in vivo reactive oxygen/nitrogen species measurement in the brain
  130. Advances in organic–inorganic nanocomposites for cancer imaging and therapy
  131. Advancements in aluminum matrix composites reinforced with carbides and graphene: A comprehensive review
  132. Modification effects of nanosilica on asphalt binders: A review
  133. Decellularized extracellular matrix as a promising biomaterial for musculoskeletal tissue regeneration
  134. Review of the sol–gel method in preparing nano TiO2 for advanced oxidation process
  135. Micro/nano manufacturing aircraft surface with anti-icing and deicing performances: An overview
  136. Cell type-targeting nanoparticles in treating central nervous system diseases: Challenges and hopes
  137. An overview of hydrogen production from Al-based materials
  138. A review of application, modification, and prospect of melamine foam
  139. A review of the performance of fibre-reinforced composite laminates with carbon nanotubes
  140. Research on AFM tip-related nanofabrication of two-dimensional materials
  141. Advances in phase change building materials: An overview
  142. Development of graphene and graphene quantum dots toward biomedical engineering applications: A review
  143. Nanoremediation approaches for the mitigation of heavy metal contamination in vegetables: An overview
  144. Photodynamic therapy empowered by nanotechnology for oral and dental science: Progress and perspectives
  145. Biosynthesis of metal nanoparticles: Bioreduction and biomineralization
  146. Current diagnostic and therapeutic approaches for severe acute respiratory syndrome coronavirus-2 (SARS-COV-2) and the role of nanomaterial-based theragnosis in combating the pandemic
  147. Application of two-dimensional black phosphorus material in wound healing
  148. Special Issue on Advanced Nanomaterials and Composites for Energy Conversion and Storage - Part I
  149. Helical fluorinated carbon nanotubes/iron(iii) fluoride hybrid with multilevel transportation channels and rich active sites for lithium/fluorinated carbon primary battery
  150. The progress of cathode materials in aqueous zinc-ion batteries
  151. Special Issue on Advanced Nanomaterials for Carbon Capture, Environment and Utilization for Energy Sustainability - Part I
  152. Effect of polypropylene fiber and nano-silica on the compressive strength and frost resistance of recycled brick aggregate concrete
  153. Mechanochemical design of nanomaterials for catalytic applications with a benign-by-design focus
https://doi.org/10.1515/ntrev-2023-0576
Schlagwörter für diesen Artikel
recycled brick aggregate; nano-SiO2; mechanical property; frost resistance; microstructure; life prediction model
Creative Commons
BY 4.0

Artikel in diesem Heft

  1. Research Articles
  2. Preparation of CdS–Ag2S nanocomposites by ultrasound-assisted UV photolysis treatment and its visible light photocatalysis activity
  3. Significance of nanoparticle radius and inter-particle spacing toward the radiative water-based alumina nanofluid flow over a rotating disk
  4. Aptamer-based detection of serotonin based on the rapid in situ synthesis of colorimetric gold nanoparticles
  5. Investigation of the nucleation and growth behavior of Ti2AlC and Ti3AlC nano-precipitates in TiAl alloys
  6. Dynamic recrystallization behavior and nucleation mechanism of dual-scale SiCp/A356 composites processed by P/M method
  7. High mechanical performance of 3-aminopropyl triethoxy silane/epoxy cured in a sandwich construction of 3D carbon felts foam and woven basalt fibers
  8. Applying solution of spray polyurea elastomer in asphalt binder: Feasibility analysis and DSR study based on the MSCR and LAS tests
  9. Study on the chronic toxicity and carcinogenicity of iron-based bioabsorbable stents
  10. Influence of microalloying with B on the microstructure and properties of brazed joints with Ag–Cu–Zn–Sn filler metal
  11. Thermohydraulic performance of thermal system integrated with twisted turbulator inserts using ternary hybrid nanofluids
  12. Study of mechanical properties of epoxy/graphene and epoxy/halloysite nanocomposites
