SUP13Cr high alloy steel and heat treatment method thereof

Abstract

The invention provides SUP13Cr high-alloy steel and a heat treatment method thereof, and relates to the technical field of high-alloy steel heat treatment, the heat treatment method comprises the following steps: S1, slow cooling after rolling: carrying out air cooling on hot-rolled steel to below 100 DEG C; and S2, annealing: placing the rolled steel subjected to slow cooling treatment in an annealing furnace, heating to 610-630 DEG C, carrying out heat preservation for 5.0-7.0 h / 100mm, and then discharging and carrying out air cooling. By changing the cooling mode after rolling and performing one-stage isothermal annealing, a tempered martensite structure with a steady state and a moderate hardness value are obtained, the annealing period is greatly shortened, and the capacity of an annealing furnace is released.

Description

Technical Field

[0001] The invention relates to the technical field of heat treatment of high alloy steel, and in particular to a SUP13Cr high alloy steel and a heat treatment method thereof. Background Art

[0002] SUP13Cr high alloy steel is widely used in offshore oil projects, OTG pipelines, shells and downhole projects due to its good corrosion resistance and mechanical properties. The raw materials for rolling or forging are mainly unstable supercooled martensite structure, and the hardness reaches more than 330HBW. It is very easy to produce core cracks due to excessive internal stress, and it is difficult to saw and cut. In order to improve the organization to release stress and reduce the hardness value, a two-stage annealing process is conventionally used, such as Figure 1 As shown in the figure, the original annealing process is: heating to 830±10℃ and keeping it for 6h / 100mm→cooling to 300℃ at ≤30℃ / h→air cooling to room temperature after leaving the furnace for 10-12h→heating to 620±10℃ and keeping it for 9h / mm→cooling to 300℃ at ≤30℃ / h→air cooling to room temperature after leaving the furnace. Although this process can fully release the thermal stress and organizational stress, and obtain a steady-state tempered martensite structure and an ideal hardness value, the energy consumption cost is too high due to the excessively high insulation temperature and long insulation time, and it seriously restricts the annealing furnace capacity at the production site.

[0003] Therefore, in the current actual production and delivery process, it is necessary to find a better heat treatment process for SUP13Cr high alloy steel, which can not only ensure that the stress can be fully released after heat treatment to obtain a steady-state martensitic structure and ideal hardness, but also shorten the annealing time and release the annealing furnace capacity. Summary of the invention

[0004] In order to solve the problem that the two-stage annealing heating time is too long, which seriously restricts the production capacity of the annealing furnace, the present invention provides a SUP13Cr high-alloy steel and a heat treatment method thereof. By changing the post-rolling cooling method and one-stage isothermal annealing, a steady-state tempered martensite structure and a moderate hardness value are obtained, and the annealing cycle is greatly shortened, releasing the annealing furnace capacity.

[0005] In order to achieve the above object, the present invention adopts the following technical solutions:

[0006] The present invention provides a heat treatment method for SUP13Cr high alloy steel, comprising the following steps:

[0007] S1. Slow cooling after rolling: air cool the hot-rolled steel to below 100°C;

[0008] S2, annealing step: placing the steel after slow cooling treatment after rolling in an annealing furnace, heating to 610-630°C for heat preservation, and keeping the heat for 5.0-7.0h / 100mm before taking out of the furnace for air cooling.

[0009] Further, based on the above technical solution, in step S1, the time required for air cooling to below 100°C is 20-26 hours.

[0010] Further, on the basis of the above technical solution, in step S2, heating to 620°C is carried out for heat preservation, and the heat preservation time is 6h / 100mm.

[0011] Furthermore, based on the above technical solution, in step S2, the heating rate is ≤60°C / h.

[0012] Further, on the basis of the above technical solution, in step S2, the annealing furnace is a trolley-type annealing furnace; and the fuel of the annealing furnace is mixed coal gas or natural gas.

