GH5630C wear-resistant alloy, preparation method and application thereof

Abstract

The application relates to the technical field of high-temperature bearings, and particularly discloses a GH5630C wear-resistant alloy and a preparation method and application thereof. The GH5630C wear-resistant alloy comprises the following chemical components: C 1.1-1.4%; Cr 28.5-31.5%; Ni 1.0-2.5%; W 4.5-5.5%; Mo 0.50-1.50%; Mn 0.50-1.70%; Si 0.20-1.50%; Nb 0.3-0.6%; La 0.02-0.2%; Fe<=3.00%; S<=0.03%; P<=0.04%; and the balance is Co. The application further provides a preparation method of the GH5630C wear-resistant alloy. The GH5630C wear-resistant alloy has a temperature resistance of more than 500 DEG C, good wear resistance, impact toughness and fatigue resistance, and can be used for manufacturing bearing parts for high-temperature aerobic or corrosive environment applications.

Description

Technical Field

[0001] This application relates to the field of high-temperature bearing technology, and more specifically to a GH5630C wear-resistant alloy, its preparation method and application. Background Technology

[0002] In advanced thermodynamic machinery, bearings are indispensable for any rotating component. For example, in aircraft engine main shafts, transmission and thrust systems, and aerospace rocket and spacecraft servo systems, bearings are critical components supporting rotation and bearing loads, installed at various nodes and connections, acting as "joints." With the development of the aviation, aerospace, and other thermodynamic machinery industries, the operating temperature requirements for bearing steel are becoming increasingly stringent. High-temperature bearing steels, such as M50 (operating temperature 315℃), as well as high-temperature carburized bearing steels like G13Cr4Mo4Ni4V and stainless bearing steels like BG42 (operating temperature 420℃), can no longer meet current needs.

[0003] In pursuit of higher operating temperatures, newly developed aerospace bearing steels, such as high-temperature stainless carburized bearing steel CSS-42L and nitrogen-containing stainless bearing steel Cronidur30, are expected to have operating temperatures exceeding 500℃. However, the martensitic strengthening mechanism of high-temperature bearing steel makes it difficult to continuously increase the operating temperature. In recent years, researchers have prepared a high-temperature ceramic bearing using ceramic materials such as Si3N4 and ZrO2, with an operating temperature of 500-1000℃. However, this high-temperature ceramic bearing has poor impact toughness and fatigue life under high contact stress, resulting in a short service life. In addition, due to the difference in expansion coefficients between high-temperature ceramic bearings and metal shafts, high-temperature ceramic bearings are prone to breakage during use, making it difficult to guarantee reliability and limiting their application range.

[0004] Therefore, it is necessary to develop a bearing material with a temperature resistance exceeding 500℃ and good wear resistance, impact toughness, and fatigue performance to meet the bearing requirements of the aerospace and other thermodynamic machinery industries. Summary of the Invention

[0005] In order to obtain a bearing material with a temperature resistance exceeding 500℃ and good wear resistance, impact resistance and fatigue resistance, this application provides a wear-resistant alloy GH5630C and its preparation method and application.

[0006] In the first aspect, this application provides a GH5630C wear-resistant alloy, which adopts the following technical solution:

[0007] A wear-resistant alloy GH5630C, wherein the GH5630C wear-resistant alloy comprises the following chemical composition: C 1.1-1.4%; Cr 28.5-31.5%; Ni 1.0-2.5%; W 4.5-5.5%; Mo 0.50-1.50%; Mn 0.50-1.70%; Si 0.20-1.50%; Nb 0.3-0.6%; La 0.02-0.2%; Fe≤3.00%; S≤0.03%; P≤0.04%; balance Co.

[0008] This application modifies the chemical composition of typical cobalt-based wear-resistant alloys by increasing the amount of carbide hard phases in the material through a high C content and adding Nb to improve the work hardening rate of the alloy, thereby significantly improving the wear resistance and fatigue strength of the GH5630C wear-resistant alloy. Furthermore, trace amounts of La are added to the GH5630C wear-resistant alloy to enhance its oxidation resistance at high temperatures. Compared with bearing steel and ceramic bearing materials in related technologies, the GH5630C wear-resistant alloy provided in this application can withstand operating temperatures of 500℃ and above, and exhibits excellent wear resistance, impact resistance, and fatigue resistance at these high temperatures. Therefore, the GH5630C wear-resistant alloy provided in this application can meet the requirements of the aerospace and other thermal machinery industries for bearings operating in high-temperature aerobic or corrosive environments.

[0009] Optionally, the GH5630C wear-resistant alloy comprises the following chemical composition: C 1.2%; Cr 30.0%; Ni 2.0%; W 5.0%; Mo 1.25%; Mn 1.2%; Si 1.2%; Nb 0.4%; La 0.08%; Fe≤3.00%; S≤0.03%; P≤0.04%; with the balance being Co.

