1. Introduction
Carbon-containing refractories (CCRs) play a crucial role in the iron and steel metallurgy process due to their outstanding thermal shock and slag resistance [
1,
2,
3,
4,
5,
6,
7]. These refractories are manufactured using aggregates primarily composed of one or more high melting-point oxides or their associated mineral phases. Carbon, noted for its exceptional refractory properties such as non-wettability by slag and high thermal conductivity, can be incorporated into CCRs either as an additive or as a binder (e.g., coal tar, petroleum pitch, or resin) [
8,
9,
10]. The integration of carbon into oxide aggregates results in various types of CCRs, including magnesia−carbon (MgO−C) [
11,
12], calcia−magnesia−carbon (CaO−MgO−C) [
13], alumina−carbon (Al
2O
3−C) [
14], zirconia−carbon (ZrO
2−C) [
15,
16], and alumina silicon carbide−carbon (Al
2O
3−SiC−C) [
17,
18].
Carbon-containing calcia, magnesia and doloma (sintered dolomite) are classified as basic oxide refractories. MgO−C refractories are widely used as lining materials for converters, electric arc furnaces, and the slag lines of steel ladles. Doloma-carbon refractory bricks find extensive application in the steel industry for lining basic oxygen furnace converters, ladle furnaces, and electric arc furnaces [
19,
20]. A significant drawback of basic refractories is their tendency to hydrate. However, including carbon enhances thermal shock resistance, reduces porosity, increases the wetting angle, and significantly improves hydration resistance [
21,
22,
23]. Non-basic oxide-carbon refractories, such as carbon-containing alumina, alumina−silicon carbide, and zirconia, are frequently used in iron and steelmaking. Al
2O
3−C refractories are primarily employed in producing continuous casting components, including slide plates, submerged entry nozzles, long nozzles, and monobloc stoppers [
24,
25]. ZrO
2−C refractories, known for their superior resistance to abrasion and corrosion, are used in hollow ware like continuous casting submerged entry nozzles [
26,
27,
28]. Al
2O
3−SiC−C refractories are mainly used in torpedoes to transfer liquid iron and steel ladles [
29,
30,
31]. Graphite is the primary carbon source in CCRs because it enhances slag corrosion resistance. This enhancement occurs through the reaction of graphite with oxides in slag and impurities within the brick, forming gaseous products. These gaseous products are then re-oxidized, resulting in a dense deposit of the secondary oxide phase at the slag-refractory interface, which prevents melt penetration [
32,
33,
34].
Oxide-carbon refractories represent a significant advancement in stainless steel manufacturing, contributing to a marked reduction in refractory consumption [
35,
36]. However, traditional oxide-carbon refractories with a high carbon content present several drawbacks:
(1) Molten metal, such as steel, can absorb carbon from the CCRs, resulting in an undesirable increase in the carbon content of the metal, which is detrimental to producing high-quality steel.
(2) The high graphite content, coupled with high thermal conductivity, can lower the temperature of the molten metal, adversely affecting the tapping process.
(3) Graphite’s tendency to be oxidized creates pores in the refractory bodies, accelerating slag corrosion and releasing CO
x greenhouse gases.
Hence, reducing the carbon content in oxide-carbon refractories is essential to mitigate the negative impacts on high-quality steel production. However, lowering carbon content adversely affects the refractories’ properties. When carbon content drops below 5 wt.%, thermal diffusivity decreases and thermal expansion increases, significantly impairing the refractories’ thermal shock and slag corrosion resistance.
In recent years, to address the problems and challenges of CCRs, researchers have investigated the effects of various types of nanomaterials on the service performances of the refractories [
37,
38,
39,
40]. Nanoscale additives were proposed in refractories as early as 2003 [
41,
42]. Further investigations have demonstrated that adding small amounts of nanoscale materials can significantly enhance the performance of refractories [
43,
44,
45]. Nanomaterials used as ingredients in CCRs are divided into two categories: active and inert materials. Inert nanomaterials primarily enhance CCR properties through nucleation, filler, and bridging effects. In contrast, active nanomaterials influence the in situ generation of new phases and nucleation as well as filler effects. Additionally, the optimal amounts of nanomaterials needed for achieving the best refractory performance vary with the geometric sizes, shapes, and physical properties.
This review thoroughly examined recent developments in oxide-carbon refractories reinforced with nanomaterial additives. The categories of nanomaterial additives, including nanocarbons, nano oxides, and nano non-oxide and the performances of reinforced oxide-carbon composites, are extensively discussed (). Based on this review, some future research trends in the field of oxide-carbon refractories are proposed.
. Category of nanomaterial additives.
2. Nanocarbon Containing Refractories
Nanocarbon sources used in oxide-carbon refractories include carbon black (CB), graphite nanosheets (GNSs), and carbon nanotubes (CNTs). These nanocarbons can easily fill the voids between coarse, medium, and fine particles, thereby promoting the formation of ceramic bonding phases. This process reduces porosity and enhances density, strength and corrosion resistance in the final refractory products [
46,
47,
48,
49].
2.1. Carbon Black Containing Refractories
Carbon black consisting of nanosized particles (approximately 30 nm) in the form of porous and compressible agglomerate, is widely used in structural composites. The addition of CB into refractories results in improved properties [
50,
51,
52,
53,
54], and the advantages associated with the addition of CB are as follows: (1) filling the gaps between other refractory components, thereby enhancing density; (2) contributing to the in situ formation of carbide phases due to its high reactivity; and (3) increasing the carbon content, which is essential for boosting the performances of CCRs.
Different nanosized carbon sources result in various properties due to their size and particle size distribution. Pilli et al. [
55] prepared low carbon-containing Al
2O
3−C refractories using two different grades of CB, namely, N220 (particle size 20–25 nm) and N990 (particle size ∼250 nm). As shown in the fracture surface of the sample in a, the nanocarbon−containing sample coked at 1000 °C exhibited a columnar or needle-like structure, attributed to forming aluminum carbide ceramic phases. The formation of in situ ceramic phases in nanocarbon-containing compositions provided a compact microstructure that improved strength, inhibited oxidation, and contributed to corrosion resistance. b shows the cold crushing strength (CCS) of samples with different particle sizes of nanocarbon black. It could be seen that the batch containing 0.5 wt.% N220 exhibited higher strength values, which might be due to the higher reactivity of nanocarbon forming more carbides. However, excessive content of nanocarbon black could cause agglomeration and the particles might not fill the gaps between alumina particles, negatively impacting density and strength. Additionally, after three thermal shock cycles, the strength retention ratio of samples containing nanocarbon (3 wt.% flake graphite + 1.0 wt.% nanocarbon black) was higher than that of samples with 25 wt.% flake graphite (c). Similarly, Wu et al. [
56] found minimal corrosion and penetration under a reducing atmosphere for Al
2O
3−SiC−C castables with 0.4 wt.% CB. However, the porosity increased with the CB content. Li et al. [
57] developed Al
2O
3−C refractories with excellent mechanical properties and thermal shock resistance by combining nano CB and MWCNTs. The improvement was attributed to the filling effect and thermal stress absorption of the nano CB, while MWCNTs reinforced and toughened the matrix of the refractories. Liao et al. [
58] dispersed carbon black (CB) particles into reactive alumina powders using planetary ball milling with ethanol as the dispersion medium. The pre-mixed fine powders were then used to fabricate Al
2O
3−C refractories, resulting in refractories with a higher cold modulus of rupture (CMOR) and superior thermal shock resistance. Bag et al. [
59] investigated the impact of nano CB content on the properties of MgO−C refractories while maintaining the total carbon content at less than half that of traditional MgO−C refractories. They determined that the optimal properties were achieved by adding 0.9 wt.% nano CB in combination with 3 wt.% graphite. The incorporation of nano CB resulted in a more uniformly dispersed matrix and enhanced filling of the microscopic spaces between coarse, medium, and fine particles in the starting materials. Additionally, the nano CB improved the slag corrosion resistance by increasing wettability resistance.