[0013] Furthermore, on the basis of the above technical solution, in a trolley-type annealing furnace, including a trolley and a material seat, multiple steel materials are bundled to form multiple round rod bundles, and the multiple round rod bundles are placed on the material seat at intervals to form round rod layers, and the upper and lower round rod layers are separated by long strip iron pads.

[0014] Furthermore, based on the above technical solution, in the annealing furnace, in the same round rod layer, the spacing distance between multiple round rod bundles is ≥30 mm.

[0015] The present invention also provides a SUP13Cr high alloy steel prepared by the heat treatment method of the SUP13Cr high alloy steel as described above, which comprises the following components by mass percentage:

[0016] C≤0.03%; Si 0.15-0.40%; Mn 0.30-0.50%; Ni 5.00-5.50%; Cr12.00-13.00%; Mo 1.80-2.00%; Cu≤0.20%; P≤0.018%; S≤0.005%; V0.06-0.09%; the rest are Fe and inevitable impurities in the smelting process.

[0017] Furthermore, based on the above technical solution, the Brinell hardness of the SUP13Cr high alloy steel is ≤280 HBW.

[0018] Further, on the basis of the above technical solution, the SUP13Cr high alloy steel includes a stable tempered martensite structure;

[0019] The SUP13Cr high alloy steel includes rolled products and forged products.

[0020] The present invention provides a SUP13Cr high alloy steel and a heat treatment method thereof, and the beneficial effects are as follows:

[0021] 1. In the heat treatment of the present invention, the annealing process is 620±10℃ insulation for 6h / 100mm→ furnace cooling in air, which is compared with the original annealing process of 830±10℃ insulation for 6h / 100mm→ furnace cooling to 300℃ at ≤30℃ / h→ furnace cooling to room temperature→heating to 620±10℃ insulation for 9h / mm→ furnace cooling to 300℃ at ≤30℃ / h→ furnace cooling to room temperature. Taking the 270mm specification as an example, the annealing cycle is shortened from 101.5 hours to 30 hours, and the coal consumption is reduced from about 980m 3 / t reduced to 285m 3 / t.

[0022] 2. In the heat treatment of the present invention, a trolley furnace is used for annealing. There are material seats arranged at equal intervals on the trolley. The steel is stacked layer by layer on the material seats. The spacing between two adjacent bundles of steel in the same layer is ≥30mm. The layers are separated by iron pads of consistent height. Through the specified distribution pattern, the furnace gas atmosphere around each steel is ensured to be consistent and evenly heated, thereby ensuring the uniform structure and hardness of the steel after annealing.

[0023] 3. In the heat treatment method of the present invention, the heating process parameters and the distribution and stacking of the steel materials work together to ensure the uniformity of the structure and hardness of the SUP13Cr high alloy steel. BRIEF DESCRIPTION OF THE DRAWINGS

[0024] In order to more clearly illustrate the specific implementation methods of the present invention or the technical solutions in the prior art, the drawings required for use in the specific implementation methods or the description of the prior art will be briefly introduced below. Obviously, the drawings described below are some implementation methods of the present invention. For ordinary technicians in this field, other drawings can be obtained based on these drawings without paying creative work.

[0025] Figure 1 Schematic diagram of the original annealing process;

[0026] Figure 2 A schematic diagram of the annealing process provided by the present invention;

[0027] Figure 3 This is the organizational structure diagram of the SUP13Cr high alloy steel obtained in Example 1 of the present invention;

[0028] Figure 4 This is the organizational structure diagram of the SUP13Cr high alloy steel obtained in Example 2 of the present invention;

[0029] Figure 5 This is the organizational structure diagram of the SUP13Cr high alloy steel obtained in Example 3 of the present invention;

[0030] Figure 6This is the organizational structure diagram of the SUP13Cr high alloy steel obtained in comparative case 1;

[0031] Figure 7 It is a schematic diagram of stacking steel materials on a trolley annealing furnace in the present invention.

