Since the 1970s and 1980s, ultrafine forms of silica SiO₂, such as microsilica and nanosilica, have been actively integrated into concrete technology. There are four primary types of amorphous silica available in the global market: precipitated silica (white soot), silica gel (dried silica gel), pyrogenic silica, and microsilica. The worldwide consumption of all synthetic silica types amounts to approximately 1 million tonnes ^{[1][2][3][4][5]}[1,2,3,4,5].

Microsilica, a by-product of silicon or ferrosilicon production, presents as amorphous silica (SiO₂) in spherical particle form ^{[1][2][3][4][5][6][7][8][9][10]}[1,2,3,4,5,6,7,8,9,10]. Widely utilized within the construction industry, microsilica serves as a modifying component in concrete production, leveraging its chemical composition and physical attributes as a highly active pozzolan ^{[10][11][12][13][14][15][16][17][18][19][20][21][22][23][24][25]}[10,11,12,13,14,15,16,17,18,19,20,21,22,23,24,25]. The extensive introduction of various highly effective chemical and mineral additives has led to significant advancements in modern concrete technology.

It is acknowledged [25] that the incorporation of mineral fillers in concrete mixtures stands as a priority for reducing cement consumption and enhancing both its technological and operational properties. Natural additives encompass crushed volcanic and sedimentary rocks, diatomites, volcanic ash, and tuff. Within technogenic additives lie waste or by-products from various industries, such as fly ash, granulated blast furnace slag, and microsilica ^{[25][26][27][28][29]}[25,26,27,28,29]. Microsilica emerges as one of the most potent and finely dispersed mineral additives. Its substantial specific surface area and amorphous structure endow it with high pozzolanic activity, functioning as an effective microfiller. The utilization of microsilica as a mineral additive proves a promising method for generating concrete with high-performance characteristics ^[25][26][25,26].

Wastes from ferroalloy production contain an elevated SiO₂ content ranging from 85% to 95%, with a reduced content down to 65–75%. The specific surface area of microsilica ranges from 15,000 to 25,000 m²/kg, significantly surpassing the specific surface area of Portland cement, which stands at 300 to 400 m²/kg. Exhibiting high pozzolanic activity, microsilica operates effectively as a microfiller ^{[30][31][32][33][34][35][36][37][38][39][40][41][42][43][44][45][46][47][48][49]}[30,31,32,33,34,35,36,37,38,39,40,41,42,43,44,45,46,47,48,49]. The development of a cementitious structure in the presence of microsilica relies on microfilling and pozzolanic effects. Furthermore, these particles serve as crystallization centers, amplifying the cement’s early-age hydration and increasing the packing density of the hydrate phases.

During cement hydration, the release of calcium hydroxide allows SiO₂ to interact due to its high pozzolanic activity. This reaction leads to the formation of highly dispersed, low-basic calcium hydrosilicates C-S-H (I) instead of portlandite crystals Ca(OH)₂, significantly enhancing the properties of the cement structure. This transformation reduces the presence of capillary pores, compacting the structure and decreasing cement stone permeability, thereby boosting its resistance to aggressive environments and overall durability ^{[23][34][45][46]}[23,34,45,46]. Concrete mixtures containing microsilica exhibit increased thixotropy, viscosity, and resistance to delamination due to their high water-holding capacity ^{[10][22][34][50][51]}[10,22,34,50,51]. However, the use of microsilica, due to its high specific surface area, significantly increases the water demand for concrete mixtures. It is estimated that 1 kg of microsilica raises the water requirement of a concrete mixture by 1 L [50]. Consequently, under conditions of uniform mobility of concrete mixtures, the use of microsilica exhibits an insignificant strength effect and proves ineffective ^{[11][12][13][14][15][16][17]}[11,12,13,14,15,16,17]. To mitigate this, plasticizing additives are necessary to reduce water demand in concrete mixtures and enhance the efficacy of microsilica as a plasticizer.

Recent reviews ^[2][3][2,3] have meticulously explored ultrafine mineral compounds with minimal silica content, examining the addition of microsilica to concrete mixtures to advance concrete technologies. Concrete remains a cornerstone material in construction, with its demand escalating annually ^[4][5][4,5]. Ordinary Portland cement (OPC) is a crucial component contributing significantly to greenhouse gas emissions ^{[10][11][12][13]}[10,11,12,13]. OPC production accounts for around 5–8% of global CO₂ emissions ^{[8][9][10][11]}[8,9,10,11]. Cement usage surpasses 4000 million tons annually and is projected to reach approximately 6000 million tons by 2060 ^[12][13][12,13], greatly contributing to climate change through greenhouse gas emissions ^[13][14][15][13,14,15]. To address this, agricultural and industrial wastes, such as rice husk ash (RHA), sugarcane bagasse ash, and olive oil ash, are utilized to partially substitute OPC in the production of green concrete ^{[16][17][18][19][20][21]}[16,17,18,19,20,21].

Reviews ^[22][23][22,23] that analyzed studies involving micro- and nanosilica in construction demonstrate their use alongside fly ash and other microparticles to enhance the compactness, strength, and durability of cementitious materials. A scientometric analysis in [22] evaluated the keywords prevalent in nanostructured (NS)-modified concrete studies, listing the 20 most frequently used terms (Table 1). Nanosilica, microsilica, compressive strength, concrete, and cement emerged as the top five terms consistently employed in this field of research.

Various minerals and chemicals have been utilized in the production of amorphous silica, with quartz sand standing as the most commonly used raw material containing silica. The methods for processing and obtaining finalized raw materials involve multi-stage and intricate processes employing expensive reagents and complex equipment ^{[30][31][32][33][34][35][36][37][38][40][41]}[30,31,32,33,34,35,36,37,38,40,41]. The primary industrial source for producing silicon dioxide involves the creation of a silicate block through the fusion of sand with sodium hydroxide at a temperature of 1700 °C. This block is then subjected to boiling in an autoclave under a pressure of 4.8–5.0 atm. while being supplied with steam ^[30][31][30,31].