[0010] Optionally, the GH5630C wear-resistant alloy further includes a chemical composition of N 0.04-0.4%.

[0011] In this application, by adding N to the GH5630C wear-resistant alloy, the primary carbides in the wear-resistant alloy microstructure can be refined and the distribution characteristics of secondary carbides can be improved, thereby making the carbide distribution in the microstructure more uniform and further improving the plasticity and impact toughness of the GH5630C wear-resistant alloy.

[0012] Optionally, the GH5630C wear-resistant alloy has a room temperature impact toughness ≥83J, a fatigue strength at 600℃ ≥650MPa, and a wear volume at 600℃ ≤30×10⁻⁶. 6 μm 3 .

[0013] Secondly, this application provides a method for preparing GH5630C wear-resistant alloy.

[0014] A method for preparing GH5630C wear-resistant alloy includes the following steps: vacuum induction melting, electroslag remelting, homogenization heat treatment, constrained upsetting, fine forging, rolling or forging, and solution treatment.

[0015] Constrained upsetting: The ingot obtained by homogenization heat treatment is subjected to constrained upsetting using a metal constrained die to obtain a forging billet; wherein, the inner diameter of the metal constrained die is 1.02-1.12 times the ideal diameter of the forging billet after constrained upsetting; the ingot heating temperature is 1150-1220℃, the final forging temperature is not lower than 1100℃, and the ingot deformation is 50-60%.

[0016] In this application, during free forging and upsetting, friction exists between the blank and the anvil, causing uneven deformation and bulging. When the tensile stress on the bulging surface exceeds the fracture strength, irregular longitudinal cracks will occur. Therefore, this application adopts a constrained upsetting method. Before forging, a rigid metal constraining ring, slightly larger than the ideal diameter of the forged blank after constrained upsetting, is used to constrain the ingot before upsetting. This effectively prevents excessive bulging of the ingot during upsetting, which could cause longitudinal cracks in the forged blank, and facilitates the transformation of the material from ingot to forged blank. This application further refines the forged blank after constrained upsetting by performing precision forging, profile forging / rolling, and heat treatment. This further improves the distribution and morphology of carbides in the material microstructure and enhances the strain hardening capacity of the matrix, thereby enabling the GH5630C wear-resistant alloy to meet the performance requirements of bearing materials.

[0017] In this application, the size of the metal constraint mold, the ingot heating temperature, and the amount of ingot deformation in the constraint upsetting step affect the wear resistance, impact toughness, and fatigue strength of the GH5630C wear-resistant alloy. When the size of the metal constraint mold is too large, the constraint effect decreases, the deformation uniformity decreases, and the resulting GH5630C wear-resistant alloy has poor wear resistance and ductility. When the ingot heating temperature is too low, the deformation resistance of the ingot is too high; when the ingot heating temperature is too high, the work hardening rate of the ingot is too low. Both of these factors will worsen the deformation uniformity of the ingot, resulting in poor wear resistance and ductility of the GH5630C wear-resistant alloy. When the amount of ingot deformation is too low, the carbides in the ingot are not sufficiently broken up, resulting in poor wear resistance and ductility of the GH5630C wear-resistant alloy. When the amount of ingot deformation is too high, the billet bulges and easily exceeds the constraint mold, thereby reducing the deformation uniformity and decreasing the wear resistance and ductility of the GH5630C wear-resistant alloy. Therefore, this application, through experimental research, has found that by adjusting the dimensions of the metal constraint mold, the ingot heating temperature, and the ingot deformation in the constraint upsetting step to the aforementioned ranges, a GH5630C wear-resistant alloy capable of withstanding working temperatures of 500℃ and above can be obtained. Furthermore, its room temperature impact toughness is ≥85J, its 600℃ fatigue strength is ≥670MPa, and its 600℃ wear volume is ≤25×10⁻⁶. 6 μm 3 .

[0018] In some implementations, the inner diameter of the metal constraint mold can be 1.08-1.2 times the ideal diameter of the forged billet after constraint upsetting.

[0019] In one specific implementation, the inner diameter of the metal constraint mold can also be 1.02 or 1.1 times the ideal diameter of the forged billet after constraint upsetting.

[0020] In this application, the height of the metal constraint mold is slightly lower than the height of the ideal forged billet after upsetting. The metal constraint mold is mainly used to constrain the bulging part during the upsetting forging process, further improving the wear resistance and toughness of the GH5630C wear-resistant alloy. Through experimental research, this application found that controlling the size of the metal constraint mold within the above-mentioned range can, on the one hand, provide good constraint for the ingot and ensure its deformation uniformity; on the other hand, it can also prevent the bulging of the ingot from contacting the mold too early, thus preventing the ingot from cooling down prematurely.

