Manufacturing method of high-toughness TiC particle reinforced martensitic wear-resistant steel plate

Abstract

The present invention belongs to the field of engineering materials and proposes a method for manufacturing high-toughness TiC particle-enhanced martensitic wear-resistant steel plates. Based on the steps of converter smelting, refining outside the furnace, protective casting, continuous casting billet heating, rolling and heat treatment, the casting temperature is lowered, high-permeability rolling is performed and the rolling compression ratio is set to control the size of high-toughness TiC particles to 1.0-2.5μm. This method can stably produce high-toughness TiC particle-enhanced martensitic wear-resistant steel plates with a hardness of 400-450HB, a tensile strength of 1200-1350MPa, an elongation of 10%-13%, an impact absorption energy of more than 35J at -20℃, and a wear resistance of more than 1.5 times that of traditional wear-resistant steels of the same hardness.

Description

Technical Field

[0001] The present invention relates to the field of engineering materials, and in particular to a method for manufacturing a high-toughness TiC particle reinforced martensitic wear-resistant steel plate. Background Art

[0002] Traditional low-alloy wear-resistant steels typically utilize a single-phase martensite structure. Their wear resistance is directly related to the hardness of the martensite matrix. The primary approach to improving wear resistance is to increase the carbon content and martensite hardness. However, increasing the carbon content and hardness of the steel significantly deteriorates its workability and weldability, making it difficult to meet the requirements of equipment manufacturing. Introducing ultra-hard TiC particles into the harder martensite matrix enhances wear resistance, achieving superior wear resistance at the same hardness. However, the addition of large amounts of TiC particles can affect mechanical properties, particularly elongation and toughness. Wear-resistant steel is widely used in industries such as metallurgy and construction, and some workpieces have complex shapes and require bending during fabrication. Therefore, both toughness and formability are critical requirements for the steel. TiC particle size significantly influences toughness. While particle size refinement can improve toughness, small particles are more easily removed by abrasives during wear. Therefore, it is crucial to find an optimal particle size range that ensures both good wear resistance and high toughness. Summary of the Invention

[0003] The present invention aims to provide a method for manufacturing high-toughness TiC particle-reinforced martensitic wear-resistant steel plates. The resulting steel plates exhibit a hardness of 440-460 HB, a tensile strength of 1300-1400 MPa, an elongation of 10%-13%, an impact energy absorption of over 35 J at -20°C, and wear resistance over 1.5 times that of conventional wear-resistant steels of the same hardness. A rolling process combining appropriately reduced casting temperatures, high-penetration rolling, and a reasonable rolling reduction ratio is proposed to achieve stable industrial production of high-toughness TiC particle-reinforced martensitic wear-resistant steel plates.

[0004] The technical solution of the present invention:

[0005] A method for manufacturing a high-toughness TiC particle-reinforced martensitic wear-resistant steel plate comprises the following steps: converter smelting, refining outside the furnace, protective casting, continuous casting billet heating, rolling and heat treatment; the chemical composition of the prepared steel plate is as follows by weight: C: 0.20%-0.40%; Mn: 0.50%-1.00%; Si: 0.20%-0.30%; Mo: 0.20%-0.50%; Ti: 0.30%-0.80%; Cr: 0.50%-1.00%; N≤0.004%; S≤0.002%; P≤0.008%; the remainder being Fe and unavoidable impurity elements; wherein, the casting temperature is lowered in the protective casting; and high-penetration rolling and a set rolling compression ratio are adopted in the rolling to achieve control of the high-toughness TiC particle size within a range of 1.0-2.5 μm.

[0006] The rolling process adopts a three-stage controlled rolling process, including recrystallization zone rolling, austenite non-recrystallization zone rolling, and two-phase non-recrystallization zone rolling. The recrystallization zone rolling adopts high-permeability rolling, with the surface temperature of the continuous casting billet between 920-960°C, the core temperature of the slab between 1000-1100°C, and the deformation between 30%-40%. The austenite non-recrystallization zone rolling starts at a temperature between 900-940°C, with a deformation between 40%-70%. The two-phase non-recrystallization zone rolling starts at a temperature between 840-860°C, with a deformation between 30%-50%. The deformation is the change in deformation at each stage divided by the initial thickness at each stage.