The application of nanoscale materials in carbon-bonded refractories has faced significant obstacles due to their extremely high production costs and the difficulty of achieving homogeneous distribution within the refractory matrix [
60]. Research suggests that preparing oxide or carbide coatings with enhanced water wettability on nanocarbon raw materials can aid their uniform dispersion in refractories. Ye et al. [
61] employed a molten salt synthesis (MSS) technique to prepare SiC coatings on CB particles. The SiC-coated CB particles exhibited significantly enhanced dispersity and flowability in water compared to their uncoated counterparts. The apparent viscosity of a water suspension containing SiC-coated CB was notably lower than that of the suspension with uncoated CB. Najafi [
62] introduced CB (N110) into MgO−C refractory bricks using Mg(OH)
2/CB mixture as a starting material. The SEM image in d clearly showed that CB nanoparticles are located between MgO particles, indicating that the sol−gel method allowed CB nanoparticles to be well dispersed and stabilized in Mg(OH)
2, preventing their severe agglomeration. The SEM image in e showed no significant microstructural defects in the MgO−C refractory matrix can be observed, and the main refractory components (MgO and graphite) were well bonded with each other. The CCS results showed that adding 1 wt.% of the nano-admixture increased the CCS value by over 100%, demonstrating its excellent mechanical properties (f). This indicates that highly dispersed CB nanoparticles significantly enhance the mechanical and physical properties of industrial MgO−C refractory bricks.
. (<b>a</b>) SEM image of the refractory sample containing 3 wt.% flake graphite and 2 wt.% nanocarbon black after coked at 1000 °C. (<b>b</b>) Cold compressive strength of the sample was achieved with the addition of N220 nanocarbon black. (<b>c</b>) Retained strength of the sample with 25 wt.% flake graphite and the sample with 3 wt.% flake graphite and 1 wt.% nanocarbon black [
55]. (<b>d</b>) SEM micrograph of the nano-MgO/carbon black mixture. (<b>e</b>) SEM micrograph of the MgO−C refractory sample with 1 wt.% MgO/carbon black nanocomposite addition. And (<b>f</b>) cold crushing strength and apparent porosity results of MgO−C refractory bricks with different amounts of nano-admixture [
62]. (<b>a</b>–<b>c</b>) Copyright 2022, John Wiley and Sons; (<b>d</b>–<b>f</b>) Copyright 2016, Elsevier.
As an amorphous phase, the CB’s oxidation resistance and thermal conductivity are not as good as those of graphite flakes, which limits its application in CCRs. Therefore, enhancing the oxidation resistance of CB will help to expand the application prospects and address an urgent need for CCRs. To improve oxidation resistance, the effects of adding various antioxidants were studied [
63,
64,
65,
66,
67,
68,
69]. Behera et al. [
70] discovered that incorporating metal powders as antioxidants increases the formation of in situ ceramic phases, attributed to the higher surface area and reactivity of N220 nanocarbon compared to graphite. Among the antioxidants studied, aluminum was the most effective. This effectiveness is due to the uniform formation of in situ ceramic phases, such as aluminum carbide and magnesium aluminate spinel.
2.2. Carbon Nanotubes Containing Refractories
CNTs are seamless cylinders formed by wrapping graphene sheets, with carbon atoms covalently bonded through sp
2 hybridization. These structures have been extensively studied due to their remarkable physical and chemical properties [
71,
72,
73]. CNTs exhibit exceptional strength along the axial direction, with Young’s modulus ranging from 270 to 950 GPa and tensile strength between 11 and 63 GPa. Additionally, their smaller particle size and high specific surface area enable CNTs to effectively fill pores or gaps in the refractory matrix, promoting the formation of ceramic bonding phases and enhancing mechanical properties [
74,
75,
76,
77].
Due to their outstanding physical, chemical, and mechanical properties, CNTs are a promising carbon source to partially or completely replace graphite flakes in CCRs. Halder et al. [
78] partially substituted graphite with amorphous CNTs to reduce the total carbon content while maintaining the same or greater carbon surface area. The incorporation of CNTs improved the compactness of the refractory composite and decreased the cumulative volume of large pores. Additionally, the partial substitution of graphite with CNTs generated a more effective surface area due to the lower density of CNTs, significantly enhancing slag corrosion resistance in specimens containing 0.18 wt.% CNTs. Luo et al. [
79] investigated the effects of multi-walled CNTs (MWCNTs) on the microstructures and mechanical properties of Al
2O
3−C refractories. The addition of 0.05 wt.% MWCNTs resulted in improved mechanical properties. However, increasing the CNT content to 1 wt.% gradually deteriorated the properties due to agglomeration. Moreover, most or all CNTs were consumed and transformed into ceramic phases during the firing process, sacrificing their intrinsic advantages. To address these issues, a SiC
xO
y coating was applied to the surface of CNTs using polycarbosilane (PCS) as the precursor. This coating protected the CNTs from oxidation and inhibited reactions with aluminum (l, g), silicon (s, g), and carbon monoxide (g), thus reducing the formation of ceramic phases at high temperatures. As a result, the refractories’ mechanical properties and oxidation resistance were enhanced [
80]. Additionally, the transformation of CNTs is significantly accelerated and primarily driven by SiO (g) compared to the Si antioxidant in Al
2O
3−C refractories. Liao et al. [
81] investigated the phase and microstructure evolutions of CNTs in B
4C- and Si-containing Al
2O
3−C refractories. Their findings indicated that incorporating B
4C lowers the partial pressure of SiO (g) because B
4C oxidizes before Si at lower temperatures. This oxidation prevents the transformation of CNTs at 1000 °C and suspends their transformation at higher temperatures.
CNTs tend to form hard agglomerates that are difficult to separate into individual nanotubes due to their nanoscale dimensions and the strong Van der Waals forces among them. Consequently, the potential benefits of incorporating CNTs in CCRs have not been fully realized because of the challenges associated with the homogeneous dispersion of agglomerated nanotubes. To address these issues, in situ synthesis and CNT-decorated oxide methods have been employed to prepare CNT-containing refractories. CNTs can be synthesized by the catalytic pyrolysis of phenol-formaldehyde resins using transition metal catalysts under an inert atmosphere. Luo et al. [
82] reported that multi-walled CNTs were obtained from Ni-catalyzed phenolic resin by increasing the pyrolysis temperature. These CNTs formed a net-like structure homogeneously distributed in the pores and on the surface of Al
2O
3 particles in the matrix. This addition significantly improved the mechanical properties, such as the cold modulus of rupture (CMOR) and flexural modulus, of the Al
2O
3−C refractory specimens. Liao et al. [
83] indicated that B
4C could favor the formation of in situ CNTs from the resin binder and suppress the transformation of CNTs into SiC whiskers in Al
2O
3−C refractories at elevated temperatures. This enhanced toughness and thermal shock resistance of the CNT-containing Al
2O
3−C refractories.