  13. Effects of CaO addition on the CuW composite containing micro- and nano-sized tungsten particles synthesized via aluminothermic coupling with silicothermic reduction
  14. Cu and Al2O3-based hybrid nanofluid flow through a porous cavity
  15. Design of functional vancomycin-embedded bio-derived extracellular matrix hydrogels for repairing infectious bone defects
  16. Study on nanocrystalline coating prepared by electro-spraying 316L metal wire and its corrosion performance
  17. Axial compression performance of CFST columns reinforced by ultra-high-performance nano-concrete under long-term loading
  18. Tungsten trioxide nanocomposite for conventional soliton and noise-like pulse generation in anomalous dispersion laser cavity
  19. Microstructure and electrical contact behavior of the nano-yttria-modified Cu-Al2O3/30Mo/3SiC composite
  20. Melting rheology in thermally stratified graphene-mineral oil reservoir (third-grade nanofluid) with slip condition
  21. Re-examination of nonlinear vibration and nonlinear bending of porous sandwich cylindrical panels reinforced by graphene platelets
  22. Parametric simulation of hybrid nanofluid flow consisting of cobalt ferrite nanoparticles with second-order slip and variable viscosity over an extending surface
  23. Chitosan-capped silver nanoparticles with potent and selective intrinsic activity against the breast cancer cells
  24. Multi-core/shell SiO2@Al2O3 nanostructures deposited on Ti3AlC2 to enhance high-temperature stability and microwave absorption properties
  25. Solution-processed Bi2S3/BiVO4/TiO2 ternary heterojunction photoanode with enhanced photoelectrochemical performance
  26. Electroporation effect of ZnO nanoarrays under low voltage for water disinfection
  27. NIR-II window absorbing graphene oxide-coated gold nanorods and graphene quantum dot-coupled gold nanorods for photothermal cancer therapy
  28. Nonlinear three-dimensional stability characteristics of geometrically imperfect nanoshells under axial compression and surface residual stress
  29. Investigation of different nanoparticles properties on the thermal conductivity and viscosity of nanofluids by molecular dynamics simulation
  30. Optimized Cu2O-{100} facet for generation of different reactive oxidative species via peroxymonosulfate activation at specific pH values to efficient acetaminophen removal
  31. Brownian and thermal diffusivity impact due to the Maxwell nanofluid (graphene/engine oil) flow with motile microorganisms and Joule heating
  32. Appraising the dielectric properties and the effectiveness of electromagnetic shielding of graphene reinforced silicone rubber nanocomposite
  33. Synthesis of Ag and Cu nanoparticles by plasma discharge in inorganic salt solutions
  34. Low-cost and large-scale preparation of ultrafine TiO2@C hybrids for high-performance degradation of methyl orange and formaldehyde under visible light
  35. Utilization of waste glass with natural pozzolan in the production of self-glazed glass-ceramic materials
  36. Mechanical performance of date palm fiber-reinforced concrete modified with nano-activated carbon
  37. Melting point of dried gold nanoparticles prepared with ultrasonic spray pyrolysis and lyophilisation
  38. Graphene nanofibers: A modern approach towards tailored gypsum composites
  39. Role of localized magnetic field in vortex generation in tri-hybrid nanofluid flow: A numerical approach
  40. Intelligent computing for the double-diffusive peristaltic rheology of magneto couple stress nanomaterials
  41. Bioconvection transport of upper convected Maxwell nanoliquid with gyrotactic microorganism, nonlinear thermal radiation, and chemical reaction
  42. 3D printing of porous Ti6Al4V bone tissue engineering scaffold and surface anodization preparation of nanotubes to enhance its biological property
  43. Bioinspired ferromagnetic CoFe2O4 nanoparticles: Potential pharmaceutical and medical applications
  44. Significance of gyrotactic microorganisms on the MHD tangent hyperbolic nanofluid flow across an elastic slender surface: Numerical analysis
  45. Performance of polycarboxylate superplasticisers in seawater-blended cement: Effect from chemical structure and nano modification
  46. Entropy minimization of GO–Ag/KO cross-hybrid nanofluid over a convectively heated surface