[0021] In some embodiments, the ingot heating temperature can be 1150-1180℃, 1150-1200℃, 1180-1200℃, 1180-1220℃, or 1200-1220℃.

[0022] In one specific implementation, the ingot heating temperature can also be 1150℃, 1180℃, 1200℃ or 1220℃.

[0023] In some implementations, the ingot deformation can be 55-60% or 60-65%.

[0024] In one specific implementation, the ingot deformation amount can also be 55%, 60%, or 65%.

[0025] In this application, the term "ingot deformation" refers to the amount of height deformation of the ingot.

[0026] Optionally, the homogenization heat treatment is performed at a temperature of 1150-1220℃ for 10-24 hours.

[0027] In this application, when the homogenization treatment time is less than 10 hours, microsegregation in the ingot cannot be effectively eliminated, and the hot working process window will be reduced; when the homogenization treatment time is greater than 24 hours, the production cycle and energy consumption costs will increase. Therefore, this application has found through experimental investigation that controlling the homogenization treatment time within the above range can yield GH5630C wear-resistant alloy with excellent wear resistance, impact toughness, and fatigue performance, which can meet the requirements for bearing materials.

[0028] In some implementations, the homogenization process can take 8-10h, 8-20h, 10-20h, 10-24h, or 20-24h.

[0029] In one specific implementation, the homogenization process can also take 8 hours, 10 hours, 20 hours, or 24 hours.

[0030] Optionally, the solution treatment temperature is 1050-1250℃ and the time is 0.5-10h.

[0031] In this application, when the solution treatment temperature is below 1050℃, more carbides tend to precipitate along grain boundaries, significantly reducing the material's mechanical properties such as plasticity, impact toughness, and fatigue strength, failing to meet the reliability requirements for bearing applications. When the solution treatment temperature is above 1250℃, it approaches the initial melting temperature of the alloy, thus significantly degrading the material's various properties and failing to meet the bearing's performance requirements. Therefore, this application, through experimental investigation, has found that controlling the solution treatment temperature within the aforementioned range can meet the comprehensive requirements of bearings for the material's mechanical properties and wear resistance.

[0032] In some embodiments, the solution treatment temperature can be 1100-1150℃, 1100-1200℃, 1100-1230℃, 1100-1250℃, 1150-1200℃, 1150-1230℃, 1150-1250℃, 1200-1250℃, or 1230-1250℃.

[0033] In one specific implementation, the solution treatment temperature can also be 1100℃, 1150℃, 1200℃, 1230℃ or 1250℃.

[0034] Optionally, the precision forging step is as follows: the forging billet obtained by constrained upsetting is subjected to multi-directional forging at a temperature of 1150-1220℃ and a final forging temperature of not less than 900℃; the forging is repeated 4-6 times, with a deformation amount of not less than 40% per forging, to obtain a precision forged billet.

[0035] Thirdly, this application provides a high-temperature resistant bearing, which is made of the above-mentioned GH5630C wear-resistant alloy.

[0036] In summary, this application has the following beneficial effects:

[0037] 1. This application adjusts the chemical composition of typical cobalt-based wear-resistant alloys to obtain a GH5630C wear-resistant alloy. The GH5630C wear-resistant alloy can withstand working temperatures above 500℃ and has excellent wear resistance, impact toughness and fatigue strength at this temperature, which can fully meet the requirements of aviation and aerospace for bearings.

[0038] 2. The preparation method of the GH5630C wear-resistant alloy of this application includes the following steps: vacuum induction melting, electroslag remelting, homogenization heat treatment, constrained upsetting, fine forging, rolling or forging, and solution treatment. By adjusting the ingot heating temperature, ingot deformation, and inner diameter of the metal constraining mold in the constrained upsetting step, a room temperature impact toughness ≥83J, a fatigue strength ≥650MPa at 600℃, and a wear volume ≤30×10 at 600℃ are obtained. 6 μm 3 GH5630C wear-resistant alloy.

[0039] 3. By adjusting the homogenization heat treatment time to 10-24 h and the solution treatment temperature to 1150-1230℃, this application can further improve the comprehensive properties of GH5630C wear-resistant alloy, resulting in a room temperature impact toughness ≥90 J, a fatigue strength at 600℃ ≥670 MPa, and a wear volume at 600℃ ≤25×10⁻⁶. 6 μm 3 . Detailed Implementation

[0040] This application provides a method for preparing GH5630C wear-resistant alloy, comprising the following steps:

[0041] (1) Vacuum induction melting: Using vacuum induction melting technology, the following chemical composition is prepared (by weight percentage) and cast at high temperature to form an electrode rod. The casting temperature is 1400-1500℃.