In addition to alumina-based refractories, CNTs can be generated in situ in magnesia-based refractories. Wei et al. [
84] reported that Fe nanosheets could catalyze phenolic resin to produce CNTs in low-carbon MgO−C refractories. Compared to specimens without the catalyst, those with the catalyst exhibited a 25% increase in CMOR and significantly greater displacement during the three-point bending test. The addition of metallic additives can reduce the partial pressures of oxidizing gases and increase that of hydrocarbon gases, thereby promoting the in situ formation of CNTs in the matrix. Zhu et al. [
85] investigated the role of Al and Si additives and various heat-treatment temperatures (800–1400 °C) in the graphitization process of phenolic resin in the MgO−C refractory matrix. Their findings indicated that, compared to specimens containing Si powder, the addition of metallic Al was more conducive to the growth of straight and bamboo-like CNTs, facilitated by the catalyst.
The dispersion of CNTs in refractories significantly impacts their performance, and oxide/CNT composite powders can enhance the uniformity of CNT dispersion in the matrix. Feng et al. [
86] prepared CNTs/MgAl
2O
4 whisker composite powders, with their microstructure and energy dispersive spectroscopy results in a,b. The CNTs interlocked with MgAl
2O
4 whiskers, facilitating their uniform dispersion within the refractory matrix. Thermal shock test results showed the residual strength ratio of low-carbon Al
2O
3−C refractories containing 3.0 wt.% CNTs/MgAl
2O
4 was 39.2%, 97.0% higher than the blank sample (c). The presence of CNTs and MgAl
2O
4 whiskers significantly improved thermal shock resistance due to mechanisms like “bridging”, “crack deflection”, and the generation of microcracks in the matrix. Additionally, the mechanism by which CNTs/MgAl
2O
4 prevented the propagation of the main crack was illustrated in d. During the thermal shock process, crack deflection due to the presence of flake graphite with excellent sliding properties on the surface layer of the aggregates can be formed. However, this effect was insufficient to stop the main crack’s propagation completely. When the crack penetrated the aggregates, multiple deflections occurred within the spinel, and a large number of microcracks formed around the area where it encountered the CNT-wrapped cubic MgAl
2O
4. The crack deflection increased the path of the main crack propagation, and the formation of microcracks created new surfaces. All of these induced the elastic strain energy release in the refractory, effectively inhibiting the catastrophic propagation of cracks. Furthermore, the MgAl
2O
4 whiskers in the matrix and other in situ formed ceramic whiskers consumed thermal stress through stretching and bridging, thus preventing crack propagation. Li et al. [
87] prepared CNT/MgO composite powders using a catalytic combustion synthesis method. SEM images showed that cubic MgO particles, along with fibrous CNTs were uniformly distributed in the prepared samples, the aspect ratio of the CNTs was 200 (e). TEM results confirmed that the prepared CNTs had a typical hollow bamboo-like structure (f). Additionally, thermal shock test results (g) indicated that increasing the content of composite powder enhanced the residual strength ratio of the samples. When 2.5 wt.% of CNT/MgO composite powder was added, the residual strength ratio of the samples was 63.9% higher than that of the pristine samples.
In addition to the previously mentioned methods, chemical vapor deposition (CVD) has proven effective for generating CNTs. Liang et al. [
88] first prepared Al
2O
3/MWCNT composite powders via the catalytic decomposition of methane and subsequently incorporated these powders into Al
2O
3−C refractories. This approach achieved a uniform distribution of MWCNTs within the Al
2O
3−C refractory matrix, thereby enhancing the thermal shock resistance of the refractories. Li et al. [
89] synthesized nano carbon-decorated Al
2O
3 powders through CVD, using ethanol as the carbon source and Ni as the catalyst. SEM images of the samples (h) revealed a substantial formation of MWCNTs on the surfaces of Al
2O
3 powders with minimal catalyst loading. Introducing MWCNT-decorated Al
2O
3 powder into Al
2O
3−C refractories stimulated the growth of SiC whiskers within the matrix, significantly improving thermal fracture resistance and providing residual strengths 1–2 times higher than those of original nano carbon black-containing refractories (i). j illustrates the toughening mechanism, where MWCNTs promoted the growth of SiC whiskers, thereby enhancing thermal fracture resistance. The “pull-out” and “bridging” mechanisms of MWCNTs and SiC whiskers explain the observed strengthening properties.
. (<b>a</b>) SEM images and (<b>b</b>) energy dispersive spectrometry (EDS) results of the CNTs/MgAl<sub>2</sub>O<sub>4</sub> sample. (<b>c</b>) CMOR of Al<sub>2</sub>O<sub>3</sub>−C refractories before and after thermal shock tests and their residual strength ratio. (<b>d</b>) Schematic diagram of crack propagation in the CNTs/MgAl<sub>2</sub>O<sub>4</sub> sample under thermal shock [
86]. (<b>e</b>) SEM image of the CNTs/MgO composite powders. (<b>f</b>) TEM image of CNTs in the CNTs/MgO sample. (<b>g</b>) CMOR and residual strength ratio of Al<sub>2</sub>O<sub>3</sub>−C refractory with CNTs/MgO composite powders before and after thermal shock test [
87]. (<b>h</b>) SEM image of nano carbon composites@Al<sub>2</sub>O<sub>3</sub> powder. (<b>i</b>) CMOR of Al<sub>2</sub>O<sub>3</sub>−C refractory with nano carbon composites@Al<sub>2</sub>O<sub>3</sub> powder before and after thermal shock test. And (<b>j</b>) schematic diagram of nanocomposites strengthening and toughening mechanisms in the Al<sub>2</sub>O<sub>3</sub>−C matrix [
89]. (<b>a</b>–<b>d</b>) Copyright 2024, John Wiley and Sons; (<b>e</b>–<b>g</b>) Copyright 2022, Elsevier; (<b>h</b>–<b>j</b>) Copyright 2018, Elsevier.
Graphene, a two-dimensional material, has recently garnered significant attention due to its unique electronic, mechanical, and thermal properties [
90,
91,
92,
93,
94,
95,
96,
97,
98,
99,
100,
101]. These exceptional characteristics make graphene an ideal candidate for various applications, including nanoelectronics, nanocomposites, supercapacitors, and chemical/biological sensors [
102,
103,
104,
105,
106,
107,
108,
109,
110,
111,
112]. Graphene nanosheets (GNSs), consisting of one or more layers of graphene, serve as an alternative reinforcement material comparable to CNTs and have demonstrated significant improvements in the service properties of CCRs.