[0007] The deformation amounts of the austenite non-recrystallized area and the two-phase non-recrystallized area account for 50%-60% of the total deformation amount.

[0008] The total rolling reduction ratio of the three-stage controlled rolling is 5-7.5.

[0009] High-quality molten steel is selected during converter smelting, and its chemical composition is prepared by eliminating niobium microalloying and adding 0.20wt%-0.50wt% of Mo and 0.50wt%-1.00wt% of Cr based on the mass of the molten steel to improve hardenability; and the content of harmful elements is controlled to be: N≤0.004wt%, S≤0.002wt%, and P≤0.008wt%.

[0010] The lowering of the casting temperature specifically involves setting the tundish superheat at 20-30°C. Under the premise of ensuring that casting can be completed smoothly, lowering the casting temperature can refine the particle size in the ingot, reduce the probability of coarse particles, and protect the casting throughout the process.

[0011] Specifically, high-permeability rolling involves using the mill's high-pressure descaling device to descale and cool the slab after it leaves the heating furnace, maintaining a surface temperature of 920-960°C and a core temperature of 1000-1100°C. High-permeability rolling ensures that the core particles of the steel plate are fully refined, improving the mechanical properties of the core.

[0012] The ultimate goal of this method is to control the particle size between 1.0-2.5μm. By setting a reasonable rolling compression ratio, the particle size can be regulated. Particle refinement can improve toughness, but too small particles will reduce wear resistance. The three-stage controlled rolling is adopted, in which high-permeability rolling is adopted for recrystallization zone rolling. The surface temperature of the continuous casting billet is 920-960℃, and the temperature of the core of the slab is 1000-1100℃. The deformation in this stage is between 30% and 40%. The effect is: the metal fluidity is good in the high-temperature stage, which can destroy the grain boundary morphology of the particles and make the particle distribution more uniform. The starting rolling temperature of the austenite non-recrystallization zone rolling is between 900-940℃, and the deformation in this stage is between 40% and 70%. The deformation temperature in this stage is low, and the material rheological stress is high, which can effectively crush micron-sized TiC particles. The starting rolling temperature in the two-phase non-recrystallized zone is between 840-860°C, and the deformation in this stage is between 30% and 50%. Deformation in this temperature range effectively breaks up micron-sized TiC particles and simultaneously induces strain precipitation. The large amount of nano-precipitation significantly improves the mechanical properties of the steel. The deformation in the austenite non-recrystallized zone and the two-phase non-recrystallized zone accounts for 50%-60% of the total deformation, and the total compression ratio is between 5-7.5.

[0013] The quenching temperature in the heat treatment is 850-900° C., the heating time is 0.5-2 hours, the tempering temperature is 180-220° C., and the holding time is 1-3 hours.

[0014] The beneficial effects of the present invention are as follows: through the manufacturing method of the high-toughness TiC particle reinforced martensitic wear-resistant steel plate of the present invention, the size of the high-toughness TiC particles is controlled within 1.0-2.5 μm, and the hardness, tensile strength, elongation and impact absorption energy of the prepared steel plate are all improved; the steel plate hardness is 440-460 HB, the tensile strength is 1300-1400 MPa, the elongation is 10%-13%, the impact absorption energy at -20°C can reach more than 35 J, and the wear resistance is more than 1.5 times that of traditional wear-resistant steel with the same hardness. DETAILED DESCRIPTION

[0015] Comparative Example 1: The chemical composition of the prepared steel plate is as follows by weight: C: 0.30%; Mn: 0.8%; Si: 0.25%; Mo: 0.40%; Ti: 0.60%; Cr: 0.80%; N≤0.004wt%; S≤0.002%; P≤0.008%; the remainder is Fe and unavoidable impurity elements.