Amorphous silicon dioxide with minimal metal impurities (less than 10⁻³–10⁻⁵ wt.%) is formed by sintering quartz foundry sands with ammonium hydrodifluoride (NH₄HF₂) ^{[33][34][35][36]}[33,34,35,36]. Additionally, amorphous silicon dioxide (white soot, 99.997% purity) can be derived from processing zirconium concentrate. This involves fluorination with ammonium bifluoride, heat treatment, subsequent condensation, and processing of the resulting halogenation products ^[30][31][30,31]. A patent search conducted in the library of patents for inventions of the Russian Federation FIPS (Federal Institute of Industrial Property) revealed that most inventions focus on the complex processing of raw materials. Starting materials such as serpentinite, marshalite, diatomite ^[9][10][11][9,10,11], nepheline, eudialyte, olivine, and fayalite ^[33][34][35][33,34,35] have been employed.

An established method for producing environmentally friendly precipitated silica involves neutralizing sodium silicate with sulfuric acid [13]. Recently, waste from various industries has piqued researchers’ interest as a source of Si. For instance, amorphous silicon dioxide can be extracted from waste generated in boron production, ash resulting from the combustion of organic fuel, waste from ferroalloy production, and flue dust from the gas purification process in aluminum industry enterprises [28].

Processing ash and slag waste from low-grade ore and non-metallic raw materials can yield foamed X-ray amorphous material (foam silicate) with a consistent chemical composition, forming either thin mineral fibers or spheres based on technological conditions ^{[28][29][30][31][32][33][34][35][36][37][38][39][40]}[28,29,30,31,32,33,34,35,36,37,38,39,40]. Research ^{[28][38][40][41]}[28,38,40,41] indicates that the economically efficient disposal of ash and slag waste on a large scale is feasible through the production of building materials and products. In an innovative approach, renewable silicophilic plants like rice, horsetails, feather grass, and oats can serve as an alternative raw material source ^[23][24][23,24]. Among these, rice production waste, specifically rice husks and rice straw, holds promise due to their high silica content: 14%–20% in rice husks and up to 13.5% in rice straw. The processing methods are straightforward and cost-effective, favoring the extraction of silica from rice straw because of its higher silicon content. Rice husks, concentrated during grain cleaning in mills, offer a more economical processing route ^[25][26][25,26].

A review [24] explored the use of rice husk ash as a cement substitute in high-strength sustainable concretes. In this context, the focus revolves around micro- and nanosilica derived from industrial waste.

2. General Understanding of the Hydration Processes of Portland Cement

Through the gradual evolution of scientific research methods and the culmination of numerous experimental and theoretical studies, a comprehensive comprehension of the hydration processes of Portland cement has been achieved ^{[25][26][27][28][29]}[25,26,27,28,29]. The primary mineral within Portland cement clinker, tricalcium silicate 3CaO·SiO₂ (alite), comprises 60%–70% of the clinker content. Researchers commonly delineate five principal stages of hydration: the initial, induction, hydration acceleration, hydration deceleration, and hardening stages. In the initial stage, the interaction between tricalcium silicate and water leads to the adsorption of water molecules and partial surface hydration of the binder grain. This phase, lasting no more than 20 min, is marked by heat release. The adsorption of water molecules results in the protonation of the binder surface, forming HnSiO₄ⁿ⁺⁴ hydrosilicate groups and releasing Ca²⁺ and OH⁻ ions into the liquid phase. Simultaneously, a semi-permeable film of calcium hydrosilicates forms on the surface of the hydrating grains, facilitating the transmission of water to the clinker mineral’s surface and the release of Ca²⁺ and OH⁻ ions from it [25]. The second stage, known as the induction period, spans from two to six hours. During the fourth and fifth stages, the crystallization of gel-like calcium hydrosilicates occurs, resulting in the development of both an outer layer and an inner layer of hydrosilicate masses ^[28][29][28,29].

3. State of Production of Micro- and Nanosilica in the Russian Federation

Annually, during the production of metallurgical silicon in Russia (RF), approximately 35,000 tons of fine dust are generated, stored in “big bags” weighing 1 ton each, or maintained on slurry fields ^[27][28][40][27,28,40]. Consequently, this results in an escalation of waste, emphasizing the crucial need for recycling and large-scale utilization from both economic and environmental standpoints ^{[29][30][31][32][33][34][35]}[29,30,31,32,33,34,35]. The disposal and processing of dust are exclusively executed using extensive metallurgical equipment within sinter production. Only specially prepared waste can be reintegrated into metallurgical processes. Waste agglomeration not only supplies enterprises with supplementary resources but also diminishes their environmental impact ^[1][2][1,2]. Forecasts indicate a growth trend in microsilica production in Russia by 2025 [1]. The surge in production, reaching 70–80 thousand tons annually, is primarily attributed to the full operation of metallurgical silicon production, driven by a sharp 80% price hike. Notably, the most appealing method of processing microsilica waste, derived from the reduction smelting of quartzite, totaling 30–40 thousand tons per year, is centralized at enterprises such as JSC Kremniy (Irkutsk region) and JSC Ural Silicon (Kamensk-Uralsky) ^[28][40][28,40]. The selection of a plant relies on its geographical proximity. Further details are outlined in Table 2, offering a comparative assessment, focusing on the fundamental effects of microsilica sourced from various Russian plants and foreign plants [40]. Russia annually produces over 150 thousand tons of microsilica, with production volumes increasing each year. As per table data, it is evident that the chemical composition of Misrosilica (MK) in the presented list is nearly identical.

• MKS (Microsilica suspension): Suspension (paste) of condensed microsilica.
• Based on chemical composition and effectiveness, microsilica is further divided into two groups, designated as follows:
• MK65: Condensed microsilica containing at least 65% silica with an efficiency index of at least 90%.
• MK85: Condensed microsilica containing a minimum of 85% silica and an efficiency index of at least 105%.