Expanded graphite (EG), derived from graphite and featuring a long-range ordered layered structure made up of parallel graphene nanosheets, exhibits remarkable mechanical properties, including compressibility, resilience, high tensile strength, and a high elastic modulus [
113,
114,
115,
116]. Consequently, EG has been utilized as a reinforcement and carbon source in CCRs, substituting traditional graphite flakes. Behera et al. [
117] used EG as a partial replacement for flake graphite in 5 wt.% graphite-containing MgO−C refractories. The composition containing 0.8 wt.% EG achieved a 20% increase in CCS and a 120% higher hot modulus of rupture (HMOR), successfully enduring 12 thermal cycles without failure. Additionally, they introduced EG into commercial Al
2O
3−C refractory slide gate plates. Using EG as a carbon source facilitated the formation of a flaw-tolerant microstructure, with in situ catalytic formation of nanostructured interconnected SiC whiskers in the matrix, which enhanced mechanical properties. Kim et al. [
118] investigated the impact of varying EG content (0−4 wt.%) in MgO−C bricks with a total graphite content of 15 wt.%. They found that as the EG content increased, the fracture strength decreased, but thermal shock resistance improved due to the increase in apparent porosity, which buffered the thermal expansion of MgO. However, EG can be easily pulled out, leading to weak interfacial bonding strength, thereby limiting its reinforcement effect. To address this issue, Wang et al. [
119] prepared β-SiC whiskers hybridized with EG and SiO
x spheres hybridized with EG, then introduced them into Al
2O
3−C refractories. These hybridized phases acted like “tree roots,” increasing the interfacial shear strength of the refractory and absorbing fracture energy during failure. As a result, the refractories’ mechanical properties and thermal shock resistance were significantly improved.
In addition, structural degradation and oxidation of graphene nanosheets often originate from unpaired carbon atoms [
120,
121,
122,
123,
124,
125]. Doping boron (B) or nitrogen (N) elements into graphene can improve structural stability and expand its application prospects in refractories. Wang and his team [
126] effectively incorporated boron and nitrogen into the carbon framework through various C−B bonds (such as B
4C, B−sub−C, and BC
2O) and C−N bonds (including pyridine-N, amino-N, and graphitic-N). This was achieved while preserving the hexagonal graphitic structure and diminishing its reactivity. The SEM image shown in a revealed the porous structure and graphite layers of B-doped EG. Due to its similar morphology and microstructure to EG, the doped EG could also be considered a potential reinforcement material. Compared to as-received EG, the B-doped and N-doped EG retained a relatively intact structure in Al
2O
3−C refractories at high temperatures due to fewer defects and lower reactivity. The fracture behavior of specimens incorporating B-doped and N-doped EG was shown in b,c. At 800 °C, specimens with EG, B-doped EG, and N-doped EG demonstrated greater force and displacement values than those with 1 wt.% flake graphite, attributed to their enhancing and toughening effects. At 1200 °C, EG promoted the formation of numerous β-SiC whiskers, while B-doped and N-doped EG mitigated performance decline due to EG’s structural changes. Therefore, at 1200 °C, the synergistic effects of B/N-doped EG and the in situ generated β-SiC whiskers enhanced the fracture properties of the refractory material. Additionally, the relatively intact structure of B-doped and N-doped EG at 1200 °C indicated more efficient thermal stress absorption and release. Consequently, specimens containing B-doped EG and N-doped EG exhibited the highest residual strength ratios (d). In the oxidation resistance test (e), the B/N-doped EG showed less weight change than EG, indicating enhanced oxidation resistance.
Graphene nanosheets (GNSs) have high mechanical strength and thermal conductivity [
127,
128,
129,
130,
131,
132]. Compared with EG, GNSs possess a higher specific surface area, and the volume effect of GNSs effectively enhances the mechanical, thermal, and electrical properties of ceramic matrix composites [
133,
134,
135,
136,
137,
138]. GNSs can be prepared by three techniques: (i) mechanical exfoliation, (ii) epitaxial growth, and (iii) graphene oxide reduction [
139,
140,
141,
142,
143,
144,
145,
146]. Among these methods, the mechanical exfoliation technique is particularly notable for its simplicity, low cost, and high efficiency, making it one of the most promising approaches for producing GNSs. GNSs/MgO and GNSs/Al
2O
3 composite powders can be obtained by ball-milling EG and oxide powders. This process ensures a uniform distribution of GNSs in alumina and magnesia powders, with the thickness and size of GNSs dependent on the amount of EG added. The incorporation of GNSs composite powders enhances the mechanical properties and thermal shock resistance of CCRs. In the magnesia−carbon system, the highly reactive GNSs can reduce the partial pressure of oxygen, increasing the partial pressure of N
2 gas. This promotes the formation of more AlN ceramic phases within the matrix, thereby strengthening and toughening the MgO−C refractories [
147]. In the alumina−carbon system, GNSs can improve mechanical properties by stimulating the growth of SiC whiskers at lower temperatures, owing to their higher reactivity compared to graphite.
. (<b>a</b>) SEM micrographs of B-doped EG. Force−displacement curves of the specimens fired at (<b>b</b>) 800 °C and (<b>c</b>) 1200 °C. (<b>d</b>) Residual CMOR and the residual strength ratio of CMOR of the specimens fired at 1200 °C after 5 thermal shock cycles. And (<b>e</b>) mass change of the specimens fired from room temperature to 1300 °C in air [
126]. (<b>a</b>–<b>e</b>) Copyright 2017, Elsevier.
To achieve the homogeneous distribution of GNSs several nanocomposite powders were prepared and then used in Al
2O
3−C and MgO−C refractories. Ding et al. [
148] developed multilayer graphene/MgAl
2O
4 composite powders using a one-step carbon-bed sintering process, with magnesium citrate serving as the source for both MgO and carbon. The resulting products contained 5.96 wt.% carbon, with graphene layers (6–10 layers) located between or outside the MgAl
2O
4 grains. These C/MgAl
2O
4 composite powders absorb strain energy and thermal stress, forming short fibrous ceramic phases within the matrix. As a result, incorporating C/MgAl
2O
4 composite powders significantly enhanced the thermal shock resistance of low-carbon Al
2O
3−C refractories. Lv et al. [
149] successfully synthesized GNSs using a liquid-phase shear exfoliation method. To enhance their properties, they modified the surface of these GNSs with AlOOH nanofibers before incorporating them into MgO-based castables, as illustrated in a. The characterization of the GNSs using TEM and AFM techniques revealed that the nanosheets had an exceptionally thin structure, comprising approximately 10 atomic layers (b,c). Moreover, a digital photograph (d) demonstrated the excellent stability of the GNSs suspension, which remained uniformly dispersed in solution over an extended period, indicating the high quality of the exfoliated nanosheets. Following hydrothermal treatment, the fibrous AlOOH was uniformly integrated with the GNSs, as confirmed by TEM imaging (e). This modification significantly enhanced the water wettability of the GNSs, facilitating their uniform dispersion within the castable material. The improved dispersion contributed to enhanced thermal shock resistance of the castables. Notably, the incorporation of 0.5 wt.% GNSs into the castables resulted in a 17% increase in the residual strength ratio compared to the pristine samples (f), demonstrating the effectiveness of the surface modification and the potential of GNSs as a reinforcement material in refractory applications. Furthermore, Liu et al. [
150] used a three-roll mill method to exfoliate flake graphite in a phenolic resin (PF) medium for the synthesis of the GNSs/PF composite, which were then introduced into MgO−C bricks (a). A mathematical model was established to show the relationship between graphite flake thickness and the number of exfoliation cycles (the inset of a), indicating that satisfactory thickness was achieved after approximately 16 exfoliation cycles. The SEM image (b) confirmed that the thickness ranged between 8.59–18.26 nm, and the TEM image (c) further verified this result. Comparative tests were conducted on refractory samples with 8 wt.% flake graphite (sample S1) and those with the GNSs/PF composite (carbon content approximately 2 wt.%). The results showed that samples with the composite exhibited superior high-temperature flexural strength (d) and oxidation resistance (e) despite having lower carbon content.