  47. Oxygen plasma assisted room temperature bonding for manufacturing SU-8 polymer micro/nanoscale nozzle
  48. Performance and mechanism of CO2 reduction by DBD-coupled mesoporous SiO2
  49. Polyarylene ether nitrile dielectric films modified by HNTs@PDA hybrids for high-temperature resistant organic electronics field
  50. Exploration of generalized two-phase free convection magnetohydrodynamic flow of dusty tetra-hybrid Casson nanofluid between parallel microplates
  51. Hygrothermal bending analysis of sandwich nanoplates with FG porous core and piezomagnetic faces via nonlocal strain gradient theory
  52. Design and optimization of a TiO2/RGO-supported epoxy multilayer microwave absorber by the modified local best particle swarm optimization algorithm
  53. Mechanical properties and frost resistance of recycled brick aggregate concrete modified by nano-SiO2
  54. Self-template synthesis of hollow flower-like NiCo2O4 nanoparticles as an efficient bifunctional catalyst for oxygen reduction and oxygen evolution in alkaline media
  55. High-performance wearable flexible strain sensors based on an AgNWs/rGO/TPU electrospun nanofiber film for monitoring human activities
  56. High-performance lithium–selenium batteries enabled by nitrogen-doped porous carbon from peanut meal
  57. Investigating effects of Lorentz forces and convective heating on ternary hybrid nanofluid flow over a curved surface using homotopy analysis method
  58. Exploring the potential of biogenic magnesium oxide nanoparticles for cytotoxicity: In vitro and in silico studies on HCT116 and HT29 cells and DPPH radical scavenging
  59. Enhanced visible-light-driven photocatalytic degradation of azo dyes by heteroatom-doped nickel tungstate nanoparticles
  60. A facile method to synthesize nZVI-doped polypyrrole-based carbon nanotube for Ag(i) removal
  61. Improved osseointegration of dental titanium implants by TiO2 nanotube arrays with self-assembled recombinant IGF-1 in type 2 diabetes mellitus rat model
  62. Functionalized SWCNTs@Ag–TiO2 nanocomposites induce ROS-mediated apoptosis and autophagy in liver cancer cells
  63. Triboelectric nanogenerator based on a water droplet spring with a concave spherical surface for harvesting wave energy and detecting pressure
  64. A mathematical approach for modeling the blood flow containing nanoparticles by employing the Buongiorno’s model
  65. Molecular dynamics study on dynamic interlayer friction of graphene and its strain effect
  66. Induction of apoptosis and autophagy via regulation of AKT and JNK mitogen-activated protein kinase pathways in breast cancer cell lines exposed to gold nanoparticles loaded with TNF-α and combined with doxorubicin
  67. Effect of PVA fibers on durability of nano-SiO2-reinforced cement-based composites subjected to wet-thermal and chloride salt-coupled environment
  68. Effect of polyvinyl alcohol fibers on mechanical properties of nano-SiO2-reinforced geopolymer composites under a complex environment
  69. In vitro studies of titanium dioxide nanoparticles modified with glutathione as a potential drug delivery system
  70. Comparative investigations of Ag/H2O nanofluid and Ag-CuO/H2O hybrid nanofluid with Darcy-Forchheimer flow over a curved surface
  71. Study on deformation characteristics of multi-pass continuous drawing of micro copper wire based on crystal plasticity finite element method
  72. Properties of ultra-high-performance self-compacting fiber-reinforced concrete modified with nanomaterials
  73. Prediction of lap shear strength of GNP and TiO2/epoxy nanocomposite adhesives
  74. A novel exploration of how localized magnetic field affects vortex generation of trihybrid nanofluids
  75. Fabrication and physicochemical characterization of copper oxide–pyrrhotite nanocomposites for the cytotoxic effects on HepG2 cells and the mechanism
  76. Thermal radiative flow of cross nanofluid due to a stretched cylinder containing microorganisms
  77. In vitro study of the biphasic calcium phosphate/chitosan hybrid biomaterial scaffold fabricated via solvent casting and evaporation technique for bone regeneration