[0042] The chemical composition of GH5630C wear-resistant alloy is as follows: C 1.1-1.4%; Cr 28.5-31.5%; Ni 1.0-2.5%; W 4.5-5.5%; Mo 0.50-1.50%; Mn 0.50-1.70%; Si 0.20-1.50%; Nb 0.3-0.6%; La 0.02-0.2%; Fe≤3.00%; S≤0.03%; P≤0.04%; balance Co.

[0043] (2) Electroslag remelting: The electrode rod cast in step (1) is remelted in an electroslag remelting continuous directional solidification crystallizer to prepare an ingot; wherein, the melting speed is 0.4-2 kg / min; the slag system used is (by weight percentage): CaF2 50-65%; CaO 15-25%; Al2O3 10-25%.

[0044] (3) Homogenization heat treatment: The ingot obtained by electroslag remelting is treated at a high temperature of 1150-1220℃ for 10-24h to obtain the ingot.

[0045] (4) Constrained upsetting: The ingot obtained by homogenization heat treatment is subjected to constrained upsetting using a metal constrained die to obtain a forging billet; the heating temperature of the ingot is 1150-1220℃, the final forging temperature is not lower than 1100℃, and the deformation of the ingot is 50-60%. Among them, the inner diameter of the metal constrained die is 1.02-1.12 times the ideal diameter of the forging billet after constrained upsetting.

[0046] (5) Precision forging: The forging billet obtained by constrained upsetting is subjected to multi-directional forging at a temperature of 1150-1220℃ and a final forging temperature of not less than 900℃; repeat 4-6 forging cycles, with a deformation amount of not less than 40% per cycle, to obtain precision forging billet.

[0047] (6) Rolling or forging: Rolling or forging the forging billet according to product requirements to obtain profiles;

[0048] When the product is a sheet or bar, the forging billet is rolled.

[0049] When the product is a forging, the forging blank is forged.

[0050] The billet is heated to 1150-1230℃ and repeated 3-5 times, with a deformation of 20-80% per heat; the final heat is heated to 1180-1230℃ and the final rolling temperature is 900-1000℃, with a deformation of 20-30% per heat.

[0051] (7) Solution treatment; the rolled or forged bar is solution treated at 1050-1250℃ for 0.5-10h and then cooled to obtain GH5630C wear-resistant alloy; wherein, the cooling can be water cooling, air cooling, oil cooling or air cooling.

[0052] All raw materials used in this application can be obtained through commercial purchase.

[0053] The present application will be further described in detail below with reference to embodiments and performance testing.

[0054] Example 1

[0055] Example 1 provides a GH5630C wear-resistant alloy bar.

[0056] The preparation of the above-mentioned GH5630C wear-resistant alloy rod includes the following steps:

[0057] (1) Vacuum induction melting: Using vacuum induction melting technology, the electrode rod is prepared according to the following chemical composition content (by weight percentage) and cast at high temperature to form an electrode rod. The casting temperature is 1450℃. The chemical composition of GH5630C wear-resistant alloy is as follows: C 1.2%; Cr 30.0%; Ni 2.0%; W 5.0%; Mo 1.25%; Mn 1.2%; Si 1.2%; Nb 0.4%; La 0.08%; Fe≤3.00%; S≤0.03%; P≤0.04%; balance is Co.

[0058] (2) Electroslag remelting: The electrode rod cast in step (1) is remelted in an electroslag remelting continuous directional solidification crystallizer to prepare an ingot; wherein, the melting speed is 1 kg / min; the slag system used is (by weight percentage): CaF 265%; CaO 25%; Al2O3 10%.

[0059] (3) Homogenization heat treatment: The ingot obtained by electroslag remelting is treated at a high temperature of 1200℃ for 10h to obtain an ingot with a diameter of 180mm and a height of 400mm.

[0060] (4) Constrained upsetting: To obtain a forging billet with a diameter of approximately 254 mm and a height of approximately 200 mm, a rigid metal constraint collar with an inner diameter of 280 mm and a height of 180 mm is used to constrain and upset the ingot obtained by homogenization heat treatment to obtain the forging billet; the ingot heating temperature is 1200℃, the final forging temperature is 1150℃, and the ingot deformation is 50%.

[0061] (5) Precision forging: The forging billet obtained by constrained upsetting is subjected to multi-directional forging at a temperature of 1200℃ and a final forging temperature of 900℃; the forging is repeated 5 times, with a deformation of 40% per forging, to obtain a precision forging billet.

[0062] (6) Rolling: Roll the forging billet into a bar with a diameter of 40mm, and repeat the rolling process 4 times;

[0063] The heating temperature for the first heat is 1200℃, the final rolling temperature is 1100℃, and the deformation is 50%.

[0064] The second heating temperature is 1200℃, the final rolling temperature is 1100℃, and the deformation is 50%.

[0065] The heating temperature for the third heat treatment is 1200℃, the final rolling temperature is 1100℃, and the deformation is 50%.