. (<b>a</b>) Schematic diagram of liquid-phase shear exfoliation process and the preparation of carbon-containing MgO castables. (<b>b</b>) TEM and (<b>c</b>) AFM images of GNSs exfoliated by kitchen blender under the optimal processing parameters. (<b>d</b>) Digital photographs of GNSs suspension after 15 days of resting. (<b>e</b>) TEM image of GNSs/AlOOH composite powders prepared at the optimal conditions (190 °C and pH = 3). (<b>f</b>) HMOR values of castable samples measured at 1400 °C for 30 min. And (<b>e</b>) CMOR and residual strength ratios of castable specimens after three thermal shock cycles at 1100 °C [
149]. (<b>a</b>–<b>f</b>) Copyright 2024, Elsevier.
. (<b>a</b>) Preparation for GNSs or GNSs/PF mixture from flake graphite in PF and further obtain low carbon MgO−C refractories, and mathematical model drawing the results of exfoliating flake graphite. (<b>b</b>) SEM images of the horizontal and vertical morphologies of products with 10 wt. % flake graphite exfoliated from flake graphite in PF with three-roll milling for 16 cycles. (<b>c</b>) HRTEM image of the GNSs with diffraction pattern (inset). (<b>d</b>) HMOR of the prepared MgO−C bricks after heat-treatment at 1350 °C for 0.5 h. And (<b>e</b>) percentage oxidation area of MgO−C bricks after 1h oxidation at 1400 °C [
150]. (<b>a</b>–<b>e</b>) Copyright 2023, Elsevier.
In summary, introducing nanocarbon can significantly improve the mechanical properties and thermal shock resistance of CCRs. However, the application of nanocarbon materials also faces several shortcomings: (1) Direct addition tends to cause agglomeration, making it difficult to disperse uniformly in the matrix. (2) The structural collapse of nanocarbon materials often occurs due to reactions between carbon and anti-oxide vapors (Al (g), Si (g), and SiO (g)) at high coking temperatures. And (3) the preparation of graphene composite powder by mechanical exfoliation has a low yield, complex process, and high cost, which makes it challenging to implement in practical production applications. Therefore, to further enhance the reinforcement effect of nanocarbon materials, it is imperative to explore new methods to improve their structural stability and minimize related interfacial reactions. provides a summary of the application of nanocarbons in CCRs and their associated properties.
. Summary of the application of nanocarbons in CCRs and their effects on the properties.
3. Nano Non-Oxides Containing Refractories
Non-oxide ceramic phases, such as nitrides, carbides, and MAX phases, considerably improve the slag corrosion resistance, oxidation resistance, and thermomechanical properties of CCRs [
152,
153,
154,
155,
156,
157,
158,
159,
160,
161,
162,
163]. Hexagonal boron nitride (h-BN), which shares a structure similar to graphite, is widely utilized as a reinforcement agent in CCR composites because of its outstanding thermal stability and oxidation resistance [
164,
165,
166,
167,
168].
Liang et al. [
166] substituted alumina fine powder with h-BN in refractory preparation, investigating how varying h-BN content and heat treatment temperature impacted the samples’ physical properties and thermal shock resistance. The findings revealed that with an increase in h-BN content, the mechanical properties of the refractory diminished due to h-BN’s chemical inertness, which hindered composite sintering. Nevertheless, thermal shock tests indicated that the sample containing 20 wt.% h-BN exhibited the optimal thermal shock resistance attributed to the weak-bonding interface between h-BN and the matrix. Ji et al. [
169] explored the effects of commercial h-BN sheet content and particle size on the comprehensive properties of low-carbon Al
2O
3−C refractories. They found that adding h-BN decreased the diameter of SiC whiskers, thereby enhancing their strengthening effect and improving resistance to crack propagation, oxidation, and thermal shock. The best overall properties were achieved with the addition of 0.5 wt.% h-BN sheets. The size of h-BN significantly influenced the mechanical properties: larger-sized h-BN (1–10 μm) improved flexural strength, whereas smaller-sized h-BN (~0.1 μm) enhanced thermal shock resistance. Zheng et al. [
170] prepared h-BN composite powders using a magnesiothermic reduction combustion synthesis route and incorporated them into low-carbon Al
2O
3−C refractories. The introduction of h-BN resulted in the in situ formation of spinel and AlN whiskers, leading to crack deflection and branching into finer cracks. When 1.0 wt.% h-BN composite powders were added, the refractories exhibited the highest residual strength retention (~35%). Besides h-BN’s chemical inertness, the in situ formation of spinel and AlN whiskers, coupled with reduced pore size, significantly enhanced slag corrosion resistance. As the composite powder addition increased from 0 to 2 wt.%, the slag corrosion index dropped from 19.74% to 8.15%. Moreover, Fan et al. [
171] addressed the challenge of reduced oxidation and thermal shock resistance in low-carbon MgO−C refractories by enhancing them with nano-layered BN-modified graphite prepared using a molten salt method. Their findings indicated that incorporating 1–4 wt.% of this modified graphite improved the mechanical properties of MgO−C refractories. This improvement was due to enhanced bonding between the matrix and in situ generated rod-like Mg
2SiO
4, columnar MgAl
2O
4, and Mg
3B
2O
6 liquid phases, which filled the pores and increased strength. Additionally, the oxidation index of MgO−C refractories with 4 wt.% nano-layered BN-modified graphite decreased by 34% compared to unmodified samples. This enhancement was attributed to the filling effect of in situ generated Mg
2SiO
4 and the protective layer formation of Mg
3B
2O
6 derived from BN oxidation.
Compared to traditional h-BN nanosheets, rod-like h-BN is better suited for applications requiring high thermal conductivity, high strength and high-temperature stability. Li et al. [
172] synthesized rod-like h-BN composed of numerous small nanosheets through a precursor catalytic pyrolysis process and used it to create a novel rod-like h-BN modified low-carbon Al
2O
3−C refractory. The SEM image (a) revealed that the synthesized h-BN had a rod-like morphology with uniform size distribution and an average diameter of approximately 2 μm. The TEM image showed that the rod-like h-BN consisted of many small nanosheets (b), and HRTEM results displayed a layered structure with clear lattice fringes and an interplanar spacing of about 0.345 nm, corresponding to the (002) plane of h-BN (c). Furthermore, adding rod-like h-BN significantly increased the high-temperature slag-wetting angle of the refractory. As depicted in d–f, the contact angle of the sample with 3 wt.% flake graphite gradually decreased to 27.6° within 720 seconds. However, replacing just 1 wt.% flake graphite with rod-like h-BN resulted in a contact angle decrease to only 55.8° over the same period. g showed the change in slag height over time, indicating that as the slag spread on the sample surface, the height decreased, and the contact angle followed a similar trend. These results demonstrated that the addition of rod-like h-BN improved the slag penetration resistance of the refractory.
. (<b>a</b>) SEM image, (<b>b</b>) TEM image, and (<b>c</b>) HRTEM image of the as-synthesized h-BN sample fired at 1200 °C. Evolution of the molten slag wetting process on the surface of sample G3 with (<b>d</b>) 3 wt.% flake graphite and sample BN1 with (<b>e</b>) 2 wt.% flake graphite and 1 wt.% rod-like h-BN. And (<b>f</b>) evolution of the contact angle and (<b>g</b>) the apparent height of the molten slag on the surface of sample G3 and sample BN1 [
172]. (<b>a</b>–<b>g</b>) Copyright 2024, Elsevier.