Microsilica is recommended to be used in conjunction with plasticizing additives and, if required, other additives as per the Russian Standard (GOST) 24,211 and GOST R 56592. Its application is intended for the following: 1. Heavy, fine-grained, light, and cellular concrete, alongside mortars and dry mixes compliant with GOST 26633, GOST 25820, GOST 25485, GOST 28013, and GOST 31357. These materials are utilized in the construction and repair of load-bearing and enclosing structures for transportation, industrial, and civil engineering, including underground and hydraulic structures. 2. Complex organo-mineral modifiers in line with GOST R 56178, designed for the production of concrete, mortars, and dry mixes exhibiting high-performance properties. Microsilica is utilized in the production of the following:

• High-strength concretes and mortars with reduced permeability and enhanced corrosion resistance are applied in various construction types like industrial, civil, and transportation.
• Low-cement concretes and mortars that exhibit decreased exotherm.
• Concrete mixtures with enhanced technological properties, including high mobility and self-compacting features, along with a high degree of resistance to segregation.

6. Preparation of Nanosilica

As per contemporary understanding, large capillary pores serve as stress concentrators in cement stone. The stone’s strength is governed by porosity as long as the pore size surpasses the critical Griffiths crack size. It is a well-established fact that there exists an inverse relationship between porosity and the strength of cement stone. In theory, the maximum strength of cement stone can be achieved when capillary porosity approaches zero ^{[51][52][53][54][55][56][57][58][59][60][61][62][63][64][65][66][67][68]}[51,52,53,54,55,56,57,58,59,60,61,62,63,64,65,66,67,68]. Current trends in concrete technology are geared toward producing concrete with minimal capillary porosity. An essential requirement for this is to not just maintain balanced fractions of fine and coarse aggregates, but also to ensure that all solid components in the concrete mix form a continuous series spanning the entire range of particle sizes—from the smallest nanodispersed components to larger crushed stone pieces. The inclusion of ultrafine silica fillers, featuring particles of various sizes, holds significant importance. While the initial stride toward a new generation of high-quality concrete involved the use of microsilica, the subsequent step should involve integrating ultrafine silica into concrete mixes, characterized by primary particles even smaller than MS (Figure 6). Interest in materials like precipitated and colloidal SiO₂ is currently burgeoning and is already being practically applied in concrete technologies. In some instances, precipitated SiO₂ is integrated into the composition of RPC concretes alongside microsilica. This inclusion contributes to achieving compressive strength ranging from 200 to 800 MPa and flexural strength of up to 100 MPa ^{[55][56][57][58][59][60][61][62][63][64][65][66][67][68][69]}[55,56,57,58,59,60,61,62,63,64,65,66,67,68,69]. Aerosil, or fumed silica, is manufactured by burning tetrachlorosilane (SiCl₄) in a stream of hydrogen and oxygen: The resulting nanosilica boasts higher dispersion (with particle sizes between 7 and 20 nm) and a specific surface area of approximately 200 m²/g more compared to MS. It also maintains a high degree of purity. Aerosil primarily serves as a filler and curing accelerator in silicone sealants and adhesives. Among all the types of industry-produced ultrafine SiO₂, aerosil stands out as the most costly. The raw materials for precipitated and colloidal SiO₂, known as hydrochemical silica, originate from aqueous solutions of sodium silicates (liquid glasses). When these solutions undergo acidification, nanodispersed SiO₂ particles are initially formed (Figure 7a). The fate of these particles relies on various process conditions such as solution concentration, pH, temperature, the presence of electrolyte salts, and multiply charged cations. In the absence of electrolytes and after undergoing specific stabilization in highly diluted conditions, primary SiO₂ particles can be enlarged to 10–50 nm by reprecipitating the substance from smaller to larger particles. This process simultaneously raises the SiO₂ concentration to 30–50 wt.% while preventing particle aggregation. Under these conditions, stable, concentrated dispersions of colloidal silica, also referred to as silica sol, are produced (Figure 8). In industrial processes to produce SiO₂ sols, liquid glass is diluted to a SiO₂ concentration of 3–5 wt.% and subsequently neutralized by passing it through a column packed with a cation exchanger in the H⁺ form. A small amount of alkali is added at the outlet to stabilize the particles. The solution is then concentrated by a process involving evaporation combined with sol growth. This operation includes introducing the solution after passing it through the ion exchanger (feeder sol) into the main sol. This allows the introduced silica to reprecipitate onto larger particles (Figure 9). The precipitated silica is filtered and washed with water on filter presses to eliminate salt, and then redissolved and fed as a suspension to a spray dryer (Figure 10). In cases where silicate solutions are acidified to a weakly alkaline medium without removing electrolyte products, for instance, Na₂SO₄ if the acidification is performed with sulfuric acid, the resulting SiO₂ particles grow to 2–5 nm and coagulate to form loose aggregates that lack sintering (Figure 11). This amorphous silica powder, technically known as chemically precipitated SiO₂, is an ultra-fine white powder used as a filler in the production of polymeric materials and in the tire, rubber, and light industries. In Russia, it is produced under the brand name “white carbon black”. For comparison, Table 5 displays the properties of silica produced by well-known global manufacturers, obtained via high-temperature synthetic conditions and hydrochemical methods.