[0016] High-quality molten steel is used during smelting, and its chemical composition is optimized: niobium microalloying is eliminated, and 0.40wt% Mo and 0.80wt% Cr are added to the molten steel to improve hardenability; the content of harmful elements is controlled: N≤0.004wt%, S≤0.002wt%, P≤0.008wt%; the tundish superheat is 45°C.

[0017] The continuous casting slab is heated in a heating furnace at a temperature of 1250°C for 4 hours;

[0018] The plate mill utilizes a high-permeability three-stage rolling process. After the continuous casting slab leaves the heating furnace, the mill's high-pressure descaling device descales and cools the slab, maintaining a surface temperature of 960°C and a core temperature of approximately 1100°C. Finishing rolling begins at 920°C and ends at 880°C, with a 35% deformation. The austenite non-recrystallization zone begins at 920°C, with a 35% deformation. The two-phase non-recrystallization zone begins at 850°C, with a 20% deformation. The total reduction ratio is 3.

[0019] After rolling, offline heat treatment is carried out, with a quenching temperature of 900°C, a heating time of 1 hour, a tempering temperature of 180°C, and a holding time of 2 hours.

[0020] Comparative Example 2: The chemical composition of the prepared steel plate is as follows by weight: C: 0.30%; Mn: 0.8%; Si: 0.25%; Mo: 0.40%; Ti: 0.60%; Cr: 0.80%; N≤0.004wt%; S≤0.002%; P≤0.008%; the remainder is Fe and unavoidable impurity elements.

[0021] High-quality molten steel is used during smelting, and its chemical composition is optimized: niobium microalloying is eliminated, and 0.40wt% Mo and 0.80wt% Cr are added to the molten steel to improve hardenability; the content of harmful elements is controlled: N≤0.004wt%, S≤0.002wt%, P≤0.008wt%; the tundish superheat is 25°C.

[0022] The continuous casting slab is heated in a heating furnace at a temperature of 1250°C for 4 hours;

[0023] The plate mill utilizes a high-permeability three-stage rolling process. After the continuous casting slab leaves the heating furnace, the mill's high-pressure descaling device descales and cools the slab, maintaining a surface temperature of 960°C and a core temperature of approximately 1100°C. Finishing rolling begins at 920°C and ends at 880°C, with a 35% deformation. The austenite non-recrystallization zone begins at 920°C, with a 35% deformation. The two-phase non-recrystallization zone begins at 850°C, with a 20% deformation. The total reduction ratio is 3.

[0024] After rolling, offline heat treatment is carried out, with a quenching temperature of 900°C, a heating time of 1 hour, a tempering temperature of 180°C, and a holding time of 2 hours.

[0025] Comparative Example 3: The chemical composition of the prepared steel plate is as follows by weight: C: 0.30%; Mn: 0.8%; Si: 0.25%; Mo: 0.40%; Ti: 0.60%; Cr: 0.80%; N≤0.004wt%; S≤0.002%; P≤0.008%; the remainder is Fe and unavoidable impurity elements.

[0026] High-quality molten steel is used during smelting, and its chemical composition is optimized: niobium microalloying is eliminated, and 0.40wt% Mo and 0.80wt% Cr are added to the molten steel to improve hardenability; the content of harmful elements is controlled: N≤0.004wt%, S≤0.002wt%, P≤0.008wt%; the tundish superheat is 25°C.

[0027] The continuous casting slab is heated in a heating furnace at a temperature of 1250°C for 4 hours;

[0028] The plate mill utilizes a high-permeability three-stage rolling process. After the continuous casting slab leaves the reheating furnace, the mill's high-pressure descaling device descales and cools the slab, maintaining a surface temperature of 960°C and a core temperature of approximately 1100°C. Finishing rolling begins at 920°C and ends at 880°C, with a deformation of 45%. The austenite non-recrystallization zone begins at 920°C, with a deformation of 75%. The two-phase non-recrystallization zone begins at 850°C, with a deformation of 55%, resulting in a total reduction ratio of 13.7.