SiC nanowhiskers (SiC
w) are known for their high melting point, excellent corrosion resistance, and chemical stability. Chen et al. [
173] investigated the effects of different carbon sources on lightweight Al
2O
3−C refractories containing silicon additives. They found that samples using highly reactive microcrystalline graphite produced more SiC
w in the microporous corundum aggregates compared to those using flake graphite. The increased SiC
w content resulted in a denser and more interwoven microporous aggregate/matrix interface structure, enhancing the performance of the refractories. This confirmed that utilizing highly reactive graphite along with silicon-containing antioxidant powders can significantly improve the mechanical properties of Al
2O
3−C refractories. Zhen et al. [
174] developed an in situ growth method for SiC
w by adding catalysts to enhance the performance of MgO−Al
2O
3−C (MAC) refractories. Their results showed that adding 0.8 wt.% Ni(NO
3)
2 catalyst led to the highest performance, with CCS and CMOR values of 56.50 MPa and 10.52 MPa, respectively. The thermal shock and oxidation resistance of MAC refractories were also enhanced through crack deflection and bridging mechanisms induced by SiC
w. Chen et al. [
175] successfully synthesized SiC
w using rice husk powders and attempted to reduce the flake graphite content in refractories by adding the synthesized SiC
w. The results indicated that the addition of SiC
w significantly affected the microstructure and mechanical properties of MgO−C refractories with different graphite contents. Introducing SiC
w promoted the generation and growth of ceramic phases in MgO−C refractories. The addition of 1 wt.% SiC
w allowed for a reduction of 1 wt.% graphite content. Furthermore, the synergistic effect of the introduced SiC
w and the generated ceramic phases improved the thermal shock resistance and oxidation resistance of the refractories.
In addition to the in situ growth and direct addition of SiC
w in refractories, forming composite powders with SiC whiskers and other materials also enhances refractory performances. Li et al. [
176] synthesized SiC nanofiber-coated graphite flakes at a relatively low temperature of 1623 K through an in situ catalytic reaction using Co(NO
3)
2·6H
2O as the catalyst precursor. Al
2O
3−C castables incorporating these SiC nanofiber-coated graphite flakes exhibited a 73.1% higher residual CMOR ratio after thermal shock testing, 20.0% lower oxidation, and 43.5% less slag corrosion compared to reference samples with pristine graphite. Liu et al. [
177] produced graphite-SiC
w composite powders using a salt-assisted synthesis method involving Si powders, graphite, and a molten salt medium. SiC whiskers, measuring 10–50 nm in length, formed on the surface of the flake graphite, increasing the oxidation activation energy of the graphite−SiC
w composite powder. The SiC cladding layer reacted with slag at high temperatures, enhancing the viscosity of the liquid, thus providing the samples with improved oxidation and slag resistance. Similarly, Ban et al. [
178] synthesized ZrB
2−SiC
w composite powders using a microwave-assisted carbo/borothermal reduction method. SEM images and EDS results of the as-prepared samples (a) revealed that the SiC
w were very fine and uniformly distributed with ZrB
2. As shown in b, the residual CMOR slightly increased with the addition of ZrB
2−SiC
w composite powders after the thermal shock test, maintaining high residual strength ratios of 65% to 85%. This improvement was primarily due to the low thermal expansion coefficient and good thermal conductivity of ZrB
2−SiC
w. The slag corrosion test setup is illustrated in c, and the post-test sample photos are shown in d. The lower half of the sample in d indicated that the oxidation layer of the sample with 6 wt.% ZrB
2−SiC
w was thinner (1.8 mm) compared to the pristine sample (2.5 mm), demonstrating that adding ZrB
2−SiC
w composite powders significantly enhanced the corrosion and oxidation resistance of the refractories.
. (<b>a</b>) Microscopic morphology of the prepared ZrB<sub>2</sub>−SiC<sub>w</sub> composite powder. (<b>b</b>) Residual strength ratio and CMOR of samples after thermal shock test (<b>c</b>) The corrosion testing equipment. And (<b>d</b>) cross−section of samples after corrosion test [
178]. (<b>a</b>–<b>d</b>) Copyright 2020, Elsevier.
As a new type of nanomaterial, ternary non-oxides can also enhance the performances of Al
2O
3−C refractories. These additives, instead of metal additives, are preferred due to their high elastic modulus, thermal conductivity, excellent thermal shock resistance, and damage tolerance. Liu et al. [
179] replaced Al with Ti
3AlC
2 to prepare low-carbon Al
2O
3−C refractories. SEM images showed the presence of Ti
3AlC
2, SiC
w, and metastable Ti
3Al
1−xC
2 formed by the selective oxidation of Ti
3AlC
2 in the refractory matrix. The SEM and EDS results (a–c) confirmed the presence of Ti
3AlC
2 in the inner part, with a significant reduction of Al in the outer regions, suggesting the forming of Ti
3Al
1−xC
2. Load−displacement curves of samples coked at different temperatures were shown in d. The displacement of samples with Al was much greater at 800 °C and 1200 °C compared to the samples, which showed greater displacement after firing at 1600 °C. This was attributed to the volume expansion of Ti
3AlC
2 during oxidation, forming a dense structure that improved the mechanical properties of Al
2O
3−C refractories. Additionally, the Ti
3AlC
2-added samples demonstrated better oxidation resistance compared to the samples with Al powders (e,f). Chen et al. [
180] introduced Cr
2AlC powder into Al
2O
3−C refractories and investigated its effect on corrosion resistance. The cross-section of the samples with different Cr
2AlC contents after a crucible corrosion test at 1600 °C is shown in g. The primary corrosion areas were at the slag/refractory interface and the slag/refractory/air interface. Calculation results of the slag penetration area revealed that Cr
2AlC addition reduced the penetration index from 32.61% to 19.34%. This improvement was attributed to the dissolution of Al
2O
3 and Cr
2O
3 from the original Cr
2AlC, which increased the local slag viscosity and suppressed further slag penetration into the refractory. Moreover, the HMOR of the Al
2O
3−C sample with 5 wt.% Cr
2AlC increased from 3.14 MPa to 5.15 MPa. Yu et al. [
25] achieved the in situ generation of flake Al
4O
4C and multi-walled carbon nanotubes in Al
2O
3−C refractories by introducing Al
4SiC
4. This ternary non-oxide, known for its exceptional stability, facilitated the development of ceramic phases. Lou et al. [
181] synthesized nano-MgSiN
2 using a molten salt method and then prepared Al
2O
3−C refractories with MgSiN
2 as an additive. At 1500 °C, nano-MgSiN
2 underwent phase reconfiguration to form Mg(g) and Si
3N
4(s), enhancing the interfacial bonding strength between aggregates and the matrix. As a result, the refractories’ mechanical properties and thermal shock resistance were significantly improved.