7. Study of Promising Methods for Processing and Recycling Waste Micro- and Nanosilica for Their Possible Use in Refractory Materials and Concrete Mixtures

The three primary properties of concrete are workability, strength, and durability. While strength and durability are typically associated with hardened concrete, and workability pertains to fresh concrete, the properties of hardened concrete directly link to mix design and fresh concrete characteristics. In essence, the mix design and the properties of fresh concrete serve as the most crucial factors controlling the mechanical performance of hardened concrete. In reference [46], the impact of silica fume dosage on the water requirement, maintaining constant segregation, is illustrated, confirming the efficacy of the superplasticizer as a water reducer regardless of the silica fume content. The outcomes depicted in Figure 12 reveal that replacing up to 10% of the cement can enhance the workability of concrete. When combined with a superplasticizer, silica fume aids in dispersing the flocculated cement particles. Braulio, M.A.L. et al. and Cheol, MinYoon ^[51][52][51,52], demonstrated that silica fume concrete exhibited strength comparable to that of concrete made from sulphate-resistant cement. However, no further progress was made in this direction. These studies were conducted amid stringent environmental standards for the metallurgical industry, predominantly concerning industrial gas purification, which incurs substantial costs, especially for multi-stage filtration systems ^[53][54][53,54]. The initial investigation into microsilica’s role as a hardener in concrete mixes took place in Norway [50]. Microsilica was regarded as another essential element in the binary oxide system, including spinel. As indicated in ^[51][55][51,55], in concrete materials containing Al₂O₃-MgO, microsilica stabilizes the volumetric expansion linked to spinel formation by creating low-melting-point phases in the Al₂O₃-CaO-SiO₂ system, such as anorthite (CaS₂) and helenite (Ca₂Al [AlSiO₇]). For products composed of a blend of alumina and spinel, silica fume mainly contributes to enhancing the flow coefficient due to its suitable morphology, thereby improving the processing of the final products. Over time, the compressive strength of the control concrete matches that of concrete with 10% and 20% silica fume [46]. Figure 13 illustrates that compressive strength generally increases as the w/(c + sf) ratio declines, emphasizing that the water and cementitious material ratio plays a more significant role than the introduction of microsilica. An analysis of the curves reveals that the optimal cement replacement with microsilica is around 10%–15%. In their work [53], the authors investigated the impact of introducing microsilica additives into aluminum–magnesium compositions. They noted that an increasing microsilica content led to higher volumetric expansion coefficients of spinel. Additionally, the study highlighted the considerable influence of microsilica on the development of CaO-Al₂O₃ phases. Compositions with minimal microsilica content (0 and 0.25 wt.%) exhibited notable changes in the sample’s linear dimensions due to the limited interaction between Al₂O₃ and SiO₂. This limited interaction also affected the reaction with CaO, maintaining conditions for CaO to form as a separate phase. Conversely, when microsilica was introduced, interactions among SiO₂-Al₂O₃-CaO led to the formation of low melting point phases, consequently reducing the linear expansion coefficient values. During CaO formation, higher linear dimension growth rates were observed, influenced by a diffusion mechanism limited by the rate of liquid phase formation. Structural analysis revealed the formation of acicular calcium oxide in the sample matrix, which, on the contrary, weakened it. On the other hand, the absence of microsilica in the mixture resulted in the formation of crystals directed inward toward the alumina filler, leading to a slower increase in the expansion coefficient. The role of microsilica in the formation of needle phases of alumina and spinel was also investigated in [56], considering variations in microsilica content from 0 to 1 wt.%. The obtained results were compared with those from the Al₂O₃-MgO system in [57]. The findings showed that even small amounts of silica significantly influenced the development of the calcium oxide grain structure in these oxide systems. This underscored the need to consider microstructural changes when developing refractory samples with enhanced properties. Mermerdaş, K. et al. [58] presented the experimental determination of the effects of steel fiber, granulated ash, lightweight filler, and varying microsilica content on the properties of a high-performance cementitious composite in its green and annealed states was conducted. The mixtures were prepared using 6 mm long steel microfibers at concentrations of 0%, 1%, and 2% of the total volume. Silica fume content ranged from 1% to 25% in the mixes. The results of the experiment indicated that the mechanical properties of HPCC and the shrinkage behavior improved with an increasing volume fraction of steel fibers. This study also demonstrated that the detrimental impact of artificial lightweight filler could be offset by the addition of microsilica. Furthermore, research Kuz’min, M.P. et al. [59] outlined calculations related to the enthalpy and Gibbs free energy in the direct reduction in silica with aluminum, showcasing the potential for producing silumins (Al-Si alloys) using amorphous microsilica. Additionally, this research identified the influence of alloying additions and impurities on the process of silicon reduction in the melt. A substantial body of scientific literature is dedicated to exploring concrete mixes containing microsilica. For instance, in [60], findings highlighted a significant correlation between the particle surface area increase and internal surface forces, suggesting a boost in concrete’s cohesive ability. This strengthening effect is in line with anticipated shrinkage values during the formation of concrete mix samples, supporting the notion of silica fume serving as a plasticizer. It appears that microsilica from silicon production, given a particular structure and polymorphism, can potentially perform a similar plasticizing function. When an external physical force, such as pumping, vibration, or tamping, is applied to the mix, the spherical microsilica particles act as a transmission mechanism, imparting greater mobility through sliding forces than ordinary concrete with a standard additive. A comprehensive exploration of this effect is detailed by Xu, W. et al. [61], where the introduction of microsilica leads to a decrease in the viscosity (plasticity) of the material with a slight increase in the shear strength coefficient for a wet concrete mix. An analysis outlined in another scientific paper [63] revealed that the structure and properties of mixes are influenced by the source of the microsilica, specifically the production to which this waste belongs. In general, the formation of products from concrete mixes is also affected by the form of the microsilica additive used, regardless of whether the powder is uncompacted or compacted, and the moisture content in suspension. Fumed silica, with high specific surface areas (typically 15,000–30,000 m²/kg), demands more moisture for mixing, a need that can be partially offset by additional procedures to alter the mix’s composition, such as reducing the fine particle content during screening [53]. Currently, silica fume concrete mixes are frequently developed using the selective particle packing method. This technique involves aggregating ultra-fine spherical particles into a total volume after sorting the mixture by size, thereby achieving a balance between small and large materials and reducing the need for additional water, which preserves the rheological properties of the concrete. Due to its higher degree of cohesion, silica fume-modified concrete is less prone to segregation than conventional concrete [62]. This reduced tendency to segregate is also advantageous in highly fluid mortars or pumpable concrete mixes. The inclusion of a small amount of silica fume into the mix for transportation acts as a pumping aid, enhancing the fluidity of the mix and providing excellent long-distance transport properties [63]. Another outcome of the cohesion effects is that concrete containing silica fume essentially retains moisture within the mix. The absence of water drainage also means that the emergence of flat shapes and structures, such as power fusion, can occur much earlier than with conventional concrete. This occurrence is influenced by increased shear resistance and a tendency toward gelation (solidification without stirring), evident in the higher rates of hardening in the form of a pozzolan. However, this so-called pure pozzolan is initiated by the presence of calcium hydroxide [64]. The necessary amount of calcium hydroxide is obtained via cement hydration, so the pozzolanic reaction is only possible after the cement has started reacting. The curing time for the modified concrete is almost comparable to that