  78. Insights into the thermal characteristics and dynamics of stagnant blood conveying titanium oxide, alumina, and silver nanoparticles subject to Lorentz force and internal heating over a curved surface
  79. Effects of nano-SiO2 additives on carbon fiber-reinforced fly ash–slag geopolymer composites performance: Workability, mechanical properties, and microstructure
  80. Energy bandgap and thermal characteristics of non-Darcian MHD rotating hybridity nanofluid thin film flow: Nanotechnology application
  81. Green synthesis and characterization of ginger-extract-based oxali-palladium nanoparticles for colorectal cancer: Downregulation of REG4 and apoptosis induction
  82. Abnormal evolution of resistivity and microstructure of annealed Ag nanoparticles/Ag–Mo films
  83. Preparation of water-based dextran-coated Fe3O4 magnetic fluid for magnetic hyperthermia
  84. Statistical investigations and morphological aspects of cross-rheological material suspended in transportation of alumina, silica, titanium, and ethylene glycol via the Galerkin algorithm
  85. Effect of CNT film interleaves on the flexural properties and strength after impact of CFRP composites
  86. Self-assembled nanoscale entities: Preparative process optimization, payload release, and enhanced bioavailability of thymoquinone natural product
  87. Structure–mechanical property relationships of 3D-printed porous polydimethylsiloxane films
  88. Nonlinear thermal radiation and the slip effect on a 3D bioconvection flow of the Casson nanofluid in a rotating frame via a homotopy analysis mechanism
  89. Residual mechanical properties of concrete incorporated with nano supplementary cementitious materials exposed to elevated temperature
  90. Time-independent three-dimensional flow of a water-based hybrid nanofluid past a Riga plate with slips and convective conditions: A homotopic solution
  91. Lightweight and high-strength polyarylene ether nitrile-based composites for efficient electromagnetic interference shielding
  92. Review Articles
  93. Recycling waste sources into nanocomposites of graphene materials: Overview from an energy-focused perspective
  94. Hybrid nanofiller reinforcement in thermoset and biothermoset applications: A review
  95. Current state-of-the-art review of nanotechnology-based therapeutics for viral pandemics: Special attention to COVID-19
  96. Solid lipid nanoparticles for targeted natural and synthetic drugs delivery in high-incidence cancers, and other diseases: Roles of preparation methods, lipid composition, transitional stability, and release profiles in nanocarriers’ development
  97. Critical review on experimental and theoretical studies of elastic properties of wurtzite-structured ZnO nanowires
  98. Polyurea micro-/nano-capsule applications in construction industry: A review
  99. A comprehensive review and clinical guide to molecular and serological diagnostic tests and future development: In vitro diagnostic testing for COVID-19
  100. Recent advances in electrocatalytic oxidation of 5-hydroxymethylfurfural to 2,5-furandicarboxylic acid: Mechanism, catalyst, coupling system
  101. Research progress and prospect of silica-based polymer nanofluids in enhanced oil recovery
  102. Review of the pharmacokinetics of nanodrugs
  103. Engineered nanoflowers, nanotrees, nanostars, nanodendrites, and nanoleaves for biomedical applications
  104. Research progress of biopolymers combined with stem cells in the repair of intrauterine adhesions
  105. Progress in FEM modeling on mechanical and electromechanical properties of carbon nanotube cement-based composites
  106. Antifouling induced by surface wettability of poly(dimethyl siloxane) and its nanocomposites
  107. TiO2 aerogel composite high-efficiency photocatalysts for environmental treatment and hydrogen energy production
  108. Structural properties of alumina surfaces and their roles in the synthesis of environmentally persistent free radicals (EPFRs)
  109. Nanoparticles for the potential treatment of Alzheimer’s disease: A physiopathological approach
  110. Current status of synthesis and consolidation strategies for thermo-resistant nanoalloys and their general applications
  111. Recent research progress on the stimuli-responsive smart membrane: A review