[0032] Reference numerals:

[0033] 1. Trolley; 2. Material stand; 3. Round bar bundle; 4. Iron pad. DETAILED DESCRIPTION

[0034] In order to make the purpose, technical scheme and advantages of the present invention clearer, the technical scheme in the embodiment of the present invention will be clearly and completely described below in conjunction with the embodiments of the present invention. It should be understood by those skilled in the art that the embodiments are only to help understand the present invention and should not be regarded as specific limitations of the present invention. Based on the embodiments in the present invention, all other embodiments obtained by ordinary technicians in the field without making creative work are within the scope of protection of the present invention. The process parameters of the following embodiments that do not specify specific conditions are usually based on conventional conditions.

[0035] The endpoints and any values ​​of the ranges disclosed in the present invention are not limited to the precise ranges or values, and these ranges or values ​​should be understood to include values ​​close to these ranges or values. For numerical ranges, the endpoint values ​​of each range, the endpoint values ​​of each range and the individual point values, and the individual point values ​​can be combined with each other to obtain one or more new numerical ranges, which should be regarded as specifically disclosed in the present invention.

[0036] According to a first aspect of the present invention, there is provided a heat treatment method for SUP13Cr high alloy steel, comprising the following steps:

[0037] S1. Slow cooling after rolling: air cool the hot-rolled steel to below 100°C, such as 95°C, 90°C, 85°C, 80°C, 75°C, etc.

[0038] S2, annealing step: placing the steel after slow cooling treatment after rolling in an annealing furnace, heating to 610-630°C (for example, 613°C, 615°C, 617°C, 620°C, 623°C, 625°C, 627°C, etc.) for insulation, and insulation for 5.0-7.0h / 100mm (5.0-7.0h / 100mm means that every 100mm diameter needs to be heated for 5.0-7.0h, for example, 5.2h / 100mm, 5.4h / 100mm, 5.6h / 100mm, 5.8h / 100mm, 6.0h / 100mm, 6.2h / 100mm, 6.4h / 100mm, 6.6h / 100mm, 6.8h / 100mm, etc.), and then taking out of the furnace and air cooling.

[0039] Specifically, the temperature of the steel after hot rolling is usually around 850°C. Conventional SUP13Cr high alloy steel requires the steel to be quickly cooled in a slow cooling pit after sawing, and then annealed after 40 hours of slow cooling. The annealing cycle is too long, the annealing cost is too high, and the furnace utilization rate is low. The present invention first obtains a martensite structure containing more δ-ferrite by rapid cooling after rolling, and then obtains a stable tempered martensite by one annealing.

[0040] Furthermore, the present invention limits the air cooling of the steel after hot rolling to below 100°C because within this temperature range, the transformation of austenite to martensite in the steel is completed, ensuring the stability of the martensite structure. This process not only helps to ensure the mechanical properties of the steel during subsequent processing and use, such as hardness, strength and toughness, but also avoids the situation where austenite fails to be completely transformed into martensite due to excessively high temperature, thereby reducing the risk of brittleness of the steel.

[0041] Furthermore, SUP13Cr belongs to martensitic precipitation hardening stainless steel, which is a high-alloy martensitic stainless steel. The theoretical austenitization AC1 temperature point is about 650℃. The steel is air-cooled, and after rapid cooling, unstable but sufficient martensite is obtained. After heat preservation at 610-630℃, stable tempered martensite can be obtained. If the annealing temperature is too high (>630℃), austenite phase transformation will occur, and unstable martensite will be regenerated after cooling; if the annealing temperature is too low (<610℃), the diffusion rate of carbon will slow down, and sufficient stable tempered martensite cannot be obtained by heat preservation at 5.0-7.0h / 100mm, resulting in the hardness and microstructure uniformity not meeting the requirements.