of the standard composition concrete. As the concrete solidifies, the chemical effect of the microsilica has a greater influence on the structure and properties of the concrete mix compared to the physical effect. Microsilica primarily reacts with calcium hydroxide to form calcium silicate hydrates (C-S-H). This enhances the binder content, which increases strength but reduces the mix’s permeability by compacting the concrete matrix [66]. Due to its significantly large specific surface area compared to the particle surface area of the primary matrix in the concrete mix, the high silica content determines its reactivity compared to other potential additives like ash, crushed and granulated slag, and alumina [28]. This observation can also be applied to the study of refractory materials. Some researchers have discovered ^[66][67][66,67] that heightened reactivity initially expedites the cement fraction’s hydration and paves the way for a substantial release of calcium hydroxide, subsequently reducing the interaction rate between mix components by a factor of 2. The study showcased that as microsilica reacts and forms calcium hydrates and silicates, they fill the voids and pores in the concrete, creating a dense packing between the cement grains and filler particles. The combined chemical and physical action on the mixed components results in its uniformity and density throughout the product’s volume. Primarily, this decreases the material’s porosity, which can be instrumental in the development of refractory modification technology using microsilica. Another study [68] revealed that a relatively porous interface rich in Portland cement encircles the filler particles in standard packaged concrete but is virtually absent when silica fume is introduced into the mix. Modified concrete generates less heat than standard Portland cement within the same curing time. This reduction occurs because the amount of cement within the mix is diminished, consequently reducing the overall heat generated in the initial stages. This is attributed to the fact that silica fume, added at a third of the cement level, begins reacting later than the release of calcium hydroxide and therefore does not generate as much heat as standard cement during its interaction and mixing. Studies by Glazev, M.V. et al. and Zimina, D.A. et al. ^[69][70][69,70] have demonstrated the sensitivity of microsilica-modified concrete to temperature fluctuations during its hardening process. Under low temperatures, there is a decrease in the rate of hydration and strength enhancement, whereas elevated temperatures result in a sharp increase in these properties. An analysis of earlier studies ^[69][70][69,70] unveiled that the addition of microsilica significantly bolsters the strength of a concrete mix. The degree of strength augmentation is contingent on several variables, including the mix type, cement quality, microsilica quantity, water-soluble additive volume, filler characteristics, and curing conditions. Silica fume concrete appears to adhere to the conventional strength-to-water/cement (w/c) ratio relationship. However, the curing process is affected by the inclusion of silica fume, leading to rapid moisture loss in modified concretes, fostering the development of voids and cracks. This phenomenon may result in a decrease in the concrete’s final strength. Conversely, the introduction of ash can reduce shrinkage porosity during solidification [40], showcasing the potential positive impact of silica production in microsilica. The recycling and utilization of fine waste material from silicon production (microsilica) constitute a crucial avenue for conserving resources ^[28][40][41][28,40,41]. The comprehensive utilization of waste across various industries empowers companies to allocate additional resources and curtail environmental impacts. For instance, in the oil refining sector, the advancement of technologies and materials for well construction is imperative to meet contemporary standards for well reliability and strength. While the addition of microsilica has been suggested to enhance the properties of cement slurries [69], this fortifying aspect has yet to be wholly proven and substantiated scientifically. Numerous studies have been undertaken to fortify the resistance of the cement ring against dynamic loading. Different methodologies have been explored to address this issue. Most researchers argue that Portland cement, despite its advantages, is marred by a significant drawback: as the strength of the cement stone increases, its fragility rises, accompanied by low strength ^[70][71][70,71]. Hence, targeted enhancements in expansive cement mixtures for cementing wells in permafrost regions present considerable interest, offering the potential to modify properties such as strength, frost resistance, expansion, and more [69]. Analysis of the microsilica’s structure demonstrates that the use of silica nanoparticles instigates significant alterations in the material. Notably, it leads to substantial compaction and improvement in the mechanical properties of the cement stone (resulting in a 3–6 fold increase in strength). Moreover, material modification with silica nanoparticles stabilizes key valence interactions such as Ca-Si-H, which is pivotal to concrete cohesion. This modification diminishes calcium leaching and enhances moisture resistance ^{[65][66][67][68][69][70]}[65,66,67,68,69,70]. By judiciously selecting and developing high-strength refractory concrete mixes, these can be manufactured using standard ready-mix plants. A slight elevation in compressive strength with silica fume in concrete directly yields heightened tensile and flexural strength, following a trend akin to standard concrete ^[66][67][68][66,67,68]. High-strength concrete often displays brittleness, and silica-modified concrete is no different. In this scenario, the modulus of elasticity does not correlate proportionally to the compressive force. The maximum value of the force causing deformation before failure under uniaxial compression rises with increased strength. However, the stress–strain curve before such failure is typically linear, as observed in [72]. Employing particle packing technology aids in enhancing plasticity by virtue of the particles’ sliding effect, thereby reducing brittleness when altering the filler-to-cement ratio. Consequently, this improves the overall integrity of the refractory concrete mix [73]. Enhanced particle adhesion is achieved through the close contact of small particles between microsilica concrete and the base of the matrix, serving as reinforcement ^{[66][67][68][69][70]}[66,67,68,69,70]. The shrinkage of microsilica concrete mirrors that of conventional concrete specimens. Yet, due to slower moisture removal, the shrinkage of microsilica concrete is more gradual. For standard tests, this implies that the observed shrinkage in fumed silica concrete is lesser than that in standard concrete specimens [62]. Various studies on refractory mixes ^[67][68][69][67,68,69] have revealed that modified concretes behave similarly to standard concretes under usual heating conditions. This adaptation allows them to be effectively tailored for their intended use in producing new kinds of refractories for metallurgical furnaces. The present diffusion mechanism in this process appears to resist vapor movement while removing residual moisture. During an intense fire test on the impregnated concrete, the low permeability of silica fume concrete thwarts vapor from escaping to the outer surface. As a consequence, crack spalling (internal fracture) occurs due to excessive vapor pressure within the matrix. Modified concretes conditioned with high mix hardening rates, as previously described, will not fracture, provided the water/cement ratio is optimally chosen. It is imperative to consider the coefficient of thermal expansion, which impacts the fire resistance of the concrete [61]. Thus, existing technologies suggest that, under equivalent technological conditions, incorporating microsilica into the concrete mix as a modifier establishes a stable structure and enhances the properties of refractory concrete for the sustainable operation of metallurgical units. It is important to note that microsilica has an ambivalent effect on the mobility of the cement paste. Consequently, the rheological properties of the cement paste change significantly, resulting in increased effective viscosity and plastic strength [69]. It has also been observed that the effect of microsilica on the rheological properties of the cement paste relies on the type and content of the superplasticizer ^{[60][61][62][63][64][65][66][67][68][69][70][71][72]}[60,61,62,63,64,65,66,67,68,69,70,71,72]. One demonstration of the pozzolanic activity of microsilica is the enhancement of the microstructure of the cement stone and the consolidation of the contact zone between the cement stone and the aggregate. In concrete, the interface primarily forms portlandite and ettringite crystals. Strengthening the contact zone enhances the adhesion of the cement stone to the aggregate, influencing the strength, crack resistance, and increasing resistance to frost and water ^[61][62][61,62].