[0066] The fourth heating temperature is 1200℃, the final rolling temperature is 950℃, and the deformation is 25%.

[0067] (7) Solution treatment: The rolled bar was solution treated at 1150℃ for 5 hours and then water cooled to obtain GH5630C wear-resistant alloy bar.

[0068] Examples 2-4

[0069] Examples 2-4 provide a GH5630C wear-resistant alloy bar.

[0070] Examples 2-4 are carried out according to the method of Example 1, except that: (4) the ingot heating temperature in the constrained upsetting step is as shown in Table 1.

[0071] Table 1. Ingot heating temperatures during the constrained upsetting process in Examples 1-4.

[0072] Example Ingot heating temperature (°C) 1 1200 2 1150 3 1180 4 1220

[0073] Example 5

[0074] Example 5 provides a GH5630C wear-resistant alloy bar.

[0075] Example 5 is performed according to the method of Example 1, except that: (4) in the constrained upsetting step, the ingot deformation is 55%, as follows:

[0076] (4) Constrained upsetting: To obtain a forging billet with a diameter of approximately 254 mm and a height of approximately 180 mm, a rigid metal constraint collar with an inner diameter of 280 mm and a height of 160 mm is used to constrain and upset the ingot (diameter of 180 mm and height of 400 mm) obtained by homogenization heat treatment to obtain the forging billet; the ingot heating temperature is 1200℃, the final forging temperature is 1150℃, and the ingot deformation is 55%.

[0077] Example 6

[0078] Example 6 provides a GH5630C wear-resistant alloy bar.

[0079] Example 6 is performed according to the method of Example 1, except that: (4) in the constrained upsetting step, the ingot deformation is 60%, as follows:

[0080] (4) Constrained upsetting: To obtain a forging billet with a diameter of approximately 254 mm and a height of approximately 160 mm, a rigid metal constraint collar with an inner diameter of 280 mm and a height of 140 mm is used to constrain and upset the ingot (diameter of 180 mm and height of 400 mm) obtained by homogenization heat treatment to obtain the forging billet; the ingot heating temperature is 1200℃, the final forging temperature is 1150℃, and the ingot deformation is 60%.

[0081] Example 7

[0082] Example 7 provides a GH5630C wear-resistant alloy bar.

[0083] Example 7 is carried out according to the method of Example 1, except that: (4) the inner diameter of the metal constraint mold in the constraint upsetting step is 260mm.

[0084] Examples 8-10

[0085] Examples 8-10 each provide a GH5630C wear-resistant alloy bar.

[0086] Examples 8-10 were carried out according to the method of Example 1, except that: (3) the homogenization heat treatment time is shown in Table 2 below.

[0087] Table 2. Homogenization heat treatment time for Examples 1 and 8-10

[0088] Example Homogenization heat treatment time (h) 1 10 8 8 9 20 10 24

[0089] Examples 11-14

[0090] Examples 11-14 each provide a GH5630C wear-resistant alloy bar.

[0091] Examples 11-14 were carried out according to the method of Example 1, except that: (7) the temperature of the solution treatment was as shown in Table 3 below.

[0092] Table 3. Solution treatment temperatures in Examples 1 and 11-14

[0093] Example Solution treatment temperature (h) 1 1150 11 1100 12 1200 13 1230 14 1250

[0094] Example 15

[0095] Example 15 provides a GH5630C wear-resistant alloy bar.

[0096] Example 15 was carried out according to the method of Example 1, except that the chemical composition of the GH5630C wear-resistant alloy bar also includes N.

[0097] In Example 15, the chemical composition of the GH5630C wear-resistant alloy is as follows: C 1.2%; Cr 30.0%; Ni 2.0%; W 5.0%; Mo 1.25%; Mn 1.2%; Si 1.2%; Nb 0.4%; La 0.08%; N 0.15%; Fe≤3.00%; S≤0.03%; P≤0.04%; balance Co.

[0098] Comparative Example 1

[0099] Comparative Example 1 provides a GH5630C wear-resistant alloy bar.

[0100] Comparative Example 1 was carried out according to the method of Example 1, except that the chemical composition of the GH5630C wear-resistant alloy bar was different.

[0101] The chemical composition of the GH5630C wear-resistant alloy bar of Comparative Example 1 is as follows: C 1.2%; Cr 30.0%; Ni 2.0%; W 5.0%; Mo 1.25%; Mn 1.2%; Si 1.2%; La 0.08%; Fe≤3.00%; S≤0.03%; P≤0.04%; balance Co.

[0102] Comparative Example 2

[0103] Comparative Example 2 provides a GH5630C wear-resistant alloy bar.

[0104] Comparative Example 2 was carried out according to the method of Example 1, except that the chemical composition of the GH5630C wear-resistant alloy bar was different.