[0042] Furthermore, the present invention limits the heating time to 5.0 to 7.0 hours for every 100 mm diameter because within this limit, sufficiently stable tempered martensite can be obtained, and steel with excellent hardness and structural uniformity can be obtained. If the heating time is too short, the tempered martensite transformation will be insufficient, and if the heating time is too long, production capacity will be wasted and fuel costs will be increased.

[0043] As an optional embodiment of the present invention, in step S1, the time for air cooling to below 100°C is 20-26 hours (such as 21 hours, 22 hours, 23 hours, 24 hours, 25 hours, etc.).

[0044] Specifically, the present invention adopts air cooling, and the slow cooling time of about 24 hours can meet the requirements. The martensitic transformation temperature of SUP13Cr is about 330°C, and annealing can only be carried out after the phase transformation is completely occurred. The air cooling to below 100°C is required because there is a temperature gradient from the surface to the core of the steel, the surface cooling rate is fast and the core cooling rate is slow. Experience shows that the surface temperature must be cooled to below 100°C to ensure that the core temperature is below 300°C.

[0045] Specifically, as an optional implementation of the present invention, in step S2, heating to 620°C is performed for heat preservation, and the heat preservation time is 6h / 100mm.

[0046] As an optional embodiment of the present invention, in step S2, the heating rate is ≤60°C / h (such as 50°C / h, 52°C / h, 54°C / h, 56°C / h, 58°C / h, etc.).

[0047] Specifically, the present invention limits the heating rate in step S2 to ≤60° C. / h because a too fast heating rate may lead to excessive thermal stress and cause cracks.

[0048] As an optional implementation manner of the present invention, in step S2, the annealing furnace is a trolley-type annealing furnace; and the fuel of the annealing furnace is mixed coal gas or natural gas.

[0049] As an optional embodiment of the present invention, Figure 7 As shown, in the trolley-type annealing furnace, a trolley 1 and a material seat 2 are included. A plurality of steel materials are bundled to form a plurality of round rod bundles 3. The plurality of round rod bundles 3 are placed on the material seat at intervals to form round rod layers. The upper and lower round rod layers are separated by long strip iron pads 4.

[0050] As an optional embodiment of the present invention, in the annealing furnace, in the same round rod layer, the spacing distance between multiple round rod bundles 3 is ≥30 mm (such as 35 mm, 40 mm, 45 mm, 50 mm, etc.).

[0051] According to a second aspect of the present invention, there is provided a SUP13Cr high alloy steel, comprising the following components by mass percentage:

[0052] C≤0.03%; Si 0.15-0.40% (such as 0.2%, 0.25%, 0.3%, 0.35%, etc.); Mn0.30-0.50% (such as 0.33%, 0.35%, 0.37%, 0.4%, 0.42%, 0.45%, 0.47%, etc.); Ni 5.00-5.50% (such as 5.10%, 5.20%, 5.30%, 5.40%, etc.); Cr 12.00-13.00% (such as 12.20%, 12.40%, 12.60%, 12.80%, etc.); Mo 1.80-2.00% (such as 1.82%, 1.85%, 1.87%, 1.92%, 1.95%, 1.97%, etc.); Cu≤0.20% (such as 0.12%, 0.14%, 0.16%, 0.18%, etc.); P≤0.018% (such as 0.012%, 0.014%, 0.016%, etc.); S≤0.005% (such as 0.001%, 0.002%, 0.003%, 0.004%, etc.); V 0.06-0.09% (such as 0.07%, 0.075%, 0.08%, 0.085%, etc.); the rest are Fe and inevitable impurities in the smelting process.

[0053] As an optional implementation manner of the present invention, the Brinell hardness of the SUP13Cr high alloy steel is ≤280 HBW.

[0054] As an optional embodiment of the present invention, the SUP13Cr high alloy steel includes a stable tempered martensite structure;

[0055] The SUP13Cr high alloy steel includes rolled products and forged products.

[0056] The present invention will be further described in detail below with reference to specific embodiments and comparative examples.