8. Adding Nano Silica to Concrete

According to numerous studies, adding nanosilica to concrete can significantly enhance the material’s compressive strength ^{[74][75][76][77][78][79][80][81][82][83][84][85][86][87][88][89][90][91][92][93][94][95][96][97][98][99][100][101][102][103][104][105][106][107][108][109][110][111][112][113][114][115][116][117][118]}[74,75,76,77,78,79,80,81,82,83,84,85,86,87,88,89,90,91,92,93,94,95,96,97,98,99,100,101,102,103,104,105,106,107,108,109,110,111,112,113,114,115,116,117,118]. Moreover, it has been demonstrated that nanosilica can reduce both the initial and final set while accelerating the early strength of concrete. This is attributed to the large specific surface area of nanosilica, which acts as a robust binder between cement and aggregate [22]. Additionally, due to its extremely small particle size, nanosilica exhibits excellent pozzolanic activity ^{[74][75][76][77][78][79][80]}[74,75,76,77,78,79,80], enabling it to effectively fill all pores and voids in the concrete, including the interfacial transition zone (ITZ), thus augmenting its strength ^{[74][78][82][84]}[74,78,82,84]. The introduction of nanosilica promotes the formation of calcium silicate hydrate (CSH) gel, a crucial component in concrete strength. The review [22] analyzed the outcomes of various authors, which are presented in Table 6. Reches, Y. [82] indicates that nanoparticles serve as highly effective additives for modifying cement products, even at low concentrations (<1%). The principal modifications, as depicted in Figure 14 (displaying typical ranges while acknowledging significant variability), include a reduction in setting time (by 1–2 h) and diffusion coefficient (by 4%–75%), along with an increase in strength (by 5%–25%) and thermal durability (an increase of 0%–30% in residual strength). Figure 14 1—nano-particles/fibers; 2,6,9—cement; 3,7,10—water; 5—silica fume/fly ash; 4,8,11—aggregate; 13,16,11—C-S-H phases; 14,17,21—ettringite; 18—capillary pores; 12,15,19—portlandite; (SP1-amorphous silicon dioxide (colloidal) particle size 15 nm; SC-FA1-amorphous silicon dioxide (colloidal) particle size 15 nm plus mineral additive; SC-BFS1—amorphous silicon dioxide (colloidal) particle size 10 nm plus mineral additive; TP1-titanium dioxide (colloidal) particle size 15 nm; CP1-CaCO₃ particles 50–120 nm in size; CP2-CaCO₃ particles 15–40 nm in size) [46] Two possible reaction mechanisms exist during cement hydration in the presence of nanosilica ^{[89][90][91][92][93][94][95]}[89,90,91,92,93,94,95]. Nanosilica addition can accelerate cement hydration. When nanosilica combines with cement grains, it forms H₂SiO₄²⁻ that reacts with existing Ca²⁺ to produce extra calcium silicate hydrate (C-S-H). These C-S-H particles disperse in the water between the cement particles, acting as seeds for a more compact C-S-H phase. The creation of the C-S-H phase no longer occurs solely at the grain surface, as with pure C₃S, but also within the pore space. This high number of nuclei speeds up the initial cement hydration (Figure 14). Nano-SiO₂ (nS) altered the characteristics of the fresh solutions. Reches, Y. [82] illustrated the hydration process schematically in Figure 15. The figure portrays the microstructure of hydration, from the initial to the late stage (left columns), and the temporal evolution of the volume fraction of various cementitious phases (right column). The hydration of OPC (dark grey) to CSH (light grey) and CH (white) results in a decrease in total content and pore size (blue). Figure 15b,e demonstrate non-pozzolanic (TiO₂, black) nanomodification of hydration, whereas Figure 15c,f exhibit pozzolanic (SiO₂, dark green) nanoparticles. Figure 15d shows the pozzolanic reaction of FA (dark red) to create CSH and other hydrates (light red), whereas the synergistic effect of nanoparticles is depicted in Figure 15e,f. Nanoparticles, both pozzolanic and non-pozzolanic, serve as nuclei for hydrate precipitation from clinker and impurities (Figure 15b,c,e,f). Pozzolanic nanoparticles prompt additional CSH (light green) through reactions with CH (Figure 15c,f). Reches, Y. [82] then delved into the primary mechanisms of nanomodification. Nanoparticles support clinker hydration and the pozzolanic response of mineral impurities by supplying more surface area for hydrate precipitation from the interstitial solution (Figure 15b,c,e,f). In concrete sans nanoparticles, the concentration of essential ions for hydration reactions (e.g., Ca²⁺, SiO₄⁴⁻, and SO₄²⁻) in the pore water rapidly elevates upon contact with water, OPC, and any impurities. Within the initial ~12 h, the concentration surpasses saturation until reaching a critical nucleation point, which initiates the formation of stable hydrate phases; after this, the ion concentration in the solution gradually diminishes [95]. In contrast, for cement products containing nanoparticle admixtures, researchers have suggested ^{[82][84][98][99][100][101][102][103][104][105][106][107][108][109][110][111][112][113][114][115][116][117][118][119][120][121][122][123][124][125][126]}[82,84,98,99,100,101,102,103,104,105,106,107,108,109,110,111,112,113,114,115,116,117,118,119,120,121,122,123,124,125,126] that the nanoparticles act as nuclei for the precipitation and growth of hydrate phases, starting when the ion concentration surpasses saturation instead of reaching critical nucleation. In fixed W/B and SP formulations, the presence of nS reduces the available lubricating water in the compound. The most notably impacted rheological parameter, yield strength, experiences a significant increase with the addition of nS to the paste. Conversely, changes in plastic viscosity are less prominent. Additionally, the addition of nS decreases the spreading diameter of these solutions by enhancing the paste’s cohesiveness. The relationship between spreading and yield stress values better elucidates the effects of nS inclusion. For instance, a 2.5% w/w nS inclusion leads to a 19.6% reduction in spreading diameter and a 157% increase in yield stress. In this case, plastic viscosity increases by only 3.6% [89]. The addition of nS enables the anticipation of the setting onset and a reduction in dwell time. Incorporating 2.5 wt.