[0105] The chemical composition of the GH5630C wear-resistant alloy bar of Comparative Example 2 is as follows: C 1.2%; Cr 30.0%; Ni 2.0%; W 5.0%; Mo 1.25%; Mn 1.2%; Si 1.2%; Nb 0.4%; Fe≤3.00%; S≤0.03%; P≤0.04%; balance Co.

[0106] Comparative Example 3

[0107] Comparative Example 3 provides a GH5630C wear-resistant alloy bar.

[0108] Comparative Example 3 was carried out according to the method of Example 1, except that the chemical composition of the GH5630C wear-resistant alloy bar was different.

[0109] The chemical composition of the GH5630C wear-resistant alloy bar of Comparative Example 3 is as follows: C 0.8%; Cr 30.0%; Ni 2.0%; W 5.0%; Mo 1.25%; Mn 1.2%; Si 1.2%; Nb 0.4%; La 0.08%; Fe≤3.00%; S≤0.03%; P≤0.04%; balance Co.

[0110] Comparative Example 4

[0111] Comparative Example 4 provides a GH5630C wear-resistant alloy bar.

[0112] Comparative Example 4 follows the method of Example 1, except that: (4) in the constrained upsetting step, the ingot deformation is 45%, as follows:

[0113] (4) Constrained upsetting: To obtain a forging billet with a diameter of approximately 254 mm and a height of approximately 220 mm, a rigid metal constraint collar with an inner diameter of 280 mm and a height of 200 mm is used to constrain and upset the ingot (diameter of 180 mm and height of 400 mm) obtained by homogenization heat treatment to obtain the forging billet; the ingot heating temperature is 1200℃, the final forging temperature is 1150℃, and the ingot deformation is 45%.

[0114] Comparative Example 5

[0115] Comparative Example 5 provides a GH5630C wear-resistant alloy bar.

[0116] Comparative Example 5 follows the method of Example 1, except that: (4) in the constrained upsetting step, the ingot deformation is 65%, as follows:

[0117] (4) Constrained upsetting: To obtain a forging billet with a diameter of approximately 254 mm and a height of approximately 140 mm, a rigid metal constraint collar with an inner diameter of 280 mm and a height of 120 mm is used to constrain and upset the ingot (diameter of 180 mm and height of 400 mm) obtained by homogenization heat treatment to obtain the forging billet; the ingot heating temperature is 1200℃, the final forging temperature is 1150℃, and the ingot deformation is 65%.

[0118] Comparative Example 6

[0119] Example 6 provides a GH5630C wear-resistant alloy bar.

[0120] Example 6 is carried out according to the method of Example 1, except that: (4) the inner diameter of the metal constraint mold in the constraint upsetting step is 290mm.

[0121] Comparative Example 7

[0122] Comparative Example 7 provides a GH5630C wear-resistant alloy bar.

[0123] Comparative Example 7 was performed according to the method of Example 1, except that step (4) of constrained upsetting was replaced with billet forging, and the specific steps are as follows:

[0124] (4) Forging: The ingot obtained by homogenization heat treatment is forged into a billet at a temperature of 1200℃ and a deformation of 50% per heat treatment to obtain a forged billet.

[0125] Performance testing

[0126] The GH5630C wear-resistant alloy bars obtained in Examples 1-15 and Comparative Examples 1-7 were subjected to performance tests, including bending strength, room temperature impact toughness, fatigue strength at 600℃, wear at 600℃, and coefficient of friction. The specific test results are shown in Table 4.

[0127] (1) Room temperature impact toughness: The impact resistance of cobalt-based deformed high-temperature alloy bars was tested according to GB / T 229-2020 "Metallic Materials Charpy Pendulum Impact Test Method". The impact resistance performance is expressed by the impact energy. The greater the impact energy, the better the impact resistance and the better the toughness of the material.

[0128] (2) Fatigue strength at 600℃: Rotational bending fatigue test was conducted according to GB / T 4337—2015 "Metallic materials - Rotational bending fatigue test method", with stress ratio R = -1, rotational speed of 4800 r / min, and rotational bending loading method, using the lifting and lowering method to determine 10. 7 Conditional fatigue strength.

[0129] (3) Wear amount and friction coefficient at 600℃: Using GH5630C cobalt-based wear-resistant alloy as a disc-shaped lower sample and GH4169 alloy in standard heat-treated condition as a pin-shaped upper sample, a pin-disc sliding wear test was conducted at an ambient temperature of 600℃ in an SRV-4 friction and wear testing machine. The wear amount of GH5630C cobalt-based wear-resistant alloy was measured, and the steady-state friction coefficient was recorded. The test conditions were set as follows: load 10N, stroke 2mm, frequency 10Hz, and time 30min. Wear amount represents wear resistance performance; the smaller the wear amount, the better the wear resistance performance.