[0057] Example 1

[0058] In terms of mass percentage, the chemical composition of the SUP13Cr steel provided in this embodiment is: C 0.016%; Si 0.28%; Mn 0.42%; Ni 5.32%; Cr 12.26%; Mo 1.85%; Cu 0.13%; P 0.012%; S 0.002%; V 0.06%; the rest is Fe and inevitable impurities in the smelting process.

[0059] The heat treatment method of SUP13Cr steel provided in this embodiment comprises the following steps:

[0060] S1. Slow cooling step after rolling: The diameter of the finished round steel is 270 mm, and it is air-cooled to room temperature for 24 hours after hot rolling.

[0061] S2, annealing step: placing the steel products after slow cooling treatment in a trolley type annealing furnace, Figure 2 The annealing process diagram shown is that the temperature is raised to 620°C at 60°C / h, and the steel is kept at this temperature for 6h / 100mm, i.e., the holding time is 16.2h. The steel is then taken out of the furnace and air-cooled to room temperature to obtain the annealed SUP13Cr steel.

[0062] The above heat treatment adopts a trolley-type annealing furnace, and the fuel is mixed coal gas; a material holder with the same height is placed on the trolley of the above annealing furnace, such as Figure 7 As shown, multiple steel products after slow cooling treatment after rolling are formed into multiple round bar bundles in bundles, and the multiple round bar bundles are placed on the material seat of the trolley-type annealing furnace at a distance of 30 mm to form round bar layers. The round bar bundles are stacked on the trolley layer by layer, and the upper and lower round bar layers are separated by long strips of iron pads.

[0063] The microstructure of the SUP13Cr steel obtained after annealing in this embodiment is shown in FIG. Figure 3 , which is a thin strip of tempered martensite, evenly dispersed in the steel matrix.

[0064] The hardness value of the SUP13Cr steel after annealing is 272HBW, which meets the requirement of ≤280HBW. This hardness range is more suitable for sawing and cutting, and the saw blade will not be damaged due to excessive hardness during the cutting process.

[0065] The coal consumption per ton of SUP13Cr steel produced by the heat treatment method is about 285m 3 , annealing cycle 30 hours.

[0066] Example 2

[0067] The main difference between this embodiment and embodiment 1 is that the diameter of the finished round steel is 210 mm, the insulation time in step S2 is 12.6 h, and the other steps and process parameters are the same as those in embodiment 1.

[0068] The microstructure of the SUP13Cr steel obtained after annealing in this embodiment is shown in FIG. Figure 4 , which is also a thin strip of tempered martensite, evenly dispersed in the steel matrix.

[0069] The hardness value of the SUP13Cr steel after annealing is 273 HBW, which meets the requirement of ≤280 HBW.

[0070] The coal consumption per ton of SUP13Cr steel produced by the heat treatment method is about 241m 3 , annealing cycle 26 hours.

[0071] Example 3

[0072] The main difference between this embodiment and embodiment 1 is that the diameter of the finished round steel is 310 mm, the insulation time in step S2 is 18.6 h, and the other steps and process parameters are the same as those in embodiment 1.

[0073] The microstructure of the SUP13Cr steel obtained after annealing in this embodiment is shown in FIG. Figure 5 , which is also a thin strip of tempered martensite, evenly dispersed in the steel matrix.

[0074] The hardness value of the SUP13Cr steel after annealing is 273 HBW, which meets the requirement of ≤280 HBW.

[0075] The coal consumption per ton of SUP13Cr steel produced by the heat treatment method is about 312 m3. 3 , annealing cycle 32 hours.

[0076] Comparative Example 1

[0077] The finished product of this comparative example has a diameter of 270 mm, and the cooling steps after rolling are as follows: after rolling, the product is quickly placed in a slow cooling pit, and after being stored for 32 hours, the slow cooling pit cover is opened and cooled to room temperature.