% nS in the compound reduced the setting time by 60% and the time to reach maximum hydration temperature by 51.3%. Consequently, the addition of nS promotes increased CH production at an early age compared to samples without nS. Moreover, the addition of nS decreases the apparent density and increases the air content of these solutions. An analysis of numerous studies ^{[82][83][84][85][86][87][88][89][90][91][92][93][94][95][96][97][98][99][100][101][102][103][104][105][106][107][108][109][110][111][112][113][114][115][116][117][118][119][120][121][122][123][124][125][126]}[82,83,84,85,86,87,88,89,90,91,92,93,94,95,96,97,98,99,100,101,102,103,104,105,106,107,108,109,110,111,112,113,114,115,116,117,118,119,120,121,122,123,124,125,126] highlights the remarkable effectiveness of nanoparticles in modifying cement products, even at low concentrations (<1%). The main modifications include a reduction in setting time (1–2 h) and the diffusion coefficient (4%–75%), along with a strength increase (5%–25%) and enhanced thermal durability (up to 30% increase in residual strength). These changes are attributed to the unique reactivity of nanoparticles, which is linked to their small size and high surface area. Smaller particles boast a higher surface area to volume ratio, and their inclusion leads to an expanded surface area. Consequently, the increased surface area of nanoparticles in the binder can boost reactivity. Typically, nanoparticles minimize the number of nano-sized pores in C-S-H and fortify the nanostructures of cementitious composites. Take nanosilica (SiO₂) as an example—each Si atom, chemically bonded to four oxygen atoms, forms a tetrahedron, serving as the basic building block. This structure results in silicate chains composed of oxygen-separated silicate tetrahedra ^{[92][93][94][95][96][97][98]}[92,93,94,95,96,97,98]. The addition of nanosilica to cementitious materials elevates durability by enhancing C-S-H hardness, rendering it more resistant to calcium leaching ^{[82][83][84][85][86][87][88][89][90][91][92][93][94][95]}[82,83,84,85,86,87,88,89,90,91,92,93,94,95]. When added to the early stages of fly ash liquor production, nanosilica absorbs most of the Ca(OH)₂, leaving a reduced amount available for fly ash hydration [89]. Consequently, the addition of nanosilica may accelerate the pozzolanic reaction in the cementitious composite. An examination of the literature reveals that the combined effect of microsilica and nanosilica is not entirely comprehended, yet it holds the potential to enhance concrete’s performance (further research is recommended to fully understand the causes of this synergistic effect). The authors of ^{[85][86][87][88][89][90][91][92][93][94][95][96][97][98][99][100][101][102][103][104][105][106][107][108][109][110][111][112][113][114][115][116][117][118][119][120][121][122][123][124][125][126][127][128][129][130]}[85,86,87,88,89,90,91,92,93,94,95,96,97,98,99,100,101,102,103,104,105,106,107,108,109,110,111,112,113,114,115,116,117,118,119,120,121,122,123,124,125,126,127,128,129,130] suggest potential mechanisms for this effect, which demand additional investigation. Firstly, the nucleation effect of nanosilica particles accelerates the cement hydration process, freeing lime for the pozzolanic reaction, thus rendering the silica fume more reactive. Nanosilica demonstrates significantly higher pozzolanic activity than microsilica. Concrete incorporating nanosilica consistently exhibited higher compressive strength than standard concrete across all ages. Furthermore, the addition of nanosilica elevated the flexural and tensile splitting strengths of the concrete. The second observation indicates that while microsilica exhibits a more extensive filling effect than nanosilica due to the larger quantity of material added, silica nanoparticles can supplement microsilica by occupying the voids between the particles to further enhance the packing density of cementitious materials. Regarding other nanomaterials, few studies have been conducted to assess the morphological attributes of nanoparticles for filling voids between cement grains. Figure 16 clearly illustrates the morphological distinctions of nanoparticles like SiO₂, CaCO₃, and TiO₂. Furthermore, Figure 15 showcases pairs of morphologically different anatase TiO₂ nanoparticles: one exhibiting a platelet geometry with a protruding surface {0 0 1} (left) and the other with a tetragonal bipiramidal geometry displaying a protruding surface {1 0 1} (right). The hydrated electron of these surfaces measures 1.6 and 1.0 J/m², respectively [82]. Such morphological characteristics are scarcely addressed in cement literature.