[0130] Table 4. Performance test results of GH5630C wear-resistant alloy bars obtained in Examples 1-15 and Comparative Examples 1-7

[0131]

[0132]

[0133] According to the test results in Table 4, the GH5630C wear-resistant alloy bars obtained in Examples 1-15 of this application have a room temperature impact toughness ≥83J, a fatigue strength at 600℃ ≥650MPa, and a wear volume at 600℃ ≤30×10⁻⁶. 6 μm 3 The coefficient of friction at 600℃ is 0.7-0.9; while the wear volume of the GH5630C wear-resistant alloy bar obtained in Comparative Example 1 at 600℃ is as high as 36×10⁻⁶. 6 μm 3 The wear volume of the GH5630C wear-resistant alloy bar obtained in Comparative Example 2 at 600℃ reached as high as 38 × 10⁻⁶. 6 μm 3 The coefficient of friction at 600℃ is 1.1; the wear volume of the GH5630C wear-resistant alloy bar obtained in Comparative Example 3 at 600℃ is as high as 41 × 10⁻⁶. 6 μm 3 Comparative Example 7 shows that the GH5630C wear-resistant alloy bar obtained by conventional forging has a room temperature impact toughness of only 76 J, a fatigue strength of only 620 MPa at 600℃, and a wear volume as high as 35 × 10⁻⁶ at 600℃. 6 μm 3 Therefore, it is demonstrated that by using the alloy composition and preparation method provided in Examples 1-15 of this application, GH5630C wear-resistant alloy with good wear resistance, impact toughness and fatigue resistance can be prepared.

[0134] The test results of Examples 1-4 show that as the ingot heating temperature increases, the room temperature impact toughness, fatigue resistance, and wear resistance of the obtained GH5630C wear-resistant alloy bars all show a trend of first increasing and then decreasing. Therefore, this application demonstrates that by controlling the ingot heating temperature in the constrained upsetting step between 1150-1220℃, it is possible to obtain GH5630C wear-resistant alloy bars with excellent comprehensive performance in room temperature impact toughness, fatigue resistance, and wear resistance. Further comparison reveals that the GH5630C wear-resistant alloy bars obtained in Examples 1 and 3 have a wear volume at 600℃ ≤ 25 × 10⁻⁶. 6 μm 3 The coefficient of friction at 600℃ is 0.7. This indicates that by further controlling the ingot heating temperature between 1180-1200℃, the wear resistance of the GH5630C wear-resistant alloy bar can be made even better.

[0135] The test results of Examples 1, 5-6, and Comparative Examples 3-4 show that as the upsetting deformation increases, the room temperature impact toughness of the obtained GH5630C wear-resistant alloy bars gradually decreases, while the fatigue resistance and wear resistance show a trend of first increasing and then decreasing. In particular, the GH5630C wear-resistant alloy bars obtained in Examples 1 and 5-6 exhibit room temperature impact toughness ≥85J, fatigue strength at 600℃ ≥670MPa, and wear volume at 600℃ ≤25×10⁻⁶. 6 μm 3 Therefore, this application demonstrates that by controlling the upsetting deformation to between 50-60%, it is possible to obtain GH5630C wear-resistant alloy bars with excellent comprehensive properties of impact toughness, wear resistance, and fatigue resistance.

[0136] The test results of Examples 1 (1.1 times), 7 (1.02 times), and 6 (1.14 times) show that in Comparative Example 6, the excessively large size of the metal constraint mold led to a reduced constraint effect and decreased deformation uniformity, resulting in poor wear resistance and toughness of the GH5630C wear-resistant alloy. In contrast, Examples 1 and 7, by setting the inner diameter of the metal constraint mold to 1.02-1.12 times the ideal diameter of the forging billet, produced GH5630C wear-resistant alloy bars with more ideal deformation uniformity, impact toughness ≥85J, fatigue strength at 600℃ ≥660MPa, and wear volume at 600℃ ≤28×10⁻⁶. 6 μm 3 Further comparison revealed that the GH5630C wear-resistant alloy obtained in Example 1 exhibited superior properties compared to Example 7. This was because the metal constraint mold used in Example 7 was slightly smaller, causing the ingot's bulge to contact the mold prematurely during the upsetting process, resulting in a drop in ingot temperature and consequently, poorer wear resistance and toughness of the resulting GH5630C wear-resistant alloy. Therefore, this application sets the inner diameter of the metal constraint mold to approximately 1.1 times the ideal diameter of the forged billet after constraint upsetting, thereby obtaining GH5630C wear-resistant alloy bars with superior overall performance in impact toughness, wear resistance, and fatigue resistance.