[0078] The annealing process is as follows: heating to 830±10℃ at a heating rate of 60℃ / h and keeping warm for 6h / 100mm→cooling to 300℃ at a rate of ≤30℃ / h→air cooling to room temperature→heating to 620±10℃ and keeping warm for 9h / mm→cooling to 300℃ at a rate of ≤30℃ / h→air cooling to room temperature.

[0079] Figure 6 The structure of SUP13Cr obtained by the annealing process provided in this comparative example. Figure 6 It can be seen that the structure of SUP13Cr is also elongated tempered martensite with a hardness value of 268HBW, which meets the requirement of ≤280HBW.

[0080] The annealing process provided in the comparative example was used to obtain SUP13Cr, and both its microstructure and hardness met the requirements. However, the coal consumption per ton of steel reached 980m3. 3 , annealing cycle 101.5 hours.

[0081] Comparative Example 2

[0082] The finished product of this comparative example has a diameter of 270 mm. The main difference compared with Example 1 is that the annealing temperature is 650° C., and the remaining steps and technical parameters are the same as those of Example 1.

[0083] The hardness value of Comparative Example 2 has a large fluctuation phenomenon, ranging from 256 to 312 HBW, which does not meet the overall requirement of ≤280 HBW.

[0084] The SUP13Cr steel produced by the heat treatment method provided in this comparative example consumes about 284 m3 of coal per ton of steel.3 , annealing cycle 30 hours.

[0085] Comparative Example 3

[0086] The finished product of this comparative example has a diameter of 270 mm. The main difference compared with Example 1 is that the annealing and heat preservation treatment is performed for 8 h / 100 mm, and the remaining steps and technical parameters are the same as those of Example 1.

[0087] The microstructure of SUP13Cr of Comparative Example 3 is also elongated strip-shaped tempered martensite, with a hardness value of 268 HBW, meeting the requirement of ≤280 HBW.

[0088] The annealing process of Comparative Example 3 was used to obtain SUP13Cr, and both its microstructure and hardness met the requirements, but the coal consumption per ton of steel reached 316m 3 , annealing cycle 35 hours.

[0089] Comparative Example 4

[0090] The finished product of this comparative example has a diameter of 270 mm. The main difference compared with Example 1 is that in step S1, the hot-rolled steel is air-cooled to 200°C in the post-rolling slow cooling. The remaining steps and technical parameters are the same as those in Example 1.

[0091] The hardness of Comparative Example 4 also has a large fluctuation phenomenon, 273-322 HBW, which does not meet the overall requirement of ≤280 HBW.

[0092] The SUP13Cr steel produced by the heat treatment method provided in this comparative example consumes about 287 m3 of coal per ton of steel. 3 , annealing cycle 30 hours.

[0093] Performance Testing

[0094] The hardness values ​​of this test are all tested using a PHB-3000 hydraulic Brinell hardness tester (3000kg test force, 10mm diameter tungsten carbide alloy ball). The hardness specimen is a 20mm thick test piece cut from round steel, and the hardness value is tested at 1 / 2 diameter.

[0095] Performance data

[0096] Table 1

[0097] Diameter (mm) Hardness value HBW <![CDATA[Coal consumption per ton of steel m 3 > Annealing cycle h Example 1 270 272 285 30 Example 2 210 273 241 26 Example 3 310 273 312 32 Comparative Example 1 270 268 980 101.5 Comparative Example 2 270 256-312 284 30 Comparative Example 3 270 268 316 35 Comparative Example 4 270 273-322 287 30

[0098] According to Table 1, compared with Example 1 and Comparative Example 1, the present invention provides a better SUP13Cr high alloy steel heat treatment method, which greatly shortens the annealing cycle and reduces the coal consumption cost per ton of steel by changing the post-rolling cooling method and the annealing holding temperature, thereby fully releasing the annealing furnace capacity.