[0029] After rolling, offline heat treatment is carried out, with a quenching temperature of 900°C, a heating time of 1 hour, a tempering temperature of 180°C, and a holding time of 2 hours.

[0030] Comparative Example 4: The chemical composition of the prepared steel plate is as follows by weight: C: 0.30%; Mn: 0.8%; Si: 0.25%; Mo: 0.40%; Ti: 0.60%; Cr: 0.80%; N≤0.004wt%; S≤0.002%; P≤0.008%; the remainder is Fe and unavoidable impurity elements.

[0031] High-quality molten steel is used during smelting, and its chemical composition is optimized: niobium microalloying is eliminated, and 0.40wt% Mo and 0.80wt% Cr are added to the molten steel to improve hardenability; the content of harmful elements is controlled: N≤0.004wt%, S≤0.002wt%, P≤0.008wt%; the tundish superheat is 25°C.

[0032] The continuous casting slab is heated in a heating furnace at a temperature of 1250°C for 4 hours;

[0033] The plate mill utilizes a high-permeability three-stage rolling process. After the continuous casting slab leaves the reheating furnace, the mill's high-pressure descaling device descales and cools the slab, maintaining a surface temperature of 960°C and a core temperature of approximately 1100°C. Finishing rolling begins at 920°C and ends at 880°C, with a 30% deformation. The austenite non-recrystallization zone begins at 920°C, with a 40% deformation. The two-phase non-recrystallization zone begins at 850°C, with a 30% deformation, resulting in a total reduction ratio of 3.4.

[0034] After rolling, offline heat treatment is carried out, with a quenching temperature of 900°C, a heating time of 1 hour, a tempering temperature of 180°C, and a holding time of 2 hours.

[0035] Comparative Example 5: The chemical composition of the prepared steel plate is as follows by weight: C: 0.30%; Mn: 0.8%; Si: 0.25%; Mo: 0.40%; Ti: 0.60%; Cr: 0.80%; N≤0.004wt%; S≤0.002%; P≤0.008%; the remainder is Fe and unavoidable impurity elements.

[0036] High-quality molten steel is used during smelting, and its chemical composition is optimized: niobium microalloying is eliminated, and 0.40wt% Mo and 0.80wt% Cr are added to the molten steel to improve hardenability; the content of harmful elements is controlled: N≤0.004wt%, S≤0.002wt%, P≤0.008wt%; the tundish superheat is 25°C.

[0037] The continuous casting slab is heated in a heating furnace at a temperature of 1250°C for 4 hours;

[0038] The plate mill utilizes a high-permeability three-stage rolling process. After the continuous casting slab leaves the reheating furnace, the mill's high-pressure descaling device descales and cools the slab, maintaining a surface temperature of 960°C and a core temperature of approximately 1100°C. Finishing rolling begins at 920°C and ends at 880°C, with a 40% deformation. The austenite non-recrystallization zone begins at 920°C, with a 70% deformation. The two-phase non-recrystallization zone begins at 850°C, with a 50% deformation, resulting in an overall reduction ratio of 11.1.

[0039] After rolling, offline heat treatment is carried out, with a quenching temperature of 900°C, a heating time of 1 hour, a tempering temperature of 180°C, and a holding time of 2 hours.

[0040] Comparative Example 6: The chemical composition of the prepared steel plate is as follows by weight: C: 0.30%; Mn: 0.8%; Si: 0.25%; Mo: 0.40%; Ti: 0.60%; Cr: 0.80%; N≤0.004wt%; S≤0.002%; P≤0.008%; the remainder is Fe and unavoidable impurity elements.

[0041] High-quality molten steel is used during smelting, and its chemical composition is optimized: niobium microalloying is eliminated, and 0.40wt% Mo and 0.80wt% Cr are added to the molten steel to improve hardenability; the content of harmful elements is controlled: N≤0.004wt%, S≤0.002wt%, P≤0.008wt%; the tundish superheat is 25°C.