[0137] The test results of Examples 1 and 8-10 show that, in Example 8, by controlling the homogenization heat treatment time to 8 hours, the resulting GH5630C wear-resistant alloy bar has a room temperature impact toughness of 83 J, a fatigue strength of 650 MPa at 600℃, and a wear volume of 30 × 10⁻⁶ at 600℃. 6 μm 3 The GH5630C wear-resistant alloy bars obtained in Examples 1 and 9-10 have a room temperature impact toughness of 91-92 J, a fatigue strength of 705 MPa at 600℃, and a wear volume of 20 × 10⁻⁶ at 600℃. 6 μm 3Therefore, this application demonstrates that by further controlling the homogenization heat treatment time to between 10 and 24 hours, it is possible to obtain GH5630C wear-resistant alloy bars with superior comprehensive performance in terms of impact toughness, wear resistance, and fatigue resistance.

[0138] The test results of Examples 1 and 11-14 show that as the solution treatment temperature increases, the room temperature impact toughness of the obtained GH5630C wear-resistant alloy rods gradually increases, the fatigue resistance shows a trend of first increasing and then decreasing, and the wear resistance gradually decreases. Therefore, considering all properties, Examples 1 and 12-13 of this application further control the solution treatment temperature between 1150-1230℃ to obtain wear-resistant alloy rods with even better overall performance, including room temperature impact toughness ≥90J, fatigue strength at 600℃ ≥670MPa, and wear volume at 600℃ ≤25×10⁻⁶. 6 μm 3 .

[0139] Although the present invention has been described in detail above with general descriptions and specific embodiments, modifications or improvements can be made to it, which will be obvious to those skilled in the art. Therefore, all such modifications or improvements made without departing from the spirit of the present invention fall within the scope of protection claimed by the present invention.

Claims

1. A GH5630C wear-resistant alloy, characterized in that, The GH5630C wear-resistant alloy comprises the following chemical composition by weight percentage: C 1.1~1.4%; Cr 28.5~31.5%; Ni 1.0~2.5%; W 4.5~5.5%; Mo 0.50~1.50%; Mn 0.50~1.70%; Si 0.20~1.50%; Nb 0.3~0.6%; La 0.02~0.2%; Fe≤3.00%; S≤0.03%; P≤0.04%; with the balance being Co. The preparation method of the GH5630C wear-resistant alloy includes the following steps: vacuum induction melting, electroslag remelting, homogenization heat treatment, constrained upsetting, fine forging, rolling or forging, and solution treatment. Constrained upsetting: The ingot obtained by homogenization heat treatment is subjected to constrained upsetting using a metal constrained die to obtain a forging billet; wherein, the inner diameter of the metal constrained die is 1.02-1.12 times the ideal diameter of the forging billet after constrained upsetting; the ingot heating temperature is 1150-1220℃, the final forging temperature is not lower than 1100℃, and the ingot deformation is 50-60%.

2. The GH5630C wear-resistant alloy according to claim 1, characterized in that, The GH5630C wear-resistant alloy comprises the following chemical composition: C 1.2%; Cr 30.0%; Ni 2.0%; W 5.0%; Mo 1.25%; Mn 1.2%; Si 1.2%; Nb 0.4%; La 0.08%; Fe≤3.00%; S≤0.03%; P≤0.04%; with the balance being Co.

3. The GH5630C wear-resistant alloy according to claim 1, characterized in that, The GH5630C wear-resistant alloy also includes a chemical composition of N 0.04-0.4%.

4. The GH5630C wear-resistant alloy according to any one of claims 1-3, characterized in that, The GH5630C wear-resistant alloy has a room temperature impact toughness ≥83J, a fatigue strength at 600℃ ≥650MPa, and a wear volume at 600℃ ≤30×10⁻⁶. 6 μm 3 .

5. The GH5630C wear-resistant alloy according to claim 1, characterized in that, The homogenization heat treatment is performed at a temperature of 1150-1220℃ for 10-24 hours.

6. The GH5630C wear-resistant alloy according to claim 1, characterized in that, The solution treatment is performed at a temperature of 1050-1250℃ for a time of 0.5-10 hours.

7. The GH5630C wear-resistant alloy according to claim 1, characterized in that, The precision forging step is as follows: the forging billet obtained by constrained upsetting is subjected to multi-directional forging at a temperature of 1150-1220℃ and a final forging temperature of not less than 900℃; the forging is repeated 4-6 times, with a deformation amount of not less than 40% per forging, to obtain a precision forged billet.

8. The GH5630C wear-resistant alloy according to claim 1, characterized in that, In the rolling or forging step, the billet heating temperature in the final heat stage is 1180-1230℃, the final rolling or forging temperature in the final heat stage is 900-1000℃, and the deformation amount in the final heat stage is 20-30%.

9. A high-temperature resistant bearing, characterized in that, The high-temperature bearing is made of GH5630C wear-resistant alloy as described in any one of claims 1-8.

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