. (<b>a</b>,<b>b</b>) SEM images of Al<sub>2</sub>O<sub>3</sub>−C samples with Ti<sub>3</sub>AlC<sub>2</sub>. (<b>c</b>) EDS spectra of the points in (<b>b</b>). (<b>d</b>) Load−displacement curves of Al<sub>2</sub>O<sub>3</sub>−C samples fired at different temperatures. Optical photographs of Al<sub>2</sub>O<sub>3</sub>−C samples with (<b>e</b>) aluminum powder and (<b>f</b>) Ti<sub>3</sub>AlC<sub>2</sub> after oxidation test at 1400 °C for 0.5 h [
179]. And (<b>g</b>) cross-section images of the samples with different Cr<sub>2</sub>AlC contents after the corrosion test at 1600 °C (AC−9: 9 wt.% graphite, ACr−2.5: 6.5 wt.% graphite and 2.5 wt.% Cr<sub>2</sub>AlC, and ACr−5: 4 wt.% graphite and 5 wt.% Cr<sub>2</sub>AlC) [
180]. (<b>a</b>–<b>f</b>) Copyright 2024, Elsevier; (<b>g</b>) Copyright 2021, Elsevier
Nano non-oxides have excellent thermal stability and corrosion resistance, showing potential for improving oxidation resistance and slag corrosion resistance of CCRs. However, nitrides and carbides have low toughness and are prone to cause brittle fracture [
182,
183,
184,
185,
186,
187,
188]. The in situ formation of nitrides and carbides requires high heat-treatment temperatures and proper oxygen partial pressure, leading to the massive escape of vapors, which can result in structural degradation and strength loss of CCRs. The stability of the MAX phase at elevated temperatures is poor, and its structure usually collapses due to the phase transformation. Thus, future studies should focus on addressing these inadequacies to enhance the performances of CCRs containing nano non−oxides.
4. Nano Oxides Containing Refractories
Oxides play a crucial role in manufacturing metallic materials, petrochemical equipment, wear-resistant machinery, and other applications within the metallurgical industry [
189,
190,
191,
192,
193,
194,
195]. Notably, oxides such as alumina (Al
2O
3), magnesia (MgO), spinel (MgAl
2O
4), and zirconia (ZrO
2) are highly valued for their exceptional resistance to extreme environments, molten steel, and slags [
196,
197,
198,
199,
200,
201]. These materials are integral in these industries due to their durability and stability under harsh conditions, making them indispensable in settings where high temperature and corrosive materials are constantly challenging.
Roungos and Aneziris [
202] explored the integration of Al
2O
3 sheets with carbon nanotubes (CNTs) in Al
2O
3−C refractories, finding that this combination of nanoscale powders led to enhanced thermal shock performance. The dual incorporation leveraged the mechanical strength of CNTs and the thermal stability of Al
2O
3 to improve the refractory’s resilience against rapid temperature changes. Ghasemi-Kahrizsangi et al. [
203] observed that the addition of nano Al
2O
3 helped to fill the intergranular voids between MgO and graphite particles, thus promoting the densification of MgO−C refractories. They noted that the formation of new phases such as MgAl
2O
4, AlN, and Al
4C
3 in samples with 6 wt.% of both nano and micro Al
2O
3 particles enhanced the cold crushing strength (CCS), oxidation resistance, and slag resistance of these refractories. Moreover, samples containing nano-Al
2O
3 exhibited superior properties attributed to the intrinsic characteristics of Al
2O
3 nanoparticles, including significant surface effects, size effects and higher activity. Luo et al. [
82] and Zhu et al. [
204] developed low-carbon MgO−C refractories by incorporating a Ni-containing catalytic precursor and Al powders, leading to the in situ formation of MgO whiskers. A droplet containing Ni at the tips of some MgO whiskers suggested that the vapor−liquid−solid process controlled the growth of these whiskers. The reinforcement from these in situ formed MgO whiskers enhanced the mechanical properties of the samples with the catalyst, resulting in higher CMOR values and significantly greater displacement compared to samples without the Ni catalyst. Das et al. [
205] investigated the impact of adding nanocrystalline MgAl
2O
4 spinel to MgO−C refractories. Their findings revealed that incorporating nano-MgAl
2O
4 spinel in MgO−C bricks improved physical and chemical properties, underscoring the potential for applications in the steel and refractory industries. This improvement was likely due to the spinel’s ability to enhance the refractory’s structural integrity and chemical stability under high temperatures.
Gu et al. [
206] synthesized MgO-based aggregates with in situ formation of nanoscale MgAl
2O
4 grains at the boundaries and on the surfaces of MgO grains, as shown in a. The study detailed in b demonstrated that with the inclusion of nanoscale Al
2O
3 powders ranging from 0 to 20 wt.%, the CCS initially increased from 102.5 MPa to a peak of 302.7 MPa before decreasing to 260.3 MPa. This trend suggests that the optimal in situ formation of MgAl
2O
4 in MgO-based aggregates significantly enhanced their strength. Additionally, the residual strength of samples after thermal shock tests followed a similar pattern to the CCS, confirming that the appropriate formation of MgAl
2O
4 enhanced thermal shock resistance, as illustrated in c. This improvement is attributed to the thermal mismatch between MgAl
2O
4 and MgO, which likely caused microcracks that released residual stress, thereby arresting stress around the main crack tip (shown in e). Consequently, the introduction of nanoscale MgAl
2O
4 improved the physical properties and the thermal shock resistance of MgO−C refractories. Furthermore, Gu et al. [
207] developed modified MgO aggregates using a nano-ZrO
2-alcohol suspension and a vacuum impregnation method, resulting in aggregates with excellent thermal shock resistance. The integration of these modified aggregates significantly bolstered the thermal shock resistance of MgO−C refractories. This enhancement is primarily attributed to the pinning effect of particles and the phase transformation toughening effect of nano-ZrO
2. Moreover, nano-ZrO
2 particles facilitated the sintering of the matrix and the formation of the AlN ceramic phase, further improved the HMOR of the refractories. This comprehensive approach underscores the importance of material engineering at the nanoscale to enhance the performance characteristics of refractory materials in high-temperature applications.
. (<b>a</b>) SEM microphotographs of samples with 19 wt.% MgAl<sub>2</sub>O. (<b>b</b>) CCS of samples after coked at 1500 °C. (<b>c</b>) Residual CCS and residual CCS ratio of samples after coked at 1500 °C. (<b>d</b>) Schematic diagram of in situ formation of nano-sized MgAl<sub>2</sub>O<sub>4</sub> in magnesia aggregates. And (<b>e</b>) schematic of crack propagation in samples with the addition of MgAl<sub>2</sub>O<sub>4</sub> [
206]. (<b>a</b>–<b>d</b>) Copyright 2019, Elsevier.
Nanosized oxides are highly reactive and can promote the formation of new ceramic phases, enhancing the performance of MgO−C refractories. Ghasemi-Kahrizsangi et al. [
208] reported that incorporating nano-ZrSiO
4 in MgO−C refractories led to the creation of new ceramic phases such as zirconium carbide (ZrC), forsterite (2MgO·SiO
2), and enstatite (MgO·SiO
2). The addition of nano-ZrSiO
4 increased the bulk density by forming the low-melting phase (MgO·SiO
2). Additionally, the phases 2MgO·SiO
2 and MgO·SiO
2 enveloped the free graphite phase, along with the high oxidation resistance phase ZrC, resulting in improved oxidation resistance of MgO−C refractories. The formation of these new ceramic phases filled the pores and voids, preventing slag penetration and enhancing slag corrosion resistance. Furthermore, the impact of adding TiO
2 nanoparticles on the microstructure and properties of MgO−C refractories was investigated [
209]. The introduction of TiO
2 nanoparticles resulted in the formation of TiN, TiC, and TiCN phases. These phases enhanced the mechanical, physical, and thermo-chemical properties of the samples through several mechanisms: (i) converting free graphite into carbide and nitride phases, (ii) reducing porosities within the matrix, and (iii) improving the firing process due to the presence of nanoparticles. This enhancement underscores the significant role that nanotechnology plays in advancing refractory materials, especially in settings that require improved durability and resistance to harsh conditions.