[0099] According to Table 1, compared with Comparative Example 2, in Example 1, due to the excessively high annealing temperature in Comparative Example 2, high requirements are placed on furnace performance, and even the temperature of some sections is higher than 650°C, resulting in local austenitization and formation of an unstable martensitic structure after cooling, which leads to the unstable hardness value of the steel obtained in Comparative Example 2, which is within the range of 256-312 HBW and does not meet the overall requirement of ≤280 HBW.

[0100] According to Table 1, compared with Example 3, in Example 1, the heating time in Example 3 is too long due to the annealing and heat preservation treatment of 8h / 100mm, resulting in excessively high coal consumption per ton of steel.

[0101] According to Table 1, compared with Comparative Example 4, in Example 1, due to air cooling to 200°C in step S1, there is a temperature gradient difference from the surface to the core of the steel, the surface temperature is low and the core temperature is high, martensite transformation has occurred on the surface, but the core is still austenite, and the structure is unstable and uneven after annealing, resulting in the unstable hardness value of the steel obtained in Comparative Example 4, which is within 273-322HBW and does not meet the overall ≤280HBW requirement.

[0102] Finally, it should be noted that the above embodiments are only used to illustrate the technical solutions of the present invention, rather than to limit it. Although the present invention has been described in detail with reference to the aforementioned embodiments, those skilled in the art should understand that they can still modify the technical solutions described in the aforementioned embodiments, or replace some or all of the technical features therein by equivalents. However, these modifications or replacements do not cause the essence of the corresponding technical solutions to deviate from the scope of the technical solutions of the embodiments of the present invention.

Claims

1. A heat treatment method for SUP13Cr high alloy steel, characterized in that: The steps include: S1. Slow cooling after rolling: air cool the hot-rolled steel to below 100°C; S2, annealing step: placing the steel after slow cooling treatment after rolling in an annealing furnace, heating to 610-630°C for heat preservation, and keeping the heat for 5.0-7.0h / 100mm before taking out of the furnace for air cooling.

2. The heat treatment method of SUP13Cr high alloy steel according to claim 1, characterized in that: In step S1, the time required for air cooling to below 100°C is 20-26 hours.

3. The heat treatment method of SUP13Cr high alloy steel according to claim 1, characterized in that: In step S2, the temperature is heated to 620°C and kept warm for 6h / 100mm.

4. The heat treatment method of SUP13Cr high alloy steel according to claim 1, characterized in that: In step S2, the heating rate is ≤60°C / h.

5. The heat treatment method of SUP13Cr high alloy steel according to claim 1, characterized in that: In step S2, the annealing furnace is a trolley-type annealing furnace; the fuel of the annealing furnace is mixed coal gas or natural gas.

6. The heat treatment method of SUP13Cr high alloy steel according to claim 5, characterized in that: In a trolley-type annealing furnace, which includes a trolley and a material seat, multiple steel materials are bundled to form multiple round bar bundles, and the multiple round bar bundles are placed on the material seat at intervals to form round bar layers. The upper and lower round bar layers are separated by long strip iron pads.

7. The heat treatment method of SUP13Cr high alloy steel according to claim 6, characterized in that: In the annealing furnace, in the same round rod layer, the spacing between multiple round rod bundles is ≥30 mm.

8. A SUP13Cr high alloy steel prepared by the heat treatment method of SUP13Cr high alloy steel according to any one of claims 1 to 7, characterized in that: In terms of mass percentage, it includes the following components: C≤0.03%; Si 0.15-0.40%; Mn 0.30-0.50%; Ni 5.00-5.50%; Cr12.00-13.00%; Mo1.80-2.00%; Cu≤0.20%; P≤0.018%; S≤0.005%; V0.06-0.09%; the rest are Fe and inevitable impurities in the smelting process.

9. The SUP13Cr high alloy steel according to claim 8, characterized in that: The Brinell hardness of the SUP13Cr high alloy steel is ≤280 HBW.

10. The SUP13Cr high alloy steel according to claim 8, characterized in that: The SUP13Cr high alloy steel includes a stable tempered martensite structure; The SUP13Cr high alloy steel includes rolled products and forged products.

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