9. Patent Research into Methods of Recycling Waste and Its Use in Various Industries as a Strengthening Additive

This section explores patented technical solutions for producing oxide system products by incorporating waste from metallurgical production. The aim is to understand the structure formation mechanism in samples and mass transfer conditions during heating or physical impact ^{[36][38][40][41][42][43][131][132][133][134][135][136][137][138][139][140][141][142]}[36,38,40,41,42,43,131,132,133,134,135,136,137,138,139,140,141,142]. In a patent by the authors of [131], microsilica was added to the concrete mix as an aqueous suspension, comprising 40%–70% of the total volume. However, this suspension exhibited high viscosity and limited rheological stability over a 90-day period, a drawback addressed by Golotsan A.A. and Dolgopolov A.N. in their work [138]. They reduced the suspension’s viscosity and enhanced its rheological stability, crack resistance, and flowability. The introduction of microsilica in the form of an aqueous suspension prompted considerations regarding the transformation of water-soluble polymorphs of silica upon contact with other matrix materials. Another invention [139] focused on obtaining finely dispersed amorphous microsilica from cost-effective mineral raw materials. This process yields microsilica with high purity and a dispersion ranging between 0.062 and 0.097 microns. Patent [140] describes a production process for finely dispersed amorphous microsilica using the sol-gel method involving diatomaceous earth and sodium hydroxide. Furthermore, patents ^[131][132][131,132] suggested using microsilica in the production of ceramic-facing materials. Its application was found to reduce water absorption while enhancing frost resistance and strength. However, a raw material mix detailed in [137] containing microsilica exhibited low compressive strength and frost resistance, making it unsuitable for wall panel production. A mix aimed at non-autoclaved aerated concrete [136] incorporated microsilica to bolster material strength but faced challenges due to the high porosity caused by aluminum powder usage. Similarly, ref [135] considered microsilica to reinforce foamed concrete, but difficulty arose due to the fibrous filler content, making homogeneous mixing challenging. The application of microsilica in the refractory industry was reviewed in [134], especially in the production of monolithic linings, to enhance strength and oxidation resistance within the range of 600–1100 °C. Finally, ^[141][142][141,142] investigated cement slurries utilizing microsilica and calcium oxide, supplementing the solution (12%–16%) alongside microsilica from silicon production waste. Considering the properties and characteristics of microsilica from various types and origins, it can serve as a strengthening additive in concrete mixtures, including refractory compositions. Patent searches have outlined the potential for introducing microsilica into various mixtures, which can be further adapted for use in metallurgical industries, particularly in the production of refractory fireclay products and concrete. This adaptation takes into account the unique properties and structure of microsilica. In summary, studies ^{[56][57][58][59][60][61][62][63][64][65][66][67]}[56,57,58,59,60,61,62,63,64,65,66,67] explored different microsilica types and indicated that adding this additive to concrete enhances its strength, frost, and chemical resistance. However, the use of superplasticizer C-3 is essential. The authors of ^{[118][119][120][121][122][123][124][125]}[118,119,120,121,122,123,124,125] suggest that the effective utilization of SiO₂ is only feasible in conjunction with a plasticizer, accelerating cement hydration and boosting cement stone strength by 20%. On the other hand, the authors of [110] observe that microsilica extends the setting time of cement mortar due to the small size of its particles. The amorphous nature of nano-SiO₂ raises a key challenge: how to meaningfully differentiate between distinct properties of nano-SiO₂. Two structural properties can significantly influence the reactivity of nano-SiO₂ [82]. Further research should address crucial aspects, starting with the assessment of crystallinity [82]. Considering amorphous SiO₂ as akin to defective quartz, the activation energy for the pozzolanic reaction correlates with ideal crystallinity, reaching maximum efficiency. The thermodynamic path of this reaction becomes more favorable as the material moves towards polycrystalline or amorphous structures, which can be evaluated through techniques like X-ray diffraction and 29 Si nuclear magnetic resonance (full width at half maximum). Another essential consideration is the degree of cross-linking [82]. If amorphous SiO₂ is viewed as interlinked polymer chains, these connections limit the reactivity of the Si anti-bonding orbital. The pozzolanic reaction replaces Si triple bonds with Si-OH bonds, but this replacement can be hindered by these cross-links. Nano-SiO₂ generated through the sol-gel process, when catalyzed by bases, tends to be more cross-linked than when catalyzed by acids. Consequently, acid-catalyzed nano-SiO₂ has shown more efficacy in enhancing the compressive strength of mortars compared to base-catalyzed nano-SiO₂ ^{[111][112][113][114][115][116][117][118][119][120][121][122][123][124][125][126][127][128][129][130]}[111,112,113,114,115,116,117,118,119,120,121,122,123,124,125,126,127,128,129,130].