[0042] The continuous casting slab is heated in a heating furnace at a temperature of 1250°C for 4 hours;

[0043] The plate mill utilizes a high-permeability three-stage rolling process. After the continuous casting slab leaves the heating furnace, the mill's high-pressure descaling device descales and cools the slab, maintaining a surface temperature of 960°C and a core temperature of approximately 1100°C. Finishing rolling begins at 920°C and ends at 880°C, with a 20% deformation. The austenite non-recrystallization zone begins at 920°C, with a 40% deformation. The two-phase non-recrystallization zone begins at 850°C, with a 30% deformation. The total reduction ratio is 3.0.

[0044] After rolling, offline heat treatment is carried out, with a quenching temperature of 900°C, a heating time of 1 hour, a tempering temperature of 180°C, and a holding time of 2 hours.

[0045] Comparative Example 7: The chemical composition of the prepared steel plate is as follows by weight: C: 0.30%; Mn: 0.8%; Si: 0.25%; Mo: 0.40%; Ti: 0.60%; Cr: 0.80%; N≤0.004wt%; S≤0.002%; P≤0.008%; the remainder is Fe and unavoidable impurity elements.

[0046] High-quality molten steel is used during smelting, and its chemical composition is optimized: niobium microalloying is eliminated, and 0.40wt% Mo and 0.80wt% Cr are added to the molten steel to improve hardenability; the content of harmful elements is controlled: N≤0.004wt%, S≤0.002wt%, P≤0.008wt%; the tundish superheat is 25°C.

[0047] The continuous casting slab is heated in a heating furnace at a temperature of 1250°C for 4 hours;

[0048] The plate mill utilizes a high-permeability three-stage rolling process. After the continuous casting slab leaves the reheating furnace, the mill's high-pressure descaling device descales and cools the slab, maintaining a surface temperature of 960°C and a core temperature of approximately 1100°C. Finishing rolling begins at 920°C and ends at 880°C, with a 30% deformation. The austenite non-recrystallization zone begins at 920°C, with a 30% deformation. The two-phase non-recrystallization zone begins at 850°C, with a 30% deformation. The total reduction ratio is 2.9.

[0049] After rolling, offline heat treatment is carried out, with a quenching temperature of 900°C, a heating time of 1 hour, a tempering temperature of 180°C, and a holding time of 2 hours.

[0050] Comparative Example 8: The chemical composition of the prepared steel plate is as follows by weight: C: 0.30%; Mn: 0.8%; Si: 0.25%; Mo: 0.40%; Ti: 0.60%; Cr: 0.80%; N≤0.004wt%; S≤0.003%; P≤0.008%; the remainder is Fe and unavoidable impurity elements.

[0051] High-quality molten steel is used during smelting, and its chemical composition is optimized: niobium microalloying is eliminated, and 0.40wt% Mo and 0.80wt% Cr are added to the molten steel to improve hardenability; the content of harmful elements is controlled: N≤0.004wt%, S≤0.002wt%, P≤0.008wt%; the tundish superheat is 25°C.

[0052] The continuous casting slab is heated in a heating furnace at a temperature of 1250°C for 4 hours;

[0053] The plate mill utilizes a high-permeability three-stage rolling process. After the continuous casting slab leaves the heating furnace, the mill's high-pressure descaling device descales and cools the slab, maintaining a surface temperature of 960°C and a core temperature of approximately 1100°C. Finishing rolling begins at 920°C and ends at 880°C, with a 30% deformation. The austenite non-recrystallization zone begins at 920°C, with a 40% deformation. The two-phase non-recrystallization zone begins at 850°C, with a 20% deformation. The total reduction ratio is 3.0.

[0054] After rolling, offline heat treatment is carried out, with a quenching temperature of 900°C, a heating time of 1 hour, a tempering temperature of 180°C, and a holding time of 2 hours.