  112. Dispersion of carbon nanotubes in aqueous cementitious materials: A review
  113. Applications of DNA tetrahedron nanostructure in cancer diagnosis and anticancer drugs delivery
  114. Magnetic nanoparticles in 3D-printed scaffolds for biomedical applications
  115. An overview of the synthesis of silicon carbide–boron carbide composite powders
  116. Organolead halide perovskites: Synthetic routes, structural features, and their potential in the development of photovoltaic
  117. Recent advancements in nanotechnology application on wood and bamboo materials: A review
  118. Application of aptamer-functionalized nanomaterials in molecular imaging of tumors
  119. Recent progress on corrosion mechanisms of graphene-reinforced metal matrix composites
  120. Research progress on preparation, modification, and application of phenolic aerogel
  121. Application of nanomaterials in early diagnosis of cancer
  122. Plant mediated-green synthesis of zinc oxide nanoparticles: An insight into biomedical applications
  123. Recent developments in terahertz quantum cascade lasers for practical applications
  124. Recent progress in dielectric/metal/dielectric electrodes for foldable light-emitting devices
  125. Nanocoatings for ballistic applications: A review
  126. A mini-review on MoS2 membrane for water desalination: Recent development and challenges
  127. Recent updates in nanotechnological advances for wound healing: A narrative review
  128. Recent advances in DNA nanomaterials for cancer diagnosis and treatment
  129. Electrochemical micro- and nanobiosensors for in vivo reactive oxygen/nitrogen species measurement in the brain
  130. Advances in organic–inorganic nanocomposites for cancer imaging and therapy
  131. Advancements in aluminum matrix composites reinforced with carbides and graphene: A comprehensive review
  132. Modification effects of nanosilica on asphalt binders: A review
  133. Decellularized extracellular matrix as a promising biomaterial for musculoskeletal tissue regeneration
  134. Review of the sol–gel method in preparing nano TiO2 for advanced oxidation process
  135. Micro/nano manufacturing aircraft surface with anti-icing and deicing performances: An overview
  136. Cell type-targeting nanoparticles in treating central nervous system diseases: Challenges and hopes
  137. An overview of hydrogen production from Al-based materials
  138. A review of application, modification, and prospect of melamine foam
  139. A review of the performance of fibre-reinforced composite laminates with carbon nanotubes
  140. Research on AFM tip-related nanofabrication of two-dimensional materials
  141. Advances in phase change building materials: An overview
  142. Development of graphene and graphene quantum dots toward biomedical engineering applications: A review
  143. Nanoremediation approaches for the mitigation of heavy metal contamination in vegetables: An overview
  144. Photodynamic therapy empowered by nanotechnology for oral and dental science: Progress and perspectives
  145. Biosynthesis of metal nanoparticles: Bioreduction and biomineralization
  146. Current diagnostic and therapeutic approaches for severe acute respiratory syndrome coronavirus-2 (SARS-COV-2) and the role of nanomaterial-based theragnosis in combating the pandemic
  147. Application of two-dimensional black phosphorus material in wound healing
  148. Special Issue on Advanced Nanomaterials and Composites for Energy Conversion and Storage - Part I
  149. Helical fluorinated carbon nanotubes/iron(iii) fluoride hybrid with multilevel transportation channels and rich active sites for lithium/fluorinated carbon primary battery
  150. The progress of cathode materials in aqueous zinc-ion batteries
  151. Special Issue on Advanced Nanomaterials for Carbon Capture, Environment and Utilization for Energy Sustainability - Part I
  152. Effect of polypropylene fiber and nano-silica on the compressive strength and frost resistance of recycled brick aggregate concrete
  153. Mechanochemical design of nanomaterials for catalytic applications with a benign-by-design focus
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