Chen et al. [
210] demonstrated that the addition of nanosized ZrO
2−Al
2O
3 composite powders can significantly reduce porosity and optimize the pore structure in MgO−C refractories, thanks to their excellent filling capabilities, ultimately enhancing the oxidation resistance and slag corrosion resistance of the refractories. The SEM image depicted in a illustrates the sample with 0.5 wt.% ZrO
2−Al
2O
3 composite powders had a well-bonded matrix of plate-like MgO aggregates and uniformly dispersed ZrO
2 particles. MgO−C samples containing these nano ZrO
2−Al
2O
3 composite powders exhibited higher residual strength ratios after thermal shock tests (b), demonstrating that the composite powders had a positive impact on thermal shock resistance. The cross-sections and corresponding oxidation indices of different samples after oxidation tests, shown in c–f, clearly revealed that with increasing content of nano ZrO
2−Al
2O
3 composite powder, the oxidation indices of the samples gradually decreased. This trend highlights the positive effect of the composite powders on the oxidation resistance of low-carbon MgO−C refractories. Furthermore, after slag corrosion tests, the corrosion indices of the samples, as shown in g, indicated that adding composite powders effectively improved the slag corrosion resistance of the low-carbon MgO−C refractories. This comprehensive enhancement in performance attributes underscores the significant role that nanosized composite powders play in advancing the durability and functionality of refractory materials under severe operating conditions.
. (<b>a</b>) SEM micrographs of the polished composite powder with 0.5 wt.% ZrO<sub>2</sub>−Al<sub>2</sub>O<sub>3</sub> after calcinated at 1400 °C (FM: fused magnesia). (<b>b</b>) CMOR and residual strength ratio of specimens after thermal shock tests. (<b>c</b>–<b>e</b>) Cross-sections of MgO−C specimens fired at 1400 °C for 3 h in air. (<b>f</b>) Oxidation index of various specimens after oxidation tests. And (<b>g</b>) slag corrosion index of MgO−C specimens after slag corrosion tests [
210]. (<b>a</b>–<b>g</b>) Copyright 2021, Elsevier.
In addition to the aforementioned studies, incorporating nanosized oxides is regarded as a practical and effective approach to enhance the thermal shock resistance and slag corrosion resistance of CCRs. To achieve this, it is essential to choose oxide materials with appropriate phase compositions and thermal expansion coefficients, control the in situ formation of new ceramic phases and thereby improve the overall performance of CCRs.
5. Conclusions
Traditional CCRs possess excellent thermal shock resistance and slag corrosion resistance. However, the high carbon content limits their application due to carbon oxidation and high thermal conductivity. Merely reducing the carbon content results in poor high-temperature service performances. To address this issue, nanomaterial-modified matrix has been developed in CCRs. Due to their unique dimensional structures and physical/chemical properties, nanomaterials as reinforcement additives can significantly improve service performances through deliberate design. Desirable features are achieved owing to the nano-architectonics of nanomaterials in terms of their unique size, shape, and composition. Three classes of nanomaterials are primarily taken into consideration for dispersion in the CCRs matrix: (1) Nanocarbon additives, including carbon black, carbon nanotubes, and graphite nanoplatelets, which are categorized as 0D, 1D and 2D, respectively, depending on their dimensions. (2) Nano oxides, come in powders such as Al
2O
3, MgO, MgAl
2O
4 and ZrO
2. And (3) nano non-oxide additives, which are classified as nitride and carbide. Introducing nanocarbon materials into the matrix of refractories can improve the mechanical properties and thermal shock resistance of CCRs. Due to the small particle size and lower density of these nanomaterials, the compactness of refractories is enhanced, and a more effective surface area is achieved. However, nanocarbon materials possess poor oxidation resistance and high reactive activity, which can induce structural alteration. Both direct addition and in situ generation of nano-oxide additives can fill pores and improve the oxidation resistance of refractories, and the newly formed ceramic phases enhance slag resistance. Nano non-oxide additives offer better oxidation and slag corrosion resistance for CCRs, but structural collapse can cause a loss of service performance.
The current status of nanomaterial-reinforced CCRs is reviewed based on available research articles. The future of nanomaterial incorporation in CCRs is very promising. With the continuous improvement in high-performance steel material requirements, recent studies have aimed to understand the behavior of CCRs reinforced with various types of nanomaterials. However, several factors need to be considered in this research field:
- The reinforcement mechanisms of nanomaterials include energy dissipation mechanisms, “crack deflection,” “pulling out,” and “bridging” mechanisms, which are related to the dimensionality of the nanomaterials. Often, the synergistic effects of multiple mechanisms produce the final results. The precise synergy of different mechanisms and the contribution of any individual mechanism remain unclear. Therefore, designing high-performance nanosized additives should consider nanomaterials physical and chemical properties and their reinforcement mechanisms to optimize service performances.
- The full potential of nanosized additives, such as carbon nanotubes and graphene nanosheets, is not yet utilized. These additives are consumed and transformed into ceramic phases during the firing process, sacrificing their intrinsic advantages. Functionalizing them and inhibiting the high-temperature reactions are interesting and challenging research areas.
- Due to the large surface area of nanomaterials, they tend to agglomerate. The literature describes two methods for deagglomeration: in situ synthesis and the addition of nanomaterial-oxide nanocomposite additives. However, these strategies need further investigation and optimization as they are time and resource-consuming, and a new method needs to be developed for this purpose.
- Despite significant improvement of CCRs properties shown by nanoscale materials addition, the dispersion and retention properties of nanoscale additives and their stability at elevated temperatures and in corrosive environments, require further research. Solving this issue has the potential to significantly improve both the mechanical properties and service life of nanomaterial-reinforced CCRs.
- The use of nanoscale materials in carbon-bonded refractories is hindered by their extremely high production costs. Nanocomposites incur additional expenses due to their costly production and processing. However, increasing demand and production will help to reduce the cost of nanosized additives.
Although the application of nanoscale additives poses various challenges, ongoing research into improved dispersion techniques, stability-enhancing nanomaterials, reinforcement mechanisms and cost reduction will pave the way for their large-scale application in various fields. Despite these challenges, nanoscale materials show promising prospects for significantly improving the service performances of CCRs.
Author Contributions
Conceptualization, F.L.; Investigation, F.L., H.G. and J.L.; Writing—Original Draft Preparation, F.L.; Writing—Review & Editing, F.L. and J.L.; Supervision, F.L. and H.Z.; Project, F.L. and H.Z.; Funding Acquisition, H.Z.
Ethics Statement
Not applicable.
Informed Consent Statement
Not applicable for studies not involving humans.
Funding
This research was funded by National Natural Science Foundation of China grant number 52072274, 52272021, 52232002 and U23A20559.
Declaration of Competing Interest
The authors declare that they have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.
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