[0055] Example 1: The chemical composition of the prepared steel plate is as follows by weight: C: 0.30%; Mn: 0.8%; Si: 0.25%; Mo: 0.40%; Ti: 0.60%; Cr: 0.80%; N≤0.004wt%; S≤0.002%; P≤0.008%; the balance is Fe and unavoidable impurity elements.

[0056] High-quality molten steel is used during smelting, and its chemical composition is optimized: niobium microalloying is eliminated, and 0.40wt% Mo and 0.80wt% Cr are added to the molten steel to improve hardenability; the content of harmful elements is controlled: N≤0.004wt%, S≤0.002wt%, P≤0.008wt%; the tundish superheat is 25°C.

[0057] The continuous casting slab is heated in a heating furnace at a temperature of 1250°C for 4 hours;

[0058] The medium and heavy plate mill utilizes a high-permeability three-stage rolling process. After the continuous casting slab exits the heating furnace, the mill's high-pressure descaling device descales and cools the slab, maintaining a surface temperature of 960°C and a core temperature of approximately 1100°C. Finishing rolling begins at 920°C and ends at 880°C, with a deformation of 35.6%. The austenite non-recrystallization zone begins at 920°C, with a deformation of 43.1%. The two-phase non-recrystallization zone begins at 850°C, with a deformation of 45.5%. The deformation in the austenite non-recrystallization zone and the two-phase non-recrystallization zone accounts for 55.6% of the total deformation, resulting in a total reduction ratio of 5.

[0059] After rolling, offline heat treatment is carried out, with a quenching temperature of 900°C, a heating time of 1 hour, a tempering temperature of 180°C, and a holding time of 2 hours.

[0060] Example 2: The chemical composition of the prepared steel plate is as follows by weight: C: 0.30%; Mn: 0.8%; Si: 0.25%; Mo: 0.40%; Ti: 0.60%; Cr: 0.80%; N≤0.004wt%; S≤0.002%; P≤0.008%; the remainder is Fe and unavoidable impurity elements.

[0061] High-quality molten steel is used during smelting, and its chemical composition is optimized: niobium microalloying is eliminated, and 0.40wt% Mo and 0.80wt% Cr are added to the molten steel to improve hardenability; the content of harmful elements is controlled: N≤0.004wt%, S≤0.002wt%, P≤0.008wt%; the tundish superheat is 25°C.

[0062] The continuous casting slab is heated in a heating furnace at a temperature of 1250°C for 4 hours;

[0063] The plate mill utilizes a high-permeability three-stage rolling process. After the continuous casting slab leaves the reheating furnace, the mill's high-pressure descaling device descales and cools the slab, maintaining a surface temperature of 960°C and a core temperature of approximately 1100°C. Finishing rolling begins at 920°C and ends at 880°C, with a deformation of 35.6%. The austenite non-recrystallization zone begins at 920°C, with a deformation of 69%. The two-phase non-recrystallization zone begins at 850°C, with a deformation of 33.3%. The deformation in the austenite non-recrystallization zone and the two-phase non-recrystallization zone accounts for 59% of the total deformation, resulting in a total reduction ratio of 7.5.

[0064] After rolling, offline heat treatment is carried out, with a quenching temperature of 900°C, a heating time of 1 hour, a tempering temperature of 180°C, and a holding time of 2 hours.

[0065] The mechanical property test results and particle size statistical results of the steel plates obtained in Comparative Examples 1 to 8 and Examples 1 and 2 are shown in Table 1.

[0066] The steel plate prepared in accordance with the technical solution of the present invention has a hardness of 450-460HB, a tensile strength of 1300-1400MPa, an elongation of 10%-13%, an impact absorption energy of more than 35J at -20°C, and wear resistance of more than 1.5 times that of traditional wear-resistant steel of the same hardness.

[0067] Table 1 Comparison of mechanical properties of steel plates and particle size

[0068]

[0069]

[0070]

[0071] In Comparative Example 1, the pouring temperature was high and the rolling reduction ratio was low, resulting in large TiC particles in the finished steel sheet, with an average size of 3.3 μm. This large particle size compromises impact toughness. Large particles also experience high internal stress and are prone to breakage, resulting in high wear weight loss and poor wear resistance. In Comparative Example 2, the pouring temperature was lowered, but the rolling reduction ratio was low, reducing the particle size and improving the steel sheet's impact and wear resistance. In Comparative Example 3, the pouring temperature was lowered, but the rolling reduction ratio was high, resulting in excessively small particle size. Impact performance improved modestly, but wear resistance was significantly reduced because small particles were easily removed, resulting in a decrease in wear resistance. The three-stage compression in Comparative Examples 4 and 5 met the requirements of the technical solution, but the compression ratio did not reach the optimal range of 5-7.5. Therefore, these two examples achieved the desired steel sheet requirements, albeit with slightly inferior results compared to Examples 1 and 2. In Comparative Examples 6, 7, and 8, the deformation in the first, second, and third stages of rolling, respectively, exceeded the requirements of the technical solution, resulting in the resulting steel sheets not meeting the requirements. The TiC particles in the finished steel plate are relatively large in size, but in Examples 1 and 2, the pouring temperature is lowered and the appropriate rolling reduction ratio is set to obtain the optimal particle size, which has higher impact resistance and the best wear resistance.

Claims

1. A method for manufacturing a high-toughness TiC particle reinforced martensitic wear-resistant steel plate, characterized in that: The method comprises the following steps: converter smelting, refining outside the furnace, protective casting, continuous casting billet heating, rolling and heat treatment; the chemical composition of the prepared steel plate is as follows by weight: C: 0.20%-0.40%; Mn: 0.50%-1.00%; Si: 0.20%-0.30%; Mo: 0.20%-0.50%; Ti: 0.30%-0.80%; Cr: 0.50%-1.00%; N≤0.004%; S≤0.002%; P≤0.008%; the balance is Fe and unavoidable impurity elements; wherein, the casting temperature is lowered during the protective casting; high permeability rolling and a set rolling reduction ratio are adopted during the rolling to control the TiC particle size to 1.0-2.5μm; the rolling adopts three-stage controlled rolling, including recrystallization zone rolling, austenite non-recrystallization zone rolling and two-phase non-recrystallization zone rolling; the recrystallization zone rolling adopts high permeability rolling, the surface temperature of the continuous casting billet is 920-960℃, the core temperature of the slab is 1000-1100℃, and the deformation is between 30%-40%; the starting rolling temperature of the austenite non-recrystallization zone rolling is between 900-940℃, the deformation is between 40%-70%; the starting rolling temperature of the two-phase non-recrystallization zone is between 840-860℃, and the deformation is between 30%-50%; The total rolling reduction ratio of the three-stage controlled rolling is 5-7.

5.

2. The method for manufacturing a high-toughness TiC particle reinforced martensitic wear-resistant steel plate according to claim 1, characterized in that: The deformation amounts of the austenite non-recrystallized zone and the two-phase non-recrystallized zone account for 50%-60% of the total deformation amount.

3. The method for manufacturing a high-toughness TiC particle reinforced martensitic wear-resistant steel plate according to claim 1, characterized in that: The converter smelting selects molten steel, whose chemical composition is to eliminate niobium microalloying, add 0.20wt%-0.50wt% of Mo and 0.50wt%-1.00wt% of Cr by weight of the molten steel to improve hardenability; and control the content of harmful elements: N≤0.004wt%, S≤0.002wt%, P≤0.008wt%.

4. The method for manufacturing a high-toughness TiC particle reinforced martensitic wear-resistant steel plate according to claim 3, characterized in that: The lowering of the casting temperature specifically involves setting the tundish superheat to 20-30°C.

5. The method for manufacturing a high-toughness TiC particle reinforced martensitic wear-resistant steel plate according to any one of claims 1 to 4, characterized in that: The quenching temperature in the heat treatment is 850-900° C., the heating time is 0.5-2 hours, the tempering temperature is 180-220° C., and the holding time is 1-